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Conducting polymers: a comprehensive review on recent advances in synthesis, properties and applications

Affiliation.

1 Centre for Nano and Material Sciences, Jain University, Jain Global Campus Jakkasandra, Ramanagaram Bangalore-562112 India [email protected] [email protected].
PMID: 35686160
PMCID: PMC9133880
DOI: 10.1039/d0ra07800j
Correction: Conducting polymers: a comprehensive review on recent advances in synthesis, properties and applications. K N, Rout CS. K N, et al. RSC Adv. 2024 May 30;14(25):17467-17470. doi: 10.1039/d4ra90058h. eCollection 2024 May 28. RSC Adv. 2024. PMID: 38818360 Free PMC article.

Conducting polymers are extensively studied due to their outstanding properties, including tunable electrical property, optical and high mechanical properties, easy synthesis and effortless fabrication and high environmental stability over conventional inorganic materials. Although conducting polymers have a lot of limitations in their pristine form, hybridization with other materials overcomes these limitations. The synergetic effects of conducting polymer composites give them wide applications in electrical, electronics and optoelectronic fields. An in-depth analysis of composites of conducting polymers with carbonaceous materials, metal oxides, transition metals and transition metal dichalcogenides etc. is used to study them effectively. Here in this review we seek to describe the transport models which help to explain the conduction mechanism, relevant synthesis approaches, and physical properties, including electrical, optical and mechanical properties. Recent developments in their applications in the fields of energy storage, photocatalysis, anti-corrosion coatings, biomedical applications and sensing applications are also explained. Structural properties play an important role in the performance of the composites.

This journal is © The Royal Society of Chemistry.

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Conflict of interest statement

The authors declare no conflict of interest.

Fig. 1. Schematic illustration of applications of…

Fig. 1. Schematic illustration of applications of conducting polymers and their composites.

Chart 1. Structural illustration of different conducting…

Chart 1. Structural illustration of different conducting polymers.

Scheme 1. Formation of monosubstituted and disubstituted…

Scheme 1. Formation of monosubstituted and disubstituted polyacetylene.

Fig. 2. Schematic illustration of different synthesis…

Fig. 2. Schematic illustration of different synthesis methods for conducting polymers.

Scheme 2. Synthesis of polyacetylene using a…

Scheme 2. Synthesis of polyacetylene using a Ziegler–Natta catalyst.

Scheme 3. Synthesis of polyacetylene using a…

Scheme 3. Synthesis of polyacetylene using a Luttinger catalyst.

Chart 2. Structural illustration of different forms…

Chart 2. Structural illustration of different forms of polyaniline.

Scheme 4. Synthesis of polyaniline by the…

Scheme 4. Synthesis of polyaniline by the chemical oxidation method.

Scheme 5. Mechanism of electrochemical synthesis of…

Scheme 5. Mechanism of electrochemical synthesis of polypyrrole.

Scheme 6. Synthesis of poly( p -phenylene)s…

Scheme 6. Synthesis of poly( p -phenylene)s using a binary system (both a Lewis acid…

Scheme 7. Synthesis of poly( p -phenylene)s…

Scheme 7. Synthesis of poly( p -phenylene)s using single system (oxidant system).

Scheme 8. Synthesis of poly( p -phenylene)s…

Scheme 8. Synthesis of poly( p -phenylene)s using a Wurtz–Fittig reaction.

Scheme 9. Synthesis of poly( p -phenylene)s…

Scheme 9. Synthesis of poly( p -phenylene)s using an Ulman reaction.

Scheme 10. Synthesis of poly( p -phenylene…

Scheme 10. Synthesis of poly( p -phenylene vinylene) by a Wittig coupling reaction.

Scheme 11. Synthesis of polythiophenes by the…

Scheme 11. Synthesis of polythiophenes by the Yomomoto route.

Scheme 12. Synthesis of polythiophenes by the…

Scheme 12. Synthesis of polythiophenes by the Lin–Dudek route.

Fig. 3. The electronic band and chemical…

Fig. 3. The electronic band and chemical structures of polythiophene (PT) with (a) p-type doping…

Fig. 4. Electronic bands and chemical structures…

Fig. 4. Electronic bands and chemical structures illustrating (a) undoped; (b) polaron; (c) bipolaron; and…

Fig. 5. Energy level diagram of the…

Fig. 5. Energy level diagram of the molecular ionization process of poly( p -phenylene) (reprinted…

Fig. 6. Representation of charge density wave…

Fig. 6. Representation of charge density wave in polyacetylene.

Fig. 7. Schematic illustration of electroluminescent mechanism…

Fig. 7. Schematic illustration of electroluminescent mechanism of conducting polymer diodes.

Fig. 8. Typical stress–strain curve of polymeric…

Fig. 8. Typical stress–strain curve of polymeric materials.

Fig. 9. Schematic representation of basic properties…

Fig. 9. Schematic representation of basic properties of conducting polymer based supercapacitors.

Fig. 10. [A] (a) Synthesis route for…

Fig. 10. [A] (a) Synthesis route for PC/PANI composite. (b) CV curves of the electrodes…

Fig. 11. [A] (a) Schematic illustration of…

Fig. 11. [A] (a) Schematic illustration of evolution of different morphologies of polypyrrole by electropolymerization.…

Fig. 12. (a) Schematic representation of synthesis…

Fig. 12. (a) Schematic representation of synthesis route for polyaniline/CeO 2 nanoparticles. (b and c)…

Fig. 13. (a and b) Nyquist and…

Fig. 13. (a and b) Nyquist and (c) Bode plots of the prepared samples. (d)…

Fig. 14. (a) Schematic illustration of the…

Fig. 14. (a) Schematic illustration of the synthesis of PEDOT:PSS-G hybrids. (b) Optical photographs of…

Fig. 15. Photocatalytic mechanism in conducting polymer…

Fig. 15. Photocatalytic mechanism in conducting polymer composites.

Fig. 16. [A] (a) Synthetic route. (b)…

Fig. 16. [A] (a) Synthetic route. (b) The process of light-harvesting and energy migration in…

Fig. 17. (a) TEM image of bare…

Fig. 17. (a) TEM image of bare CdO nanoparticles. (b & c) SEM image of…

Fig. 18. Schematic representation of photothermal treatment…

Fig. 18. Schematic representation of photothermal treatment using a conducting polymer.

Fig. 19. [A] (a) Schematic illustration of…

Fig. 19. [A] (a) Schematic illustration of effect of NIR radiation on S-rGO–Fe 3 O…

Fig. 20. (a) AFM images of PANI-NF/AuNP…

Fig. 20. (a) AFM images of PANI-NF/AuNP surface, PANI-NF/AuNP/GSH surface, PANI-NF/AuNP/GSH/FA surface, and HeLa cells…

Chandra Sekhar Rout

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Recent advances in nanostructured conducting polymers: from synthesis to practical applications.

Graphical Abstract

1. Introduction

2. overview and classification of synthesis methods, 2.1. polymerization mechanism, 2.2. methods for fabricating conducting polymer nanomaterials, 2.2.1. solid template approach, 2.2.2. molecular template approach, 2.2.3. template-free approach, 2.2.4. other methods, 2.3. synthesis methods for cp nanohybrids, 3. progress in cp nanomaterial synthesis, 3.1. recent advances in the synthesis of cp nanomaterials, 3.2. novel trends for synthesis of cp nanohybrids, 4. selected applications of cp nanomaterials, 4.1. sensors, 4.2. electrochemical energy storage devices, 4.3. photovoltaic cells, 4.4. drug carriers, 5. conclusions and outlook, acknowledgments, author contributions, conflicts of interest.

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Polymerization routes employed to obtain conducting polymers (CPs).
Route	Details	Ref.
Chemical polymerization	Requires an oxidizing agent to synthesize the polymer. The morphology of the polymer can be controlled by varying the parameters of the process, such as monomer/oxidizing agent concentration, temperature, pH, and reaction time.	[ , , , , , ]
Electrochemical polymerization	An oxidizing agent is not required for this route, which is an efficient approach for depositing CPs on substrates. Some monomers are theoretically not electropolymerizable. Furthermore, it is difficult to scale up this process. A high oxidation potential may lead to over oxidation of the polymer.	[ , , , , , ]
Photo-polymerization	Illumination is needed for polymerization. This route was developed to solve the over oxidation problem of the electrochemical method. The process can be well controlled simply by turning the light on or off.	[ , , , , ]

Synthesis methods of CP nanomaterials.
Synthesis methods	Advantages	Disadvantages
Solid template	Applicable to almost all CPs. Possible to precisely control the size and morphology.	A post-synthesis process is required to remove the template. Nanostructure quantity is confined by the size of the template membrane.
Molecular template	Relatively simple, and thus scale-up is possible under optimized conditions.	Hard to provide good uniformity of size and morphology.
Template-free	Simple process without templates.	Limited to certain precursors.
Electrospinning	Simple to produce continuous CP nanofibers.	Only soluble and thermoplastic polymers are applicable.
Nanoimprinting	High throughput and high resolution.	An expensive micro-mold is required.

Preparation methods for synthesizing CP nanohybrids.
Main Group	Advantage	Disadvantage	Example	Ref.
Ex situ synthesis	Simple Solution-processable	Limited applications Poor control of the contact between each component	Mechanical mixing	[ ]
Ex situ synthesis	Simple Solution-processable		Layer-by-layer deposition	[ ]
In situ synthesis	Variable methods based on chemical or electrochemical route. Facile control of many variables	Higher complexity as many parameters need to be considered	In situ polymerization. Electrodeposition. In situ reduction	[ , , ]
One-pot synthesis	Simple Short processing time	Limited control over structure and morphology of the products	Redox reaction Co-deposition	[ , , ]

Representative examples of fabrication methods for CP nanomaterials developed over the last three years.
CP	Polymerization method	Details	Refs.
PANI	Amyloid nanofiber template polymerization	Amyloid nanofibers were successfully used as templates for the formation of conductive core-shell nanowires	[ ]
	Planar DNA template	Production of CPs with controlled shapes on 2D polyelectrolyte templates was investigated for the first time	[ ]
	Electrospinning using poly(amic acid) fiber as a template	Hollow nanofibers with controllable wall thicknesses were successfully obtained	[ ]
	Dedoped chemical polymerization	Water-dispersed CP nanofibers with high capacitance were achieved by double doping	[ ]
	Biphase interfacial polymerization	The mechanism for self-assembly in crystalline 1D nanostructures was investigated	[ ]
	Surface-initiated polymerization	A new approach for multimodal core-shell nanoparticles with a stable doping state was reported	[ ]
	Interfacial polymerization	A novel hollow PANI nanocapsule with holes in the wall was synthesized	[ ]
PPy	Time-dependent template-assisted polymerization	A new synthesis approach for the precise control of wall morphologies of colloidal microparticles was studied	[ ]
PPy	Modified pulse potentiostatic method	A good method to control the shape of micelles at the substrate/electrolyte interface and control the morphology of CPs was proposed	[ ]
PEDOT	Galvanostatic electrodeposition	Good result combining a carboxylated polystyrene template made by nanosphere lithography with SDS as a molecular template was achieved	[ ]
	Non-spontaneous emulsification	A novel method using colloidal chemistry to fabricate multifunctional CPs was developed	[ ]
	Electron pulse-enabled in situ polymerization	The mechanism of CP growth was investigated experimentally and via modeling	[ ]

Representative reports for the solid/vapor-phase polymerization of CP nanomaterials.
Phase	CP	Details	Refs.
Solid phase	PANI	Hairy CP nanowires were obtained via mechanochemical polymerization using citric acid as a dopant	[ ]
	PEDOT	The role of temperature in the solid-state synthesis was studied	[ ]
	PEDOT	A low-cost, low-temperature method to fabricate high-performance CPs was successfully developed	[ ]
Vapor phase	PANI	The effect of microwave radiation was studied	[ ]
	PPy	The role of co-vapor in the vapor-phase polymerization (VPP) method was studied	[ ]
	PPy	An application for drug storage was carried out by depositing PPy using the chemical vapor deposition (CVD) method	[ ]
	PEDOT	The dependence of electrical conductivity on VPP temperature was discussed	[ ]
		Single-crystal CP nanowires were developed using VPP with liquid-bridge-mediated nanotransfer printing	[ ]
		A one-step fabrication of 2D nanoparticles was investigated	[ ]
		The advantages of directly depositing CP nanofibers was demonstrated	[ ]

Representative examples of the incorporation of inorganic species into CPs.
CP	Inorganic species	Preparation method	Details	Refs.
PANI	Au	Interfacial polymerization	The formation mechanism of Au-PANI was presented	[ ]
	Cu	Concurrent synthesis	The structure of a Cu/PANI hybrid was studied	[ ]
	Pd	Layer-by-layer technique	A Pd/PANI/Pd sandwich-structure nanotube array was first reported	[ ]
	TiO	Combination of hydrothermal and electropolymerization	A multicolor electrochromic film was fabricated based on hybrid core-shell nanorod arrays	[ ]
	CdO	Chemical oxidative polymerization	Aqueous diethylene glycol solution medium was used for the first time	[ ]
	MoS	Vertically aligned chemical polymerization	A good example of hybrid 3D tubular structures was discussed	[ ]
	Se Te	Lyotropic liquid crystalline template	A mesoporous dual-layer film was synthesized using Brij56 surfactant	[ ]
	MnFe O	Incorporative polymerization	Dual nature of hybrid (cathode catalyst and anode modifier) was first demonstrated	[ ]
PPy	Ag	Incipient network conformal growth technology	A new porous material, namely, an “aero-sponge,” was proposed	[ ]
	Ag	Cathodic co-deposition	Highly stable sensing activity of the hybrid was studied	[ ]
	MnO	Electropolymerization	Effect of deposition time was reported	[ ]
	ZnO	Ultrasound-assisted chemical polymerization	Well-controlled granular and layered nanocomposite was formed	[ ]
	CuO	Wire template technique	The previous method was extended to study polymerization time	[ ]
	CoO	Modified hydrothermal and post-annealing process	3D growth of well-aligned nanowire array was developed	[ ]
	MoS	In situ intercalative polymerization	A facile strategy for intercalation of PPy into MoS nanosheets was proposed	[ ]
	TiO	Pulsed-light and pulsed-potential method	Good control of the deposition rate was demonstrated	[ ]
	LiV O	Low-temperature in situ polymerization	A new anode material for rechargeable lithium batteries was reported	[ ]
	ZnCo O	Reflux method and chemical polymerization	A facile method for fabricating mesoporous ZnCo O -coated PPy was developed	[ ]
PT	ZnO	Electropolymerization growth	Interfacial bonding and morphology control was described	[ ]
PEDOT	V O	“Cocoon-to-silk” fiber reeling method	First method for fabricating layered V O /PEDOT nanowires was reported	[ ]
PEDOT	Iron oxide *	Spin-coated-assisted deposition with “supporting layer technique”	A new simple, fast, and inexpensive technique for the fabrication of a free-standing hybrid was reported	[ ]
CP **	Ag, Au, CdSe	RAFT polymerization	Role of the direct covalent attachment was emphasized	[ ]

Representative examples for photosynthesis of CP nanohybrids.
Material	Preparation method	Details	Refs.
PPy/Ag	One-pot UV-induced photopolymerization	Effect of concentration ratio of composite in cellulose fabric was studied	[ ]
PPy/Ag	One-step interfacial photopolymerization	Thin, flexible nanofilms were synthesized at the water–air interface	[ ]
PPy/TiO	Photo-assisted electrodeposition	Effect of LiClO in the presence of SDBS was investigated	[ ]
PPy/TiO	Photoelectrochemical polymerization	Properties of nanohybrid in the presence of SDS was studied	[ ]
PPy/WO	In situ photopolymerization	A room-temperature H S gas sensor was fabricated	[ ]
PPy/ceria	Photo-induced polymerization	A good example of one-step photopolymerization was shown	[ ]
PPy/methacrylate	UV and visible light photopolymerization	The mechanism of photopolymerization with iodonium salt was presented	[ ]
PPy/AgBr/Ag	Microemulsion photopolymerization	Effect of different concentrations of cationic surfactant CTAB was studied	[ ]
PT/epoxy	One-pot photoinduced synthesis	A novel methodology for fabricating a network film was given	[ ]
Clay/PPy/Ag	In situ photopolymerization	The silanization of clay on a PPy/Ag surface was discussed	[ ]
PEDOT/TiO	Photoelectrochemical polymerization	Role of donor-π-acceptor sensitizers was described	[ ]
		A new method using aqueous micellar solutions was shown	[ ]
		The effect of light intensity on the oxidation level of PEDOT was studied	[ ]

Representative examples of studies where carbon nanomaterials were incorporated into CPs.
Carbon	CP	Preparation method	Details	Refs.
GN *	PANI	In situ polymerization	A microspherical and porous structure was fabricated	[ ]
		Reflux technique	Complex of PANI and GN for enhancing charge-transfer ability was reported	[ ]
		Sandwiched GN–mesoporous silica as template	A novel approach to fabricate mesoporous PANI film coating on GN	[ ]
		Low-temperature in situ polymerization	PANI nanorods were coated on graphene nanomesh	[ ]
	PPy	Double-doping electropolymerization	A good example for anchoring double-doped CP on GN sheet was given	[ ]
	PEDOT	Electrochemical codeposition	The role of SDS surfactant in the incorporation of GN into PEDOT was studied	[ ]
rGO	PANI	In situ reduction	A high-surface-area hybrid was reported	[ ]
	PANI	Electrostatic adsorption synthesis	The thickness was well-controlled by pH modification	[ ]
	PPy	Vacuum filtration method	The improvement of cycling stability was demonstrated via the addition of rGO	[ ]
		Hydrogen bubble dynamic template	A general method for fabrication of 3D macroporous hybrid was studied	[ ]
		Interfacial polymerization	The comparison of two different methods was shown, emphasizing the strength of interfacial polymerization	[ ]
		Bioreduction technique	A new simple, environmentally benign method that was time- and cost-efficient was developed	[ ]
		One-step synthesis	A good example of a cathode material was shown	[ ]
		Interfacial polymerization	A novel electrode material was developed	[ ]
	PEDOT	Fast thermal treatment with in situ deposition	A good example of a hybrid CP for gas sensing was studied	[ ]
SWCNT	PANI	Liquid–liquid interfacial polymerization	The synthesis and characterization of hybrid thin films in liquid–liquid interface was first studied	[ ]
SWCNT	P3HT **	Diels-Alder ligation	A facile covalent strategy was developed to address the bundling issue of CNTs	[ ]
MWCNT	PEDOT:PSS	Electrochemical co-deposition	A facile and effective approach for electrode preparation was reported	[ ]

Representative examples of ternary CP nanohybrids.
Ternary system			Details	Refs.
CP	Carbon	Inorganic species	Details	Refs.
PANI	GN/CNT		Intercalation of CNT between GN sheets	[ ]
	GN/CNT		In situ deposition of PANI on GN/CNT paper	[ ]
	Graphite felt/CNT		Electropolymerization of PANI in the presence of graphite felt	[ ]
	Graphite felt/CNT		Electrophoretic immobilization of CNT on the hybrid	[ ]
	GN/CNF *		Production of G/CNF by electrospinning	[ ]
	GN/CNF *		In situ polymerization of PANI	[ ]
	GO	S	Layer-by-layer synthesis of PANI layer on GO-S composite with heating	[ ]
	rGO	MnO	PANI vertically grown on GO sheet	[ ]
	rGO	MnO	Reduction of GO and follow by the deposition of MnO onto PANI	[ ]
	rGO/CNT		Combination of chemical foaming, thermal reduction, and KOH activation to prepare rGO	[ ]
	rGO/CNT		Interfacial polymerization	[ ]
	N-doped rGO	NiFe O	NiFe O simultaneously grown with reduction and doping of GO	[ ]
	N-doped rGO	NiFe O	In situ chemical polymerization of PANI	[ ]
	CNT	Fe	Reduction of FeCl in the mixing solution of aniline and CNTs	[ ]
	CNT	CoS	Hydrothermal synthesis of CNT/CoS	[ ]
	CNT	CoS	In situ electropolymerization of PANI	[ ]
	rGO	MnFe O	Hydrothermal reaction to disperse MnFe O well on the rGO surface	[ ]
	rGO	MnFe O	In situ polymerization of PANI	[ ]
	Vertical rGO	Pd	One-step electrodeposition of PANI and rGO	[ ]
	Vertical rGO	Pd	Spontaneous redox reaction of PANI with Pd salt	[ ]
	CNT	Ag	In situ chemical polymerization of PANI in the presence of AgNO and MWCNTs	[ ]
	C	TiN	Sequential coating of C and PANI on the surface of TiN nanowire array	[ ]
	C	S	In situ polymerization of aniline on the pore surface of mesoporous C which served as a reservoir for S	[ ]
PPy	rGO/CNT		Reduction of GO in the presence of CNT	[ ]
	rGO/CNT		In situ chemical polymerization of PPy in the presence of rGO/CNT powders	[ ]
	GN	S	In situ polymerization of PPy in the presence of GN	[ ]
	GN	S	Suspension mixture of PPy/GN with nano-S	[ ]
	CNT	TiO	Chemical preparation of complex of TiO /CNT	[ ]
	CNT	TiO	In situ polymerization using MO as template	[ ]
PPy/PEDOT	CNT		Series of processes: high-temperature reflux technique, thermal compression, oxygen plasma etching, and electrochemical polymerization	[ ]
PT		Pd/TiO	Water-in-oil emulsion of TiO microspheres	[ ]
PT		Pd/TiO	Loading Pd species and coating PT	[ ]
PEDOT:PSS	rGO	RuO	Mechanical stirring and sonochemical treatment of PEDOT:PSS in PSS-coated rGO solution	[ ]
	rGO	RuO	Chemical interaction between RuO and hybrid	[ ]
	GO/CNT		Self-assembled interfacial coupling method	[ ]

© 2016 by the authors. Licensee MDPI, Basel, Switzerland. This article is an open access article distributed under the terms and conditions of the Creative Commons by Attribution (CC-BY) license ( http://creativecommons.org/licenses/by/4.0/ ).

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Nguyen, D.N.; Yoon, H. Recent Advances in Nanostructured Conducting Polymers: from Synthesis to Practical Applications. Polymers 2016 , 8 , 118. https://doi.org/10.3390/polym8040118

Nguyen DN, Yoon H. Recent Advances in Nanostructured Conducting Polymers: from Synthesis to Practical Applications. Polymers . 2016; 8(4):118. https://doi.org/10.3390/polym8040118

Nguyen, Duong Nguyen, and Hyeonseok Yoon. 2016. "Recent Advances in Nanostructured Conducting Polymers: from Synthesis to Practical Applications" Polymers 8, no. 4: 118. https://doi.org/10.3390/polym8040118

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v.11(10); 2021 Jan 28

Conducting polymers: a comprehensive review on recent advances in synthesis, properties and applications

Centre for Nano and Material Sciences, Jain University, Jain Global Campus, Jakkasandra, Ramanagaram, Bangalore-562112 India, [email protected] moc.liamg@tuorsc

Chandra Sekhar Rout

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1. Introduction

Polymers were considered to be electrical insulators before the invention of conducting polymers (conjugate polymers), but these organic polymers have unique electrical and optical properties similar to those of inorganic semiconductors. 1 A conjugated carbon chain consists of alternating single and double bonds, where the highly delocalized, polarized, and electron-dense π bonds are responsible for its electrical and optical behavior. Typical conducting polymers include polyacetylene (PA), polyaniline (PANI), polypyrrole (PPy), polythiophene (PTH), poly( para -phenylene) (PPP), poly(phenylenevinylene) (PPV), and polyfuran (PF) ( Chart 1 ). Alan G. MacDiarmid and physicist Alan J. Heeger discovered (SN) x sulfur nitride metal, an inorganic material, which showed higher electrical conductivity when doped with bromine, and this finding led to the investigation of conducting polyacetylene. Polyacetylene doped with bromine has a conductivity a million times higher than that of pristine polyacetylene and this investigation was rewarded by a Nobel Prize in 2000. 2 Conventional polymers consist of thousands to millions of monomer units. They are stiff and soluble in solvents, but a conjugated polymer chain consists of a lower number of monomer units. The mechanical property is gained by the presence of alternating single and double bonds present within it. The solubility and processability of conducting polymers depend mainly upon the attached side chains, and the attached dopant ions give them mechanical, electrical and optical properties. 3 Conducting polymers are crystalline and partially amorphous. Conducting polymers consist of both localized and delocalized states, and the delocalization of π bonds depends heavily upon disorder, and this delocalization plays an essential role in the generation of charge carriers like polarons, bipolarons, solitons, etc. , which are responsible for the transition from insulator to metal. 4 The conductivity of conjugate polymers acts like an insulator to a semiconductor in their pure form, and the conductivity increases with dopant concentration. In the undoped state, they behave as an anisotropic, quasi-one-dimensional electronic structure with a moderate bandgap of 2–3 eV like a conventional semiconductor and they exhibit the electrical and optical behavior of semiconductors along with the mechanical action of typical polymers. When conjugated polymers undergo doping or photoexcitation, the π bond gets self-localized to undergo nonlinear excitation as polarons, solitons, bipolarons, etc. , and the polymer transforms from a nonlinear excitation state to a metallic state. 5–7 Here in this comprehensive review, we effectively discuss the different synthesis approaches, properties and various applications of conducting polymers ( Fig. 1 ).

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2. Conducting polymers and their synthesis

2.1. polyacetylene.

The invention and conductivity enhancement by doping of polyacetylene were rewarded with the Nobel Prize. 8 Polyacetylene and its derivatives show multifunctional behaviors. On close examination, some of its features can be explored, including electrical conductivity, photoconductivity, liquid crystal properties, and chiral recognition. The main chain of polyacetylene is made up of a linear polyene chain. It is flexible and can be decorated with pendant groups, i.e. , the hydrogen molecules present in the alternating carbon can be replaced with a foreign molecule to form a monosubstituted or di-substituted polyacetylene ( Scheme 1 ). 9

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Conducting polymers were synthesized using various methods, including chemical oxidation, electrochemical polymerization, vapor phase synthesis, hydrothermal, solvothermal, template-assisted, electrospinning, self-assembly, and photochemical methods, the inclusion method, the solid state method, and plasma polymerization 10–15 ( Fig. 2 ). Generally, conducting polymers have low electrical conductivity and optical properties in their pristine state; however, doping with suitable materials can give them excellent properties. Polyacetylene has a conductivity in the range of 10 −5 s cm −1 , but when the doping level increases, its conductivity rises drastically to 10 2 to 10 3 s cm −1 , 16 and depending upon the dopant material its properties also change and also give it tunable properties like electrochemical or optical mechanical properties, etc. 4,17 There are several synthesis methods for polyacetylene: catalytic polymerization, non-catalytic polymerization, catalytic polymerization of other polymers, and precursor-assisted synthesis. In the case of the catalytic-polymerization technique, catalysts like Ziegler–Natta catalysts or Luttinger catalysts are used for the synthesis. The polymerization of acetylene produces polyacetylene polymer and oligomers like cyclooctatetraene and vinyl acetylene. There are a lot of catalysts available for the synthesis of polyacetylene and among them Zeigler–Natta catalysts have high solubility in organic solvents and high selectivity. Being a combination of both Ti(0- n -C 4 H 9 ) 4 and (C 2 H 5 ) 3 A1, they produce highly crystalline free-standing films of polyacetylene on the wall of the reaction flask on which the catalyst is coated ( Scheme 2 ). 18

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Luttinger catalysts are also used for the preparation of polyacetylene; they consist of a combination of a hybrid reducing agent and a complex of a group [VIII] metal such as nickel chloride. These catalysts produce high molecular weight polyacetylene without traces of oligomers ( Scheme 3 ). When compared with a Ziegler–Natta catalyst, a Luttinger catalyst uses hydrophilic solvents like water–ethanol tetrahydrofuran (THF) or acetonitrile as a solvent for catalytic action. But it has less catalytic activity than a Zeigler–Natta catalyst and the product formed by these catalysts have almost the same physical and chemical properties. 19

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Electrochemical polymerization of acetylene comes under the heading of non-catalytic polymerization. Anodic oxidation of a monomer precursor in the presence of suitable electrolytes on an inert metal surface is regarded as an electrochemical synthesis. Various electrochemical techniques like cyclic voltammetry, potentiostatic, galvanostatic, and galvanostatic charge discharging techniques have been used for synthesis. The main advantage of this technique is that it will allow the straight deposition of a polymer film on the metal, and we can control the film thickness easily by tuning the electrochemical parameters. 20 Korshak et al. synthesized polyacetylene films by ring-opening polymerization of 1,3,5,7-cyclooctatetraene with a metathesis catalyst, W[OCH(CH 2 Cl) 2 ] n Cl 6− n (C 2 H 5 ) 2 AlCl ( n = 2 or 3), which is an example of the synthesis of polyacetylene without using an acetylene monomer. 21 Light-induced synthesis of the conjugated system has also been reported, where irradiation of acetylene gas with UV leads to the production of polyacetylene. 22

2.2. Polyaniline

Polyaniline is the most promising and most explored among conducting polymers, and polyaniline has high stability, high processability, tunable conducting and optical properties. The conductivity of polyaniline is dependent upon the dopant concentration, and it gives metal-like conductivity only when the pH is less than 3. 23 Polyaniline exists in different forms ( Chart 2 ). They are classified as leucoemeraldine, emeraldine, and pernigraniline, by their oxidation state, i.e. , leucoemeraldine exists in a sufficiently reduced state, and pernigraniline exists in a fully oxidized state. Polyaniline becomes conductive only when it is in a moderately oxidized state and acts as an insulator in a fully oxidized state. 24

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The polymer backbone consists of both quinoid and benzoid rings, in differing proportions. The difference in the ratio causes the existence of three oxidized states: the fully reduced leucoemeraldine form is in a quinoid state, the fully oxidized pernigraniline form is in a benzoid state and the conductive emeraldine form has an equal ratio of both benzoid and quinoid rings. The dopant does not change its chemical property and will not create any bond with the main chain; it exists in the close vicinity of the polymer chain. 25

The chemical oxidation method is one of the most straightforward methods to synthesize polyaniline; in this method a monomer precursor of the corresponding polymer is mixed with an oxidizing agent in the presence of a suitable acid under ambient conditions to give products, where the doping acid and oxidizing agent are those preferred by the authors concerned ( Scheme 4 ). The change in color of the reaction medium to green indicates the formation of polyaniline. The preparation of the composite also follows the same method. Generally, oxidizing agents like ammonium persulfate, ammonium peroxy disulfate, ceric nitrate, ceric sulfate, potassium bichromate, etc. are used. Depending upon the pH of the acid dopant, the conductivity effectively modulates the physical parameters. The polymer and composite possess good conductivity when the pH is between 1 and 3. 26–28

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Interfacial polymerization is also used to synthesize polyaniline, in which an aniline monomer is solubilized in an organic solvent like toluene, an oxidant solution and a dopant acid-containing aqueous solution. Polymerization takes place in the interphase of these two immiscible liquids when an oxidant solution is added to the monomer solution. A microemulsion technique is also followed for the synthesis of polyaniline, where the polymerization also takes place in the interface between two immiscible liquids, but the difference is in the surfactant used. 29–31 The electropolymerization technique happens without the effect of an oxidant, and is the same in the case of polyacetylene. 32,33 Electrospinning is also used to synthesise fibrous polymer morphologies of nano or micro diameters under the influence of a strong electrical field. In this case, a high voltage is applied to the polymer droplets, and the charged droplets get stretched due to surface tension, and at a critical point, the liquid erupts and starts to weave on the counter surface. The principles of both electrospraying and electrospinning are the same. Electrospinning is the only method to produce bulk polymer fibrous structure. Conducting polymers and their composites like pure polyaniline, polypyrrole, polyaniline/polyethylene oxide/carbon nanotubes have been prepared by this technique. There are lot of factors dependent on electrospinning, such as the molecular weight of the polymer, viscosity, distance between spinneret and counter surface, temperature, humidity, etc. 34–36

2.3. Polypyrrole

Polypyrrole is unique due to its increased commercial interest because of its high stability, enhanced conductivity, and it is relatively easy to form homopolymer and composites from it. Polypyrrole was first prepared by the chemical oxidation of a pyrrole monomer in the presence of hydrogen peroxide, and it is a black powdery material. Polypyrrole behaves like an insulating material in its undoped virgin state, and it shows a constant conductivity of 10 −5 s m −1 when doped with halogenic electron acceptors such as bromine or iodine. 37 It is not crystalline, and acts as amorphous in nature, but bulk polypyrrole has 15% crystallinity, and the crystalline region is in the monoclinic phase. 38 For electrochemically synthesized polypyrrole with a thickness of 1 μm and a yellow blackish colour, transformation occurs by an increase in protonation concentration and it has higher stability in air and high thermal stability in the range of 300 °C; thermal degradation can occur due to the loss of dopant anions. 39,40

Among the synthesis methods, electrochemical synthesis is widely used to obtain highly conductive polypyrrole, where the procedure and technique are similar to those of other conducting polymers ( Scheme 5 ). The yield of the product is limited in this technique due to the reduced anode size. The main advantage this method has over other techniques is that we can control the thickness and morphology by controlling the electrochemical parameters. 41–44 There are a lot of electrochemical synthesis mechanisms available. Here in this polymerization mechanism, a free radical cation is developed due to deprotonation, and this free radical attacks the neutral monomer unit. After reoxidation of the dimeric radical and proton loss, the dimeric molecule can experience subsequent oxidation, which results in chain growth. The release of protons in the course of the oxidation of pyrrole was observed experimentally. 45

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Polypyrrole was initially synthesized by the oxidation of a pyrrole monomer in the presence of H 2 O 2 to obtain an amorphous blackish powdery material. 46 Pyrrole black is insoluble in organic solvents and shows limited conductivity in the range of 10 −10 to 10 −11 s cm −1 . It is prepared by using acid and peroxide, and its conductivity will increase when doped with a halogen electron acceptor. In general, aqueous or anhydrous FeCl 3 , or other salts of iron( iii ) or copper( ii ) are widely used as chemical oxidants. 47

Some factors affect the conductivity and yield: (1) solvent type and oxidant used; (2) pyrrole/oxidant ratio; (3) reaction temperature and reaction time. When polypyrrole is prepared with an FeCl 3 oxidant, the final product is doped with Cl − anions.

Highly conductive polypyrrole is synthesized by controlling the oxidation potential of an aqueous solution by adding an oxidant to it. Apart from metallic salts, polypyrrole has been synthesized using a halogen electron acceptor, such as bromine or iodine, in various solvents. 37

2.4. Poly( p -phenylene)s

Poly( p -phenylene) is a macromolecule made up of benzoid aromatic nuclei, directly joined by C–C bonds. Poly( p -phenylene)s attract considerable interest due to their high thermal stability, high air stability, and ease of doping and tunable conducting and high optical properties. The mechanical rigidity of the polymer backbone along with conjugation is a promising development in the field of nonlinear optics. The solubility of poly( p -phenylene)s is limited but gradually increases when flexible side chains are attached to the backbone. The conductivity of poly( p -phenylene) will grow 14 times when it is doped with suitable dopants, and it allows both p-type and n-type doping. The conductivity increases with dopant exposure time. 48 Poly( p -phenylene)s play a vital role in the fabrication of organic LEDs due to their improved optical property and blue light emission compared to other conjugated systems. The structural features of poly( p -phenylene) are dependent on temperature: it shows a planar structure at higher temperature ranges, and it shows phase transition and a distorted planar structure at lower temperature ranges. Poly( p -phenylene) has a tunable optical band gap, and structural changes occur with the addition of suitable dopants or by adding side chains. 49 Poly( p -phenylene) exhibits higher mechanical properties; also, it shows very high tensile properties compared with engineering polymers. It shows a two times higher modulus and strength compared with polyetheretherketone (PEEK) or thermosetting polyimide (PI). Polyparaphenylene has various uses in various mechanical applications within the temperature range of 140 °C. 50

Direct oxidation of benzene molecules is widely using for the synthesis of poly( p -phenylene)s. Here in this procedure dehydro coupling of benzene nuclei with an oxidative catalyst leads to the formation of carbon–carbon bonds. The polymerization reaction is carried out by using reagent consisting of a binary or a single system ( Schemes 6 & 7 ). The binary system consists of both a Lewis acid and an oxidant system, and in the case of a single reagent system (FeCl 3 ), the system acts as both a Lewis acid and an oxidative system by itself. A combination of an AuCl 3 and CuCl 2 system is an example of a binary reagent system, where AuCl 3 acts as Lewis acid, and CuCl 2 acts as an oxidant. Reactions are carried out at temperatures of 36–37 °C.

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The first chemically synthesized poly( p -phenylene) was obtained using a Wurtz–Fittig reaction, which is a metal coupling reaction ( Scheme 8 ). 51 The Ulman reaction is also used for getting poly( p -phenylene)s and the products obtained by this method have lower molecular weight and fewer structural irregularities ( Scheme 9 ). But this method is useful for the preparation of substituted phenyls such as methyl and nitro groups. 52

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The precursor method was also investigated for the synthesis of poly( p -phenylene)s. Conducting polymers are insoluble in nature and the preparation of the targeted polymer from an insoluble precursor polymer is an excellent research topic. The Marvels, Grubbs, and ICI precursor method was famous for the production of poly( p -phenylene)s. In the case of the Marvels method, the main drawback is that the product will have low molecular weight and decreased stereochemical control. 53 Electrochemical synthesis and reductive polymerization have also been used. 37

2.5. Poly( p -phenylene vinylene)

Poly( p -phenylene vinylene) was the first electroluminescent material used for the fabrication of organic light-emitting diodes due to its high optical property. It was extensively studied for the fabrication of LED displays. The crystallographic studies of poly( p -phenylene vinylene) revealed its amorphous nature and, later, the isotropic distribution of crystallites with monoclinic unit cells was observed. 54,55 In the case of poly( p -phenylene vinylene), the crystallite distribution was found to be in two planes. The electrical properties of the poly( p -phenylene vinylene) change in some orders is dependent on dopants, and it behaves as an insulator in its pristine form. The electrical properties of pristine poly( p -phenylene vinylene) depend upon the structural behaviour and also depend on the reaction conditions. When doped, its conductivity value changes from 10 −13 to 10 3 s cm −1 . 56 Poly( p -phenylene vinylene) has potential applications in optoelectronic fields like LEDs, lasers, photodetectors, etc. Due to its improved mechanical property it was used in the area of LED panels and the first fabricated poly( p -phenylene vinylene) panel was structured by sandwiching poly( p -phenylene vinylene) between an ITO anode and a low work function metal cathode. 57

There are a lot of methods available for the preparation of poly( p -phenylene vinylene). The Wittig coupling reaction has been studied extensively. In this reaction procedure, the coupling between an aromatic bisphosphonium salt and a bisaldehyde yields poly( p -phenylene vinylene) ( Scheme 10 ). A Suzuki coupling reaction was also investigated for the production of poly( p -phenylene vinylene) by Pd-catalyzed coupling of alkyl-substituted aryldiboron acids with dibromo aromatic compounds.

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Other synthesis methods have also been reported, such as electropolymerization, 58 benzoine condensation, ring-opening polymerization, metathesis polymerization, and chemical vapor deposition. 37

2.6. Polythiophenes

Polythiophene and its derivatives are extensively studied for their environmental stability, thermal stability and high optical property compared with other conducting polymers. Polythiophenes are widely used to fabricate non-linear optical devices, photochromic modules, polymer LEDs, anticorrosion coatings and are used in energy storage devices. The electronic and optical properties of polythiophenes can be modulated by doping engineering or by chemical modifications. The band gap of polythiophenes varies 3–1 eV depending on the dopant and side chain employed. 59 Poly(3,4-ethylenedioxythiophene) (PEDOT) is an important derivative of polythiophene and it was thoroughly studied for its high electrical and electro-optical properties. The main problem with the PEDOT derivative is its insolubility in water. This was successfully overcome by introducing a polyelectrolyte like polysulfonates (PSS) into the PEDOT matrix. PSS act as both a dopant and a stabilizer by a charge balance mechanism. The PEDOT:PSS derivative has high conductivity, good mechanical flexibility and long-term thermal stability. 60 The electrical properties of polythiophene and its derivatives are enhanced through solvent treatment, the introduction of a surfactant and by varying the PSS concentration. Poly(3-hexylthiophene) (P3HT) is another class of derivatives of polythiophenes and their applications are mainly focused on the opto-electronic and electronic fields. P3HT is popular because of its wide availability, low cost, well-known morphology and easy processability. P3HT is a semicrystalline polymer and its backbone is made up of isolated rings and linear side chains. This structural arrangement enables the freedom to sample conformational space. The glass transition temperature of P3HT is recorded as 12 °C and it has a high tensile modulus of 200 MPa to 1 GPa, which varies in accordance with the synthesis method and the purity of the sample. 61

Polythiophene was chemically synthesized in the early 1980s by the Yamamoto and Lin–Dudek routes ( Schemes 11 & 12 ). Other advanced techniques, like direct sol–gel, oxidative synthesis, 62 organometallic coupling reaction, 63 electropolymerization, template-assisted synthesis, and hydrothermal and solvothermal techniques, have been effectively studied. 60

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For the synthesis of polythiophene derivatives like PEDOT, PEDOT:PSS and P3TH, the composite was achieved using various techniques, including green synthesis, 64 synthesis in microfluid systems, electropolymerization and by some other novel techniques. 65,66

3. Electrical and electronic properties

The electrical properties of a material are usually explained using its electronic band structures. The energy difference between the conduction band and the valance band classifies materials from insulators to conductors. 67 Intrinsically conducting materials have a decreased bandgap, and the conduction and valance bands overlap. The electronic band theory clearly explained the case of conducting polymers, but some other studies have also revealed the transport properties of conducting polymers rather than band theory. All conducting polymers have conjugate bonds in their backbones, and these bonds are responsible for the movement of electrons: i.e. , a single bond contains a localized σ bond and a double bond has both σ and weaker π bonds. The dual relationship between first and second carbons includes a π bond and this π bond transfers to the second and third carbons, and the π bond between the third and fourth carbon transfers to the next pair; this displacement of π bonds allows the electrons to flow. 4 The conductivity shows drastic changes depending upon the dopant material, the arrangement of the polymer chain, and its length. The dopant concentration and pH value enhance the conductivity; for example, polyaniline shows excellent conductivity if the pH is maintained between 0 and 3.

Undoped pristine polymers may act as an insulators or semiconductor, and conductivity increases with increasing dopant concentration. The dopants exhibit redox reactions, and they add and withdraw electrons from the conducting polymers. 68 There are two types of doping: p-type doping and n-type doping, and the dopants produce both positive and negative polarons/bipolarons. These charge carriers are delocalized over the polymer chains, which facilitates the electronic conductivity. 16,69 In the case of p-type doping the electrons migrate from the HOMO of the polymer backbone to the dopant species and a hole is created, and this hole creates a deficiency of electrons in the backbone. But in the case of n-type doping the electrons transfer to the LUMO of the polymer backbone and electron density occurs, and these charge carriers enhance the conductivity ( Fig. 3 ). There is academic interest in p-type doping because of the high stability of positively charged carriers. 70–72

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The band structure of polypyrrole with different stages of doping was tested. Pristine undoped polypyrrole acts as a semiconductor material with a high bandgap of 3.16 eV and when it is doped with p-type materials the polymer backbone gets oxidized, and the loss of π electrons from the polymer backbone occurs. This electron loss deforms the polymer structure from benzoid to quinoid and generates one polaron in the backbone. This polaron creates a localized electronic level within the band structure, and further oxidation of bipolarons occurs due to the removal of π electrons. 73 This transformation from benzoid to quinoid form is faster in the case of bipolarons. If it is oxidized, again the bipolarons overlap, and a separate small bipolaronic band is created within the main band structure, and the band energy is reduced to 1.4 eV from 3.16 eV. In Fig. 4 , we can see the transformation of a semiconducting polypyrrole to a metallic polypyrrole. 47

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The unit cell present in the polymer backbone interacts with the neighboring unit and creates a valance band and a conduction band. Conjugative polymers have high energy levels while ionizing, and once the polymer becomes ionized, transformation of the band structure occurs. The change may be from benzoid to quinoid. 74

Analyzing Fig. 5 shows that E ip-v is the vertical relaxation energy, and E rel is termed the relaxation energy gained while ionizing, and E dis and E ip-d are the distorted energy in the ground state and ionization energy of the distorted molecule, respectively. The distortion energy leads to an upward shift of the HOMO and a downward shift of the LUMO. For the conducting polymer polyacetylene, the valance band is filled by sp 2 orbitals of the carbon atom and the s orbital of the hydrogen atom, but the conduction band is empty. The bandgap energy is almost 10 eV, and it is too high. 75,76 Trans -polyacetylene has the novelty of exhibiting a degenerated energy state, i.e. , it has two geometrical structures with the same energy, and the difference in geometry arises due to the exchange of a single bond between carbon–carbon interactions. The actual conducting mechanism in polyacetylene is well understood. As discussed above, polyacetylene acts as an insulator in its pristine form and after doping with electron-deficient or electron-withdrawing dopants (AsF 3 , Br 2 ,i 2 /CCl 4 ) it forms radical cations or polarons by removing electrons from the π bond, because the removal of an electron from the π bond is relatively easy compared to removal from a σ bond. Then after treating with dopants again, it generates bipolarons by taking one more electron from the radical present in the polaron. After the generation of bipolarons, the π bonds are shifted in between σ bonds to form solitons. The solitons can be negative or positive depending upon the dopant used. 77

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The conduction mechanism in conducting polymers has two sides. One is a chemical aspect, and the other is the solid-state physics aspect. Chemists approach a conducting polymer as a conjugative bond system, while physicists see it as a charge density wave, 78 as shown in Fig. 6 . In the case of double bonds which are more electron dense than σ bonds, the movement of a π electron is related to the oscillation of a charged density wave, and more specifically it is a bond order wave because electron density is not confined at the lattice site. 79

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3.1. Charge carrier transport models

In the conduction mechanism of conjugate polymers the charge carriers are responsible for the conduction. In polypyrrole, bipolarons trigger the conductivity while in trans -polyacetylene, solitons act as charge carriers. In conducting polymers, the charge carriers hop not only in the defective area but also in interchain gaps. Mott explains that electrical conductivity depends on temperature and concentration. Temperature dependence on conductivity can be explained by some models. 80

3.1.1. Mott model

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L and Δ E have a connection with the density of states N ( E F ).

L d Δ E N ( E F ) ∼1 where d is the dimensionality of the system. From the above equation, it is clear that the product of the number of available states in a volume L d energy interval and the density of states is of the order of one.

here n is the dimensionality of charge transfer, σ 0 is conductivity at room temperature and T 0 is Mott's temperature constant:

Investigation of the Mott model is done by plotting a graph of log σ vs. T −γ , where the least square fitted curve gives an idea about both dimensionality and the charge transport mechanism.

3.1.2. Schaefer–Siebert–Roth model

This model is slightly different from Mott's model: in the Mott model localization length and hopping distance are taken into account, but here localization length with conjugation length are taken into account. When polyacetylene is doped with p dopants or n dopants, breakage of a π bond and charge carriers like polarons and bipolarons occur, and the formation of these charge mobilizers causes the formation of different conjugation lengths within the backbone. 83

here σ 0 and T 0 depend upon localization length, and γ depends upon the density of states at the Fermi level.

4. Optical property

The electronic structure of conjugated polymers is anisotropic and quasi-one-dimensional due to the presence of π bonds in the polymer backbone by utilizing electron–phonon interactions. The electronic transport behavior in organic semiconductors is usually due to the influence of charge mobilizers like solitons, polarons, or bipolarons in the ground state degeneracy. The sub-gap optical transitions occur in the polymer backbone while doping triggers charge mobility by a shift of oscillator strength from π to π*. These nonlinear excitations are responsible for the charge mobility. The conjugated polymers behave like semiconductors in their pristine form, and they act metallically when doped with p and n dopants. In the nonlinear excitation of conjugated polymers, 84 there are some conflicts with the photoexcitation of conjugated polymers, i.e. , polarons or bound neutral excitons. 85,86 Before understanding the optical property of conjugate polymers, we need to know the basics of the physical properties of simple solids. The optical constants of solids give a complete idea of both vibronic and electronic properties, when an electromagnetic wave interacts with the polymer. The response of the system is characterized by the function of dielectric constants. 87

ε 1 ( ω ) and σ ( ω ) are the real part of the dielectric function and frequency-dependent conductivity. A reliable way to determine the optical property of a solid is to shine a monochromatic light onto the sample and calculate the values of reflectance and transmittance as a function of phonon energy. The reflectance data gives an idea of electronic structure, optical conductivity, and dielectric constant after analyzing the reflectance spectra using Kramers–Kronig analysis. 88

4.1. Electroluminescence, electrochromic and photochromic effects of conjugated polymers

Electroluminescence is a tendency to generate light by electrical excitation, and its typical behavior is observed in both organic and inorganic semiconductors. As we can see in Fig. 7 , electroluminescence requires the pumping of both electrons and holes from respective electrodes, and these opposite charges are recombined to form excitons. The radioactive decay of excitons occurs by this recombination. 89 Electroluminescence in an organic film was first investigated in 1980 by using a two-layer sublimed molecular device. This device was constructed by using two layers of thin films consisting of a hole transporting layer made up of aromatic diamine and an electron transporting layer of 8-hydroxyquinoline aluminum. Indium tin oxide and magnesium silver alloy were used as hole injectors and electron injectors, respectively. 90 A wide variety of organic polymers are used as transport layers. The conjugated polymers show semiconductor to metallic behavior by the movement of π bonds present in the backbone. The delocalization of π bonds generates charge mobilizers like polarons, bipolarons, solitons, etc. The electroluminescence in conducting polymers was first reported in poly( p -phenylene vinylene). The energy band gap of poly( p -phenylene vinylene) is around 2.5 eV, and this value lies between π and π*, and poly( p -phenylene vinylene) generates green-yellow luminescence of energy lower than its energy gap. 57 Generally, a molecule contains a single and a double bond. The π electron present in the double bond is excited to a higher energy state by absorbing photon energy which is more significant than the band gap. Similarly, in the case of conjugated polymers, the π electron present in the alternating double bonds on the backbone transfers from the HOMO to the LUMO and the energy gap E g can be even smaller. When the polymer absorbs photon energy, electron transfer from the HOMO to the LUMO occurs and the electron–hole pairs generate excitons. The conducting polymers exhibit phosphorescence and fluorescence. If the spins of both excited and lower states are the same, that kind of light emission is called phosphorescence; if spins are opposite the emission is called fluorescence. Conducting polymers show a novel optical property when doped with fullerene and the disubstituted polyacetylene shows higher photoluminescence quantum efficiency than in an undoped or monosubstituted state. 91

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Optical changes in conducting polymers occur during chemical reactions and by the effect of external factors like a strain effect on the polymer matrix as well as a shift in planarity. There are a lot of physical and chemical elements influencing the optical property like excitation and ionization impurities, phonons present in the polymer, recombination, excitons, strain factor, etc. The degree of anisotropy, conjugation length and topochemical reaction are three specific chemical aspects influencing the optical property. 92

Topochemical reactions are triggered by exposure to UV radiation, gamma radiation and X-ray radiation, by thermal annealing. Solvent types also induce topochemical reactions. The criteria for this kind of reaction are that the stereochemistry of the dimer is determined by the contact geometry of the nearest neighbor's double bonds, and the distance between adjacent monomers must be less than 4 Å. 93,94 A topochemical reaction is used to conduct polymerization of a conjugate system such as polydiacetylene or polyaniline. Irradiation causes hydrogen bonding between polymer and head groups. This weak intermolecular hydrogen bond bends the polymer backbone and builds it into a zigzag structure which causes a change in color to red. A strong intermolecular bond makes an extended chain-type structure that gives a blue color to polyacetylene. The temperature also affects the optical behavior, i.e. , polydiacetylene shows a red-to-blue transformation at low temperatures, and poly(3-hexylthiophene-2,5-diyl) (P3HT) changes from yellow to magenta at higher temperature. 95 The same trend was observed in polymers when changing the solvent ratio and conjugation length. Conjugation length is defined as the number of uninterrupted π bonds in the conjugated system. On the other hand, it is the defined length of the oligomer containing a specific number of monomer units. Samuel et al. developed a model that relates molecular weight to conjugation length with absorbance. When polymers have higher conjugation length, the polymer will show high molecular weight due to the presence of the π bond because a high number of π bonds increases the molecular weight, which leads to a higher absorbance rate. 96

Photochromism is a phenomenon of light-induced reversible change in the color of chemical species. The two forms have different absorption spectra. The change occurs with a change in physical properties, including viscosity, dielectric constants, surface wettability, and refractive index. This controlled modulation of properties paves a path to the field of optical switches. The light-induced transformation enables a transition from thermodynamically stable state A to less stable state B, in which both states have different absorption spectra. The inter-transition also allows movement from B to A either thermally or photochemically. Generally, most photochromic materials exhibit a colorless state when they are stable and a color transition occurs when moving to an unstable state. Both inorganic and organic materials exhibit a photochromic effect. 97 Organic materials like polyaniline, polypyrrole, PEDOT, PEDOT:PSS, and P3TH show a photochromic effect due to the pericyclic reaction, cis – trans isomerization or intramolecular hydrogen/group transfer process. 98 Organic field emitting transistors have a huge global market and research interest due to their wide applications in the fields of flexible devices, memory, sensors, and smart cards. The fabrication of conventional OFETs with functional molecular blocks is the latest research trend due to the sensitivity of organic functional groups towards pressure, temperature, light, etc. 99 The change in color with changes in viscosity, wettability, refractive index, and solubility in photochromic materials have applications in sophisticated electronic devices. Photochromic camera lenses and photochromic camera filters led the global market and were replaced by organic conducting polymers due to their low weight and higher comfort.

On the other hand, most conducting polymers show electrochromic properties. Electrochromism is defined as an external voltage triggering a reversible change in the optical property of a material. 100 The first electrochromic device was fabricated by Deb et al. during research into amorphous and crystalline materials. Transition metal oxides were the most studied and explored in the field of electrochromic materials and were later followed by small organic materials. Conjugated polymers, another set of electrochromic materials, are in the limelight due to their high optical contrast and easy modification of their structures to develop new electrochromic devices. 101 Generally, electrochromic materials are classified based on their electronically accessible optical states. The first set of materials like PEDOT have only one colored state during the application of an external voltage. The second type of materials including polythiophenes have two colored states and the third class of materials have more than two colored states depending on their redox state. 102 Some conducting polymers like polyaniline 103 and poly(3,4-ethylene dioxythiophene) 104,105 are inherently multi-colored systems and have a wide variety of optoelectronic applications. The mechanism behind electrochromism is a change in pi-electron character with electrochemical oxidation or reduction. Electrochromic cells, 106 LCDs and electrochromic smart widows are the main applications of electrochromic materials. 107

5. Mechanical properties

The mechanical properties of polymer materials depend upon the monomer arrangement and crystallinity. A crystalline polymer has better mechanical properties compared with amorphous semi-crystalline polymers. The macroscopic mechanical property of conducting polymers depends upon the microscopic change in the molecular mobility of macromolecules. Molecular mobility depends upon factors like the structure of branching polymer conformations and macroscopic properties like pressure–temperature etc. In the case of amorphous polymers, the distribution and arrangement of monomers are random, and crystalline polymers are not stacked. The molecular motion is higher in amorphous polymers, and when temperature reaches T g the polymer is transformed to a rubbery state from its glassy state. This transition leads to a change in mechanical properties. The mechanical property of a polymer depends heavily upon the molecular weight: i.e. , the toughness and strength parameters are related to molecular weight and chain entanglement. 108–110 The engineering stress–strain curve of the polymers is a plot between strain on the x -axis and stress on the y -axis ( Fig. 8 ). A graphical model of the stress–strain curve is given below. From the graph of the region, OA is represented as an elastic region. In the elastic region, the material will return to its original place after removing the load. The region AB represents the plastic region. The movement of the molecule is high, and deformation occurs on the material when the load is removed. In the elastic region, the material obeys Hook's law. After point A (the elastic limit), the material becomes visco-plastic and permanent deformation occurs. 111

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5.1. Elasticity and Young's modulus

The conducting polymers both expand and contract electrochemically: i.e. , a redox reaction causes the elasticity. When anions are excluded from or included in the polymer matrix, it becomes strained. The magnitude of the strain depends upon the number of anions. The electrochemical deformations are utilized in the application of artificial muscles. When the polymer is oxidized by applying a positive voltage with a suitable electrolyte, the material loses electrons from the polymer and a pair of anions is formed in the electrolyte. This anions cause the expansion of the polymer. The contraction with reduction is similar to expansion with oxidation. Investigation of stress–strain analysis has been undertaken using different techniques like AFM, nanoindentation, a conventional pull test, and electrochemomechanical actuators. 110

The mechanical property depends upon the molecular weight of the polymer, and the effect of different molecular weights M n = 20, 25, 90, and 110 kg mol −1 on the modulus of poly(3-hexylthiophene) has been investigated. The results reveal that a material with a lower molecular weight shows brittle tensile behavior, constrained molecular mobility, and the extended chain crystals cannot withstand a higher strain rate. When the molecular weight increases, the moduli increase drastically, and they provide a high elongation of 300%. Another procedure is to place the film over a water surface, where the same trend is observed. A material with a higher amount of ductility and toughness shows resistance against fracture, which helps for stretching over curved surfaces like vehicle body parts. A comparison of the moduli in both techniques of film on water and film on an elastomer was undertaken. From these two tests it is observed that the modulus value is three to six times higher in the case of the film on an elastomer and the material shows constant moduli for samples ≥40 kDa in film on water testing. 112 The mechanical behavior of a conducting polymer is investigated by using various theoretical techniques like strain-induced elastic buckling instability. Hutchinson and co-workers developed a quantitative idea of the surface wrinkling patterns of stiff polymers. This technique is useful for the mechanical analysis of organic semiconductors, polymer films, carbon nanotubes, fibrous polymer materials, polyelectrolyte multilayer films, conjugated polymers, etc. The moduli of the system have been evaluated by placing the conjugated polymer coatings on soft substrates and related to bucking instability.

where λ b is the buckling wavelength which is related to the polymer film thickness d f and tensile moduli of both film and substrate E s and E f respectively. The Poisson ratios of both film and substrate are noted as ϑ f and ϑ s . The Poisson ratios are assumed to be 0.5 and 0.35 for PDMS and conjugated polymer films, respectively. Seitz had developed a theoretical method for the determination of the mechanical behavior of polymers by considering molecular properties like length and rotational bonds present in the polymer, molecular weight, van der Waals, glass transition temperature, and length of rotational bonds. The model was modified for materials with glass transition temperatures above room temperature or below room temperature. The tensile modulus of the polymer is related to the bulk modulus and Poisson ratio. 113

The bulk modulus of the material has been given by the Lennard–Jones potential equation, which is attributed to the function of cohesive energy E coh and molar volume V at room temperature.

where V 0 is the volume at the energy minimum. The cohesive energy from the molecular structure was evaluated using the Fedors method, and the molar volume has been calculated by using empirical correlation depending on the T g value of the polymer. The value of molar volume depends upon the glass transition temperature: i.e. , T g higher than room temperature, T g close to room temperature, or T g below room temperature.

The Poisson ratio of the polymer is modelled with the molecular correctional area, which is given as

The molecular correctional area depends upon factors like van der Waals volume V w and length of the monomer chain in its fully extended conformation.

where N A is Avogadro's number. Both V w and l m are estimated from the structure of the monomer.

5.2. Structure–property relationship

There are a lot of structural properties like side chain length, regioregularity, degree of polymerization, and presence of non-conjugated monomer units, which can affect the mechanical properties of conjugated polymers. 114 The side chain attached to conjugated polymers results in novel polymers with unique physical and chemical properties. Attached aliphatic chains play an important role in the mechanical properties of conjugated polymers. The glass transition temperature of both engineering and conjugated polymers will decrease when attached to side groups. Gu et al. discovered that the mechanical properties of the conducting polymer polydiketopyrrolopyrrole will depend strongly on the length of the attached side chain. Here they observed that an increase in alkyl side group on the polymer backbone will reduce both the elastic moduli and tensile strength of the polymer. 115 The hydrogen bonding present in the side chain also affects the mechanical and electronic properties of conducting polymers. 116 Another factor that depends on the mechanical property is the bonding arrangement of the monomer unit present in the polymer. The increase in regioregularity of polythiophene and its derivatives will increase the tensile strength and decrease the polymer toughness and elasticity. 117,118 The high degree of polymerization will enhance the chain entanglement in the polymer system and this entanglement will affect the physical properties. The entanglement will resist cavitation and crack formation. It also protects against the breakage of the polymer chain. 110,119

6. Applications of conducting polymers

6.1. supercapacitors.

The world economy plays an important role in the utilization of fossil fuel sources, natural gas, and coal. The depletion of fossil fuels is causing a lot of social and environmental problems. Due to climate change, global warming, and health issues, the replacement of conventional energy sources is mandatory. Because of this, scientists have put their effort into developing eco-friendly, high-energy, renewable energy resources, including supercapacitors, fuel cells, and wind energy. Nowadays, supercapacitors are of great commercial interest because of the future markets for wearable devices, electric vehicles, etc. The main difference between conventional capacitor and supercapacitor devices is that they store 1000 times more energy than a dielectric capacitor. Also, they have a high-speed charge–discharge cycle, and they exhibit high energy and power density and also good cycle life. 120

Supercapacitors are mainly of three types depending on their charge storage mechanism. In the case of an EDLC, it works by a non-faradic process, and the accumulation of charge happens in the interface between electrode and electrolyte. An electrochemical double layer of charge occurs and this double layer is responsible for capacitance. Carbon-based materials such as carbon, carbon nanotubes and graphene with high surface areas are mainly governed by this energy storage mechanism and are commonly used as electrode materials for EDLC. In the case of pseudocapacitors, they work by a faradic process, and charge storage happens by a redox reaction or intercalation process. Pseudocapacitors have increased power density and energy density compared to EDLCs. 121 Conducting polymers 122 and transition metal oxides such as Mn 3 O 4 (ref. 123 ) or Co 3 O 4 (ref. 124 ) have been extensively used as electrode materials for pseudocapacitors due to their redox activity. Hybrid supercapacitors are a combination of both EDLCs and pseudocapacitors. EDLCs show proper specific capacitance and good cycle stability and pseudocapacitors have good energy and power density. In hybrid capacitors, the advantages of both EDLC and pseudocapacitor are present. 75

Conducting polymers have many applications due to their electrical properties, high theoretical capacitance, good wave absorption, 125 high redox activity, and excellent electrochemical behavior. 126 Conducting polymers are available in different morphologies like sheets, particles, hydrogels, rod-like structure, etc. 127 These different morphologies have different electrical, mechanical and optical properties ( Fig. 9 ). 128 The specific capacitance of a composite depends heavily on the material morphology. Zhang et al. investigated the synthesis and evaluated the performance of porous carbon nanosheets/polyaniline nanowires for high-performance supercapacitor applications. Generally, carbonaceous materials like graphene, activated carbon, or graphite are composited with polyaniline to overcome the cycle stability drawback of polyaniline. The main demerit of polyaniline carbonaceous composite materials is that they aggregate at the time of synthesis, which reduces the active sites and increases ion mobility, severely affecting the performance of the supercapacitors. To overcome this problem, researchers focused on 3D porous carbons. 129 Here, the composite was synthesized by an in situ chemical oxidative method using ammonium persulfate. Aniline concentration also plays an important role here because aniline concentration increases the specific capacitance. Here polyaniline shows an antagonistic effect. The supercapacitance performance of the composite was studied using CV and GCD. From the electrochemical data, it was shown that the specific capacitance of PC/PANI is 512 F g −1 , which is much higher than that of PC or polyaniline (250 and 201 F g −1 ) at a current density of 1.0 A g −1 . From the asymmetric data, it was revealed that PC/PANI//PC has a proper capacitance of 77 F g −1 at a current density of 1.0 A g −1 . The maximum energy density and power density are 17.1 W h kg −1 and 14 000 W kg −1 which are higher than previous reports ( Fig. 10[A](a–e) ). 130

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The mechanical stability of polyaniline is effectively utilized in the fabrication of flexible supercapacitor applications because of its easy synthesis, redox characteristics, conductivity, etc. Sharma et al. investigated the performance of a three-dimensional cellulose/graphite/polyaniline ternary composite. In this study, they followed a novel synthesis method to fabricate the supercapacitor. They pasted graphite sheets on top of cellulose paper by sandwiching them with PVDF. This flexible cellulose graphite sheet was further used for the electrodeposition of polyaniline. From the electrochemical data, we can see that it provides an excellent specific capacitance of 357 F g −1 in a three-electrode setup and a specific capacitance of 256 F g −1 in a two-electrode system at a current density of 100 mA cm −2 . The high specific capacity is due to the higher number of active sites for a redox reaction in polyaniline nanowires. These supercapacitors show a high specific energy of 64.8 W h kg −1 , an energy density of 6.48 W h L −1 , and a cycle stability of 86% after 1000 cycles. 131

Carbonaceous materials like CNTs, graphene and graphite have potential applications in different fields due to their structural, mechanical and electrical properties. SWCNT and MWCNT have been widely used in supercapacitor applications over the last decade. 132 Simotwo et al. studied the synergetic effect of both CNT and polyaniline. They synthesized high-purity electrospun polyaniline and polyaniline/carbon nanotube fibers, and their supercapacitor performance was investigated. Electrospinning is a fiber production method using electric charge. Here poly(ethylene oxide) was used as a carrier polymer for electrospinning. The PANI : CNT : PEO weight ratio was kept fixed at 81 : 12 : 7. From the electrochemical data, CV shows that a polyaniline/CNT composite has good specific capacities of 324 and 281 F g −1 at 5 mV s −1 . When the GCD current density was varied from 0.5 to 10 A g −1 PANI/CNT gave a specific capacitance of 380 F g −1 and polyaniline gave 308 F g −1 at a current density of 0.5 A g −1 . From the CV graph, anodic and cathodic peaks in PANI/CNT undergo a slight shift to the left or right directions with increasing scan rate. This may be due to the internal resistance and also due to the phase transfer of polyaniline from the emeraldine salt to luecoemeraldine salt form in the presence of CNTs. 133

As discussed before, morphology plays a vital role in the performance of a supercapacitor. It is possible to synthesize a variant morphology of polyaniline by controlling the hydrothermal conditions. 134 Among the studied composites of polyaniline, polyaniline/graphene is of great industrial interest because of the synergetic π–π effect. Wang et al. evaluated the synthesis and SC performance of graphene polyaniline composites following two-step hydrothermal synthesis to obtain the composite. In this controlled synthesis, they tried different temperature ranges and the performance of each composite was evaluated. They first synthesized a GO/polyaniline intermediate suspension, and this was transferred into an autoclave and the reaction was carried out at various temperatures like 120, 150 and 180 °C. By analyzing Fig. 10[B](a–f) , we can clearly understand that S120 gives excellent SC performance compared to the others. From the CV data, the GNS/PANI composite shows a proper capacitance of 532.3 F g −1 at a scan rate of 2 mV s −1 with good cyclic performance (capacitance retention is as high as ∼99.6%) after 1000 cycles. 135

Nanomaterials with high surface area and good porosity have been suggested as good electrode materials for supercapacitors. 136,137 Among conducting polymers, polypyrrole has good conductivity, good redox reversibility, high environmental friendliness, and mechanical stability. Due to these properties, polypyrrole is used in different applications like corrosion inhibition, 138 sensors, 139 supercapacitors, fuel cells, 140 etc. Nanostructures of polypyrrole can be easily synthesized by the direct electropolymerization of monomers on the substrate. Deepak P. Dubal et al. effectively investigated the structural and electrochemical properties of potentiodynamically synthesized polypyrrole. Here they synthesized different morphologies of polypyrrole by varying the electrochemical parameters ( Fig. 11[A](a) ). When the scan rate is increased, the morphology changes from nanobelts to atomically thin nanosheets. Analyzing the CV and GCD data from Fig. 11[A](b and c) clearly shows that the morphology plays an important role in the specific capacitance and stability after 5000 cycles. Here the nanobelt morphology has the lowest specific capacitance of 296 F g −1 , the nanosheets possess a higher value of 584 mF g −1 , and nanobricks have an intermediate value of 357 F g −1 . Nanosheets possess a high discharge to charge efficiency of 91%. 61 Ge et al. investigated the performance of rGO/PPy nanofilms. They were fabricated by vacuum filtration along with the electrochemical reduction of graphene oxide. This free-standing rGO/PPy film has both high mechanical and electrochemical properties. From electrochemical data, it shows a high areal capacitance of 216 mF cm −2 at 0.2 mA cm −2 , and a high capacitance retention rate of 87% after 5000 cycles. 141

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Coaxial supercapacitors are very hard to fabricate because of their precise layer-by-layer arrangement of positive and negative electrodes. The main interest behind coaxial supercapacitors is they do not need any supporting materials and also that they have good ion transport between positive and negative electrodes. This is because of the short separation distance. Cheng et al. evaluated the performance of MnO 2 nanosheets integrated with CNT/PEDOT:PSS coated CNT fibers. The PEDOT:PSS coating was done by continuous dipping of CNT fibers in PEDOT:PSS solution followed by annealing at 120 °C. The ternary CNT/PEDOT:PSS/MnO 2 fiber electrode was achieved by the electrochemical growth of MnO 2 on the CNT/PEDOT:PSS fiber. CNT/PEDOT:PSS provides both pseudocapacitance and binding action to combine both the outer MnO 2 layer and inner CNT fiber. From electrochemical data, it is proven that CNT/PEDOT:PSS/MnO 2 has an excellent specific capacitance value of 411.6 F g −1 , better than that of CNT/MnO 2 . It provides a high capacitance retention rate of 91% over 10 000 cycles. 142 Similarly, Yao and co-workers investigated the performance of a coaxial fiber shaped asymmetrical supercapacitor with a CNT core covered with vanadium nanowire arrays as the negative electrode material with an Na 2 SO 4 /PVA gel electrolyte. Here the positive electrode MnO 2 /PEDOT:PSS/CNT sheet was wrapped over the negative electrode. Initially MnO 2 was deposited electrochemically over CNT fiber. From the electrochemical data, it delivers an excellent areal capacitance of 213.5 mF cm −2 with a corresponding energy density of 96.07 μW h cm −2 and excellent flexibility. 143

Conducting polymers have utilized the advantages of metal oxides in many composites because of their high theoretical capacitance, high electrochemical activity and reversibility properties. 144 Cobalt oxide has a low electronic property and the worst electrochemical cycle stability. To overcome these drawbacks, carbon matrices, like CNT, graphene, etc. , have been assembled. A hybrid with carbonaceous materials overcomes the above disadvantages of cobalt oxides. Raj et al. synthesized a Co 3 O 4 /polyindole composite via an electrodeposition method for supercapacitor applications. They chose polyindole because it gives higher thermal stability, higher redox activity, slower degradation and higher thermal stability than other conducting polymers like polyaniline or polypyrrole. The electrochemical properties of this hybrid system were studied by CV and GCD analysis. From the data, Co 3 O 4 /polyindole gives a very good specific capacitance of 1805 F g −1 while pristine Co 3 O 4 has a specific capacitance of 1565 F g −1 at a current density of 2 Ag −1 . 145 This is much higher than previously reported for hybrids like CNT/Co 3 O 4 (ref. 146 ) or Co 3 O 4 /graphene 147 composites.

Transition metal dichalcogenides like MOS 2 , MoSe 2 , NbSe 2 , MoTe 2 or WTe 2 are promising materials for supercapacitor applications. They have a good electric double layer property, and they also have excellent mechanical and electrochemical stability. 148 Pristine MoS 2 itself gives very high specific capacitance and they also have different phases like 1T, 2H or 2R. 149 I-Wen Peter Chen and his co-workers developed an ultrathin MoS 2 /PANI/CNT composite paper type flexible supercapacitor with an unusual volumetric energy density. Transition metal dichalcogenides have different phases according to which specific capacitance changes. They have synthesized the composite by a chemical in situ polymerization technique and different compositions have been tried. Among the synthesized composites, a composite with a high amount of polyaniline had a better specific capacitance than MoS 2 and a composite with the right amount of MoS 2 showed a high energy density of 0.013 W h cm −3 and an ultrahigh power density of 1.000 W cm −3 . Most of the 2D materials have good electronic properties and good electrochemical activity. 150 K Balakrishnan et al. synthesized different polyaniline-2D material composites, and composite performance was evaluated by electrochemical characterization techniques. We all know that 2D materials have novel structural and electrochemical activities, and that they show good specific capacitance in their pristine forms. Here they investigated polyaniline nanocomposites of few-layered MoS 2 , WS 2 , borocarbonitrides (B x C y N z ), and nitrogen-doped rGO. Borocarbonitrides (B x C y N z ) contain different proportions of boron, carbon and nitrogen, and they have a hexagonal BCN structure like graphene. The property of BCN changes with changes in the proportions of B, C, and N. They exhibit a composition-dependent electronic property. Depending on the composition, the band gap varies between 1.0 and 3.9 eV and a carbon-rich composition possesses a huge bandgap. 151 In this work, they studied the supercapacitor behavior of polyaniline nanocomposites of MoS 2 , WS 2 , borocarbonitrides (B x C y N z ), and nitrogen-doped rGO. Synthesis was through an in situ chemical polymerization technique, and electrochemical performance was evaluated in three-electrode systems with 2 M H 2 SO 4 as the electrolyte. By understanding CV and GCD data, it is clear that the 1 : 1 composite has less specific capacitance and capacitance rises with increasing polyaniline content. 152 Among the composites, the NRGO/polyaniline composite has a good cycle retention property. In the impedance data, it is clear that NRGO and MoS 2 polyaniline composites have good capacitance properties in the lower frequency range. Pristine polyaniline possesses higher resistance than its composites ( Fig. 11[B] ).

MoS 2 has a considerable interlayer distance. It possesses good chemical and electrochemical stability due to this. They are widely used in Li-ion batteries and supercapacitors. Interlayers are attracted by weak van der Waals forces. Intercalation is the easiest process to obtain monolayered MoS 2 . The monolayered MoS 2 nanosheets are used as a template for growing conducting polymers. Wang et al. have developed a pizza-like MoS 2 /polypyrrole/polyaniline ternary nanostructure. This ternary hybrid system is synthesized by a two-step in situ chemical route. The main problem of conducting polymers is that they have very poor cycle stability. To overcome this problem, conducting polymers are used to make hybrid nanostructures with carbonaceous and other materials. In this study pristine MoS 2 and MoS 2 /PPY show an ideal rectangular CV curve without characteristic redox peaks and a fast charge–discharge cycle. While polyaniline and binary hybrids of polyaniline show a CV curve with redox peaks. On analysis, it is clear that the MoS 2 /PPy/PANI ternary system has an enlarged area and it exhibits a good specific capacitance of 1273 F g −1 at 0.5 A g −1 . Performance is maintained at 83% after 3000 charge–discharge cycles with high cycle retention. 153

A summary of studies on the use of conjugated polymers in supercapacitor applications is given in Table 1 .

Polymer	Electrolyte	Specific capacitance	Cycle stability	Energy and power density
Polyaniline/graphene	EMITFSI/PVDF–HFP	87.8 mF cm at 0.22 mA cm	100% after 10 000 cycles	12.2 μW h cm and 226.4 μW cm
Polyaniline/graphene/Fe O hydrogel	1 M H SO	1124 F g at 0.25 A g	82% after 10 000 cycles	14.4 W h kg and 58 W kg
MnO /polyaniline/hollow mesoporous silica	PVA–KOH	248.5 F g at 1 A g	>97.7% after 5000 cycles	88.4 W h kg and 800 W kg
Polythiophene-graphite graphene oxide	1 M KOH	971 F g at 1 A g	98% after 10 000 cycles	38.11 W h kg and 7000 W kg
PEDOT:PSS/rGO	1 M H SO	249.5 F g at 0.5 mA	75% after 2000 cycles	10.68 W h kg and 81.25 W kg
NiCO-MOF/polypyrrole	2 M KOH	1109 F g at 0.5 A g	79.1% after 10 000 cycles	41.2 W h kg and 375 W kg
rGO/PEDOT/PANI	Solid electrolyte	388.5 F g at 5 mV s	99% after 10 000	26.89 W h kg and 800 W kg
SDBS doped polypyrrole/HC	6 M KOH	1086 F g at 5 mV s	90% after 2500 cycles	218.05 W h kg and 1075 W kg
Ti C /polypyrrole	2 M H SO	109.4 mF cm at 1.05 mA cm	96% after 10 000 cycles	3.398 μW h cm and 0.0845 mW cm
Carbonized iron/polyaniline/graphene Ni foam	1 M NaNo	69.9 F g at 1 A g	91% after 10 000 cycles	68 W h kg and 718.2 W kg
CuS/C@polyaniline	3 M KCl	425.53 F g at 1 A g	89.86% after 3000 cycles	—

6.2. Corrosion inhibition applications

Metals have potential applications in automobiles, construction, energy, household industries, packaging, and aerospace. Due to this, they have a perfect global market. When metals are exposed to moisture, or an acid or alkaline environment, they degrade very rapidly. The economic aspect of corrosion is unbelievable. In the USA and developing countries like Nigeria, 300 billion dollars and 10 billion dollars are respectively spent every year on research into and prevention of corrosion. 165 Inspired by this, researchers have paid good attention and are focusing on corrosion–resistant coatings. Nowadays, a variety of corrosion inhibition techniques and coatings are available. In earlier years, chromate-based primers were quite extensively used because of their high corrosion–resistant property. Chromate coatings are used as both anodic and cathodic inhibitors. They have good adhesion with the metal surface and with topcoats and they are also economically feasible. 166,167 The main demerit of chromates and chromium-containing coatings is that they are hazardous to both the environment and to human life (they are carcinogenic). For this reason, the Environmental Protection Agency (EPA) has limited the use of chromate conversion coatings. 168 Nowadays, chromate conversion coatings have been replaced by organic coatings like epoxy, 169 acrylic, 170 polyvinyl butyral, 171 etc. Conducting polymers and conducting polymer pigmented paint coatings play a very potent role in corrosion inhibition. Conducting polymers have been receiving increasing attention, as possible components of corrosion–resistant coating systems, due to their ability to maintain the stable passivity of a metal by an anodization process coupled with O 2 reduction on the surface of the film. They form a metal oxide interface layer between metal and coating. Also, in the case of phosphate pigments, specifically phenyl phosphonic acid, they can form a metal phosphate thin film on the metal surface, and this phosphate layer inhibits corrosion effectively. 172

The mechanisms behind the corrosion inhibition property of polymers are given below.

1. Anodic protection mechanism: in this mechanism, polyaniline can generate a metal oxide layer above the metal surface and beneath the coating. These metal oxide layers act as a powerhouse for corrosion inhibition. 173

2. When a metal comes into contact with conducting polymers, an electric field is generated. This electric field restricts the flow of electrons from the metal to oxidized species. Thus, corrosion inhibition occurs. 174

3. Conducting polymers, especially polyaniline, have the property of controlled release of inhibitors upon reduction. A conducting polymer-based coating deposited on the metal surface will release the anion when reduction occurs. This property reduces corrosion. 175

Among coatings, epoxy-based coatings are widely using in corrosion inhibition applications. Pigments are an important ingredient in these coatings, to achieve the desired application. As we discussed above, chromates are one of the main pigments used for corrosion inhibition. Due to their environmental and social problems, chromate conversion coatings are being replaced by other pigments. Graphene-incorporated coatings are also studied because of their hydrophobicity, sheet-like morphology, inertness, and because they act as a barrier to chemical aggressiveness. Zinc phosphates are also a very commonly used anticorrosion pigment because they are less toxic and have lower toxicity than chromates. Zhu and his co-workers investigated the synergetic effect of polypyrrole functionalized graphene and zinc phosphate pigmented epoxy coatings. From an electrochemical impedance spectroscopy study, it is clear that a coating containing a high amount of polypyrrole gives a good coating resistance R ct value in 3.5% electrolyte. The R ct values are 8.4 × 10 4 Ω cm 2 , 7.7 × 10 4 Ω cm 2 and 2.5 × 10 4 Ω cm 2 with corresponding exposure times of 2, 24 and 240 h. From this we can observe that there is only an insignificant change in R ct . The addition of GO–PPy nanocomposites to the ZP coating accepts electrons and transitions from the oxidized state to the reduced state. The increased Fe 3+ and Fe 2+ ions are converted to a passive film of an oxide layer (Fe 3 O 4 and Fe 2 O 3 ). 176

Sathyanarayanan et al. developed polyaniline pigmented epoxy and vinyl acrylic organic coating, and evaluation of its performance was carried out on stainless steel. From their studies, they pointed out that the electrochemical impedance spectroscopy value initially decreases gradually; then the impedance value increases with an increase in exposure time. This phenomenon is due to the formation of pinholes on the surface of the metal surface. On increasing the exposure time, the coating adsorbed a metal-oxide interface layer in between the metal surface and beneath the coating. 177 From their studies, they noticed that polyaniline pigmented organic coatings are very effective as corrosion inhibition coatings, and that this depends on the coating thickness and exposure time. They also observed that the corrosion resistance first decreases initially from 10 8 to 10 6 ohm cm 2 ; then the coating resistance increases due to the passivity property of the polyaniline pigment. 178 Lei et al. investigated the anticorrosion behaviour of polyaniline/CeO 2 incorporated epoxy coating. Polyaniline/CeO 2 was synthesized by a hydrothermal route followed by in situ polymerization. From analysis of the potentiodynamic polarization curve, the conducting polymer pigmented composite shows higher corrosion potential and lower corrosion current density than the control sample. The conducting polymer composite coating shows an improved anticorrosion tendency on a defective site after continuous salt spray analysis 179 ( Fig. 12[A] ).

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Electrochemically synthesized coating and polypyrrole pigmented organic coatings have also been explored. Armelin et al. utilized polypyrrole and polyaniline as anticorrosive additives in zinc epoxy coating, and their performance was evaluated via an immersion test and some standard ASTM tests. In this study, they made epoxy paint with and without the conducting polymer pigment and the performance of the coating was evaluated separately. From the research, they observed that it exhibits reversible redox properties like chromate coatings and this enhances its corrosion inhibition property. Zinc pigments generate zinc oxides which cover the metal layer and reduce the corrosion tendency, In this study, we can observe that by increasing the polypyrrole percentage beyond a certain limit, a better inhibition property is not exhibited. The percentage of polypyrrole must be optimum. 138 Aguirre et al. studied the synthesis and performance evaluation of a poly(3,4-ethylendioxythiphene) PEDOT conducting polymer on a stainless alloy. They synthesized PDOT by cyclic voltammetry, giving 10 cycles in the potential range from −0.7 to 1.3 V at a scan rate of 0.05 V s −1 . Here the corrosion inhibition property of the coated metal was studied electrochemically as well as through physical evaluation. Visual analysis and a peel test were undertaken in consecutive time intervals. Electrochemical analysis was done by OCP analysis from polarization curves. From the above characterizations, they concluded that PEDOT is an excellent promising material for the inhibition of corrosion. 180

Kalendova et al. discovered that epoxy paint contains polyaniline with acidic basic and neutral extracts like Zn 3 (PO 4 ) 2 ·2H 2 O, Ca 3 (BO 3 ) 2 and SrCrO 4 . From these studies, they observed that PANI + Zn 3 (PO 4 ) 2 ·2H 2 O has a good corrosion inhibition property in both NaCl and SO 2 . 181 Electrochemically synthesized polypyrrole on Q235 steel with different dopants like oxalic acid, sodium dodecylbenzene sulfonate, toluene- p -sulfonic acid, sulfamic acid, or phytic acid was studied. The thickness of the coating was controlled to 40 μm. The anticorrosion behavior of all the above coatings was studied using dynamic potential polarization curves and electrochemical impedance spectroscopy. Fig. 13 clearly shows that polypyrrole coated metal is more suitable than bare metal. Among the above dopants, SDBS–PPy shows better anti-corrosion performance than other dopands. 182

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Many scientists have adequately studied the anticorrosion behavior of carbonaceous material. Carbon dots, carbon nanotubes, graphite, graphene and graphene oxide have been adequately investigated. It was observed that these materials possess a high rate of corrosion inhibition property. V. Martina et al. investigated the synergetic effect of a carbon nanotube polyaniline nanocomposite. Here studies were done through FTIR spectroscopic characterization before and after coating. Spectral analysis was utilized to understand the role of composite films in corrosion protection and to discriminate the best-performing CNTs. 183 Electrochemically deposited polyaniline graphene nanofilms were synthesized along with the composite coatings and their cyclic voltammetry (CV) was investigated with a working electrode potential between −0.8 and 1.6 V at a scan rate of 0.05 V s −1 for 10 cycles. After electrochemical studies, they observed that the corrosion inhibition property of the polyaniline graphene composite is about 97%. 184 Chemically synthesized polypyrrole–graphene oxide nanosheets blended with waterborne epoxy coating were studied. In GO–PPy nanosheets with zinc phosphate pigment (from the electrochemical impedance spectroscopy analysis) the coating process was found to have a very high rate of anticorrosion property compared to other coatings. This property is attributed to more complex arrays of non-agglomerated GO–PPy sheets and the passivation function of zinc phosphate in the coating. 176 Montmorillonite polyaniline nanocomposite coatings also show outstanding corrosion inhibition behavior. The property of this composite using a series of potentiodynamic and impedance spectroscopy measurements in 3.5 wt% aqueous NaCl solution was investigated. From these studies, they discovered that the corrosion current ( i corr ) values decreased greatly. 185

Yue Su and co-workers developed a PEDOT:PSS-exfoliated graphene pigmented water-borne epoxy coating. PEDOT:PSS has an outstanding tendency to develop a metal oxide layer in between the topcoat and the metal surface, which protects the metal from degradation. As seen in Fig. 14(a) , the π–π interaction between graphene and conducting polymer leads to exfoliation of graphene into monolayers. This will enhance the dispersion of graphene in the conjugate polymer matrix. The coated metal surface after a salt spray test reveals that the coating containing both conducting polymer and graphene protects the metal in a good way ( Fig. 14(b) ). Analysing the electrochemical data clearly shows that a graphene pigmented epoxy coated metal surface has a lower inhibition property than a pure epoxy coating and degradation occurs with increasing soaking time ( Fig. 14(c–h) ). Coating with both a conducting polymer and graphene gives a high impedance value. The coating develops a metal oxide layer after soaking. 186

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Corrosion is primarily due to atmospheric exposure and the electrochemical activity of metals. Corrosion inhibition is mainly attributed to the incorporation of an anticorrosive pigment and the placing of a physical barrier to prevent moisture contact. Hydrophobic coatings are preferred for their water-repellent properties. PANI/TiO 2 coating possesses good thermal conductivity, good hydrophobicity, and good anti-corrosion activity. Thermal conductivity plays a vital role in the durability of a coating because thermal conductivity increases heat dissipation. It prevents the delamination of a coating resulting from heat expansion. Analyzing EIS data, it is clear that the PANI/TiO 2 coating exhibits a greater area in the Nyquist plot. This means that the composite provides better corrosion inhibition. The hydrophobicity of a coating is evaluated by contact angle measurements. If the contact angle is below 90°, the coating must be hydrophilic and if contact angle is above 90°, the coating shows hydrophobicity. Here PANI/TiO 2 has a contact angle of 150°, so it is clear that the coating is super-hydrophobic in nature. 187

Before painting metal substrates, a chromate treatment or wash primer coat will be applied. Due to their toxicity and environmental issues, chromate conversion coatings have almost been replaced by wash primers. Generally, wash primers are made from polyvinyl butyral resins. The wash primer itself acts as a corrosion inhibition coating. To obtain a higher amount of anti-corrosion performance, polyaniline incorporated wash primers are being studied. In this work polyvinyl butyral containing polyaniline and chromate pigments are studied separately. By analyzing the electrochemical impedance data for 1–10 days in 3% NaCl electrolyte, it is clear that a polyaniline pigmented wash primer has a coating resistance value of 4 × 10 3 to 2.3 × 10 3 which is almost the same as that of a chromate pigmented primer (1.4–5.19 × 10 4 ). 188

A summary of studies on the use of conjugated polymers in corrosion inhibition is given in Table 2 .

Substrate	Organic solvent	Anticorrosion pigment
Steel	Water-borne epoxy	Polyaniline/poly(methyl hydrosiloxane)
Carbon steel	Epoxy	Polyaniline/F-silicon nitride
Glass	Epoxy	Fluro substituted polyaniline
Carbon steel	Epoxy	Polyaniline–CNT
Stainless steel	Solvent free	Polypyrrole/functionalized carbon powders
Carbon steel	Epoxy	Polypyrrole functionalized zinc oxide and zinc phosphate
Porous stainless steel	Solvent free	Polypyrrole
Stainless steel	Sulfonated melamine formaldehyde	Polypyrrole
Aluminium	Solvent free	Polypyrrole
Magnesium alloy	Epoxy	Polyaniline@MIL-101
Carbon steel	Epoxy	2-Hydroxyphosphonocarboxylic acid doped polyaniline
Aluminium alloy	Solvent free	Ag/polyaniline
Magnesium alloy	Solvent free	Polypyrrole/V O

6.3. Photocatalytic applications

Among photocatalysts, TiO 2 is preferred because of its novel bandgap, easy synthesis, cheapness, high photo-activity, resistance to photocorrosion and high oxidizing power. Generally, TiO 2 exhibits three different phases: anatase, rutile, and brookite. Among the three phases, anatase has good photochemical behavior due to its high bandgap of 3.2 eV. Titanium dioxide can be easily prepared hydrothermally or by a sol–gel approach. Polyaniline with organic semiconductors is a great research prospect because it has good electron–hole charge separation, a good absorption coefficient of visible spectra, a high mobility of charge carriers, and low-cost and easy synthesis. The process behind dye degradation includes incidence of light on the photocatalyst, photo-induced holes, the accumulation of electrons on the semiconductor surface, initiation of a redox reaction, and degradation of the reaction product. Reddy and his coworkers synthesized a TiO 2 /polyaniline hybrid system by an in situ polymerization technique. They studied the photocatalytic activity of the composite for the degradation of rhodamine, acetic acid, and methylene blue. Under continuous 3 h UV irradiation, RhB was degraded by 80%, and methylene blue and phenol were degraded by 67% and 51%, respectively, in 200 min of irradiation time. The photocatalyst still gives good activity after 3 cycles of irradiation. It is clear that the catalyst has a reusable property. In the photocatalytic mechanism of TiO 2 /PANI studied by ESR spin trapping experiments, under UV irradiation, the main oxidative species are superoxide anion radicals, O 2 ˙ − , hydroxyl radicals, (˙OH) and holes (h + ). When polyaniline is exposed to UV irradiation, a π–π* transition happens. This means that photogenerated electrons become excited to the π* orbital of polyaniline. Which has the same energy as the conduction band of titania, resulting in chemical bonding. This helps in the transfer of a photogenerated electron from polyaniline to TiO 2 . These absorbed electrons migrate to the surface of the photocatalyst and react with water and oxygen to produce hydroxyl and superoxide anion radicals, which cause oxidation of the contaminants. Similarly, photogenerated holes migrate from the valance band of TiO 2 to the high energy state of polyaniline, because the VB of TiO 2 and the CB of polyaniline have the same energy level. And these photogenerated holes migrate to the surface of the photocatalyst, and oxidation of contaminants occurs 201–205 ( Fig. 15 ).

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Heavy metals like Zn, Pb, Hg, Cd, Cr, Ni, Co, Fe, etc. are harmful to the environment. These heavy metals are expelled as industrial waste and they dangerously affect the aquatic ecosystem. The US Environmental Protection Agency, Agency for Toxic Substances and Disease Registry listed chromium as a potentially toxic element. 206 Chromium has a high amount of toxicity, which affects human life severely causing eczema, and lung, nasal, and sinus cancers, etc. Chromium exists in different valance states from −2 to +6. Among these, chromium[ iii ] and chromium[ vi ] are too dangerous due to their environmental stability. 207 There are a lot of biological techniques used for the removal of chromium traces like bioremediation using bacteria, 208 fungi 209 and algae, and phytoremediation. By comparing these studies, physiochemical treatments like photocatalysis, adsorption, 210 membrane separation 211 and ion exchange 212 can be used as effective methods for the removal of traces of chromium. A mesoporous titanium polyaniline nanocomposite can remove chromium ions. The mesoporous TiO 2 can react with atoms, molecules and nanoparticles not only on the surface but also throughout the bulk. Deng et al. tried to point out the photocatalytic activity of the MT/PANI hybrid system for the successive removal of chromium ions. Here they synthesized a hybrid with different concentrations of polyaniline. The hybrid system is twice as active as pristine MT, and 3% MT/PANI adsorbed 100% of chromium[ vi ] ions after 10 cycles. It is evident that the composite has reusability. But MT and other concentrations of polyaniline had reduced activity after 10 cycles of reaction. This ideal efficiency is due to the adsorption behavior of the protonated amino group present in the polyaniline. 202 The mechanism behind the photocatalytic activity of the polyaniline graphene composite has been beautifully described. When visible light is irradiated on the composite, the photogenerated electrons in the conduction band of polyaniline migrate towards the Fermi level of graphene. This is because the energy of both the CB of polyaniline and the Fermi level of graphene is almost the same. Then the migrated electrons on the surface of graphene react with the dissolved oxygen to form superoxide radical ions. These react with water to form H 2 O 2 . H 2 O 2 reacts with the photogenerated electrons on the surface of graphene and photogenerated holes in the CB of polyaniline. The generated ˙OH is responsible for dye degradation. When the dye is exposed to UV irradiation, it is converted to dye*. In the case of MB, the photogenerated electron in the LUMO migrates to the VB of polyaniline. Then the photogenerated holes in the dye react in the presence of water to form ˙OH, which degrades the MG dye. In the case of RhB* and CR*, electrons can be injected into the CB of polyaniline via electron transfer and these electrons, in turn, flow downhill to RGO, and are scavenged by the O 2 on the surface of the catalyst to form superoxide radical anions. 204

For RhB and CR

˙OH + ˙O 2 − + dye + → colorless degraded product

Polyphenylene is widely used as a photocatalyst due to its high chemical and thermal stability. Gu and his team reported catalytic behavior in a Pd/polyphenylene composite synthesized by a palladium catalyzed Suzuki reaction. They observed that polyphenylene has a high light harvesting property along with energy transfer through its conjugated backbone. The reduced size effect of palladium causes a better catalytic reaction. From the UV-vis absorption data it is clear that the catalyst has better light absorption and the composite has higher conversion efficiency in the transition of p -NPh to p -APh. The Pd/polyphenylene catalyst shows better reusability after a series of reaction cycles. The light energy harvesting of polyphenylene causes the migration of electrons towards the palladium surface, resulting in a high electron density over the palladium surface. It also causes better hydrogen activation and thereby better photocatalytic activity ( Fig. 16[A] ). 213

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A chemically prepared polyaniline/CdO nanocomposite has an excellent dye degradation ability under both UV and sunlight irradiation. Electron densities and bond energy on the surface of the polyaniline while making a composite with CdO enhance the dye decoloration up to 7 times more than pristine polyaniline. The mechanism behind the degradation of methylene blue and malachite green has been emphasized. Both these dyes are extensively used industrially and biologically as well as chemically. These highly toxic dyes have been degraded using semiconducting materials like ZnO and TiO 2 . CdO has a high direct bandgap of 2.3 eV and an indirect bandgap of 1.8 eV. Therefore, it is a great research prospect in the field of optoelectronics, such as solar cells, phototransistors, photodiodes, transparent electrodes, catalysts, and gas sensors. In this study they examined the decolorization of dye by using polyaniline, CdO and polyaniline/CdO nanoparticles in the presence of natural sunlight as well as under UV irradiation. From the data it is clear that CdO concentration should be an optimum to obtain high efficiency of dye degradation. The kinetics of degradation are well described by the apparent first-order rate equation ln( C 0 / C t ) = κ . A polyaniline/CdO composite has a higher κ value. The catalyst degrades 99%, and 98% of MB and MG dyes, respectively, in the first cycle of reaction. The catalyst has high reusability because it shows an efficiency of 82% and 97% after the fifth cycle 205 ( Fig. 17 ).

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The photocatalytic behavior of the g-C 3 N 4 /TiO 2 @PANI composite was investigated. The composite has better photocatalytic activity against Congo red toxic dye due to the better electron–hole pair separation and reduced band gap of the composite. This was observed from UV-Vis analysis, PL and band gap analysis ( Fig. 16[B] ). The composite shows almost 100% photocatalytic activity towards Congo red molecules at some particular concentrations. The composite does not show active photocatalytic behavior beyond a particular concertation of Congo red due to the lack of optical density and a deficiency of active radicals to activate photocatalysis. 214 The photocatalytic activity of polypyrrole with TiO 2 nanoparticles for the degradation of organic dyes has also been studied. The energy level between the VB and the CB is denoted as the bandgap E g . Materials get excited only when the energy of an incident photon is equal to or higher than the E g . The electrons absorb energy from the photons, and they are excited to the CB from the VB. But in the case of TiO 2 , it has a wide energy gap. Due to this, the excitation in sunlight is limited and excitation shows best under UV irradiation. When making a composite with conjugative polymers, the bandgap is reduced compared to pristine TiO 2 . This is why a polymer TiO 2 composite absorbs more photons, and the degradation of dyes is enhanced. The photocatalytic mechanism is almost the same here as in the case of polyaniline. Under sunlight irradiation the electrons in Ppy/TiO 2 are excited from the highest energy state of polypyrrole into the lowest energy level. Then they will migrate into the CB of TiO 2 . The holes in the polypyrrole are left as such in the HOMO. The electrons in the VB of TiO 2 move to the HOMO of polypyrrole and holes are left in the VB of TiO 2 , so the recombination of electrons–holes occurs. This means a huge amount of electron–hole generation takes place in the surface of the TiO 2 . These photogenerated holes and electron react in the presence of oxygen and water to form photoinduced anions like O 2− and OH − . These two photoanions are responsible for dye degradation. Here in this study Wang and co-workers investigated the performance of the polypyrrole/TiO 2 in a (1 : 100) molar ratio. The first-order rate equation was used to determine the rate of degradation. From the data, it is clear that polypyrrole/TiO 2 (1 : 100) has a higher κ value. 203

The electronic property of a conducting polymer is easily tunable when a composite is made with metallic semiconductors. Pristine conducting polymers have problems with the high rate of electron–hole pair recombination, so it is mandatory to modulate this property to enhance photocatalytic activity. g-C 3 N 4 has a moderate band gap energy, so it is easily excited under sunlight. Polyaniline has an outstanding electron-donating tendency and is an excellent hole acceptor. A hybrid of polyaniline and g-C 3 N 4 has a decreased rate of electron–hole recombination and a unique production of photocatalysts so that the above composite is extensively using in the photocatalytic degradation of organic dyes. The above composite has been investigated for the degradation of methylene blue. 92.8% degradation and a high cycle life of the catalyst have been observed. Alenizi et al. have synthesized a novel ternary g-C 3 N 4 /TiO 2 @polyaniline composite and investigated the degradation of Congo red dye under sunlight. The deterioration of Congo red was studied previously by using WO 3 –TiO 2 /activated carbon, alginate/Fe 2 O 3 /CdS and TiO 2 -SWNT-P-21 composites, but the efficiency of degradation was not more than 85%. But here in this study, Congo red dye was decolorized by 100% in 3 h of reaction under sunlight. The composite has a higher rate of reusability after the fourth cycle with an efficiency of 90.1%. The mechanism behind this composite was the same as before. When it was exposed to sunlight, electrons were separated from the composite, migrated from the CB of TiO 2 to the valence band of g-C 3 N 4 , and recombination with holes occurred. Generated holes migrate towards the surface of the polyaniline and the electrons left in the conduction band of g-C 3 N 4 react in the presence of oxygen, H 2 O and OH − to form photoanions. These photo-induced products drive the photocatalytic reaction. The exciting factor behind this composite is its higher efficiency compared to its pristine form or a binary composite of the above materials. 214

A summary of studies on the use of conjugated polymers in photocatalytic applications is given in Table 3 .

Polymer	Light source	Pollutant	Efficiency
Polyaniline/TiO	UV irradiation	Bisphenol-A	99.7% in 80 min
PPy–TiO	Xe lamp (vis)	Methyl orange	100% in 60 min
BiVO /Ag PO /PANI	Visible light illumination	CIP	85.92% in 60 min
PPy–ZnIn S	Iodine gallium lamp		100% in 60 min
CuO/TiO /PANI	Visible light illumination	Chlorpyrifos	95% in 90 min
BiOBr–Ag–PPy	Halogen lamp (vis)	Malachite green	97% in 120 min
PANI/PbS QD	Visible light illumination	Rhodamine 6G	87% in 50 min
Polythiophene/Bi O I	Visible light illumination	Bisphenol A	98.6% in 20 min
Polypyrrole/halloysite nanotubes/Fe O /Ag/Co	Visible light illumination	Methylene blue	91% in 120 min
Polythiophene/ZnO	Mercury lamp	(MB) dye and gemifloxacin mesylate (GFM) antibiotic	95% of MB dye 80% GFM in 180 min
ZnFe O Ag/PEDOT	Sunlight irradiation	Tetracycline	71.77%
Polythiophene/MnO	Visible light irradiation	MG dye and mixture of MG dye and trichlorophenol	98% for MG dye and 97% in 80 min

6.4. Biomedical and antimicrobial application

Near-infrared (NIR) photothermal treatment (PTT) is a promising approach for ablating cancer cells in the human body. An NIR laser is used to illuminate the targeted area using fiber optics. Ablation of cancer cells is done by the use of a photothermal material with minimal invasiveness compared to other treatment methods like chemotherapy or radiotherapy. One of the main advantages of PTT over other treatments is its targeted action. Due to this property, this treatment protocol minimizes the loss of tissues near the active site. Materials with nanoscale dimension, good NIR absorption, a high amount of photostability, and less photocorrosion and low cytotoxicity show great prospects as photothermal materials for PTT. The metal nanoparticles tend to show surface plasmon resonance when illuminated with IR radiation and, after excellent illumination, the photostability of most metal nanoparticles is lost. Conducting polymers like polyaniline, polypyrrole, PDOT ( Fig. 18 ) etc. have outstanding capability for absorbing IR, and they have notably less cytotoxicity. That is why these polymers are widely used for both in vivo and in vitro cell studies. Mei Chen et al. studied the possibility of polypyrrole as a photothermal material for the control of the growth of the 4TI tumor model. In this study, they investigated it experimentally by in vivo and in vitro analysis, and they observed that polypyrrole has a photothermal efficiency of 44.7% and has an excellent cancer cell ablation property under NIR irradiation of 1 W cm −2 . The tumor size was measured in consecutive intervals, and it was observed that all irradiated tumors disappeared, and no tumor growth was noted after a course of 60 days. The NIR photothermal treatment of F127 modified polyaniline was also studied. The composite was synthesized by a two-step hydrothermal method followed by colloidal dispersion of the composite by sonication. 226

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Synthesized polyaniline composites have a potential future in photothermal treatment due to their high amount of strong NIR absorption, optimum size, good water dispersion, and high photothermal efficiency of 48.5%. The critical feature of zero toxicity is useful in in vivo investigations. 227 Carbonaceous materials like graphene, graphene oxide, and reduced graphene oxide have a potential role in PTT because of their suitable NIR absorption, high surface area, and efficient thermal conversion, but their application has been limited because of their low dispersity. Recently magnetic iron oxides have also been used in various biomedical applications like targeted drug delivery, bioimaging, and even for cancer treatments. Soysal et al. investigated the synergetic behavior of an S-rGO–Fe 3 O 4 –polyaniline composite, and they observed that the composite has good photothermal as well as targeted drug delivery and bioimaging behavior. The composite irradiated at 808 nm has an excellent photoconversion efficiency of 86.3% and the composite with the least aqueous concentration has low cytotoxicity. It also shows an excellent bioimaging property ( Fig. 19[A] ). 228

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Polypyrrole has high photothermal activity towards cancer cells. Chen and his coworkers investigated the photothermal efficiency of polypyrrole towards 4T1 cancer cells without any surface modification. The biocompatibility of polypyrrole paves a way for both in vivo and in vitro analysis. From investigation they observed that polypyrrole has 44.7% photothermal conversion efficiency and it has a high ablation efficiency due to its high NIR absorption 226 ( Fig. 19[B] ).

Cytosensors are used to analyze and evaluate cells by using electrochemical parameters like current, impedance, and capacitance. Cell activity concentration and other mechanisms like the proliferation of cells are adequately assessed by electrochemical sensors. Generally, zero-cytotoxic metal and magnetic and photochromic nanoparticles are applied for the investigation of cell studies beyond conducting polymers. Due to their high conductivity, electrochemical stability and response, conducting polymers have excellent potential as bio-electrochemical sensors. Cancerous HeLa cells impregnated with GCE/PANI-NF/AuNP/GSH/FA–BSA systems were investigated. Here the sensing action for HeLa cells by the composite is discovered in the changing impedance data. The HeLa impregnated composite restricts the flow of current from the composite to the electrolyte; hence an overall change in the EIS data is noted. From the impedance data, the potential of composites with and without HeLa cells was studied by the difference in the R ct value. The impregnated composite has the lowest value of R ct and has good composite resistance while the HeLa impregnated composite has a high R ct value due to hindrance of the current flow to the electrolyte ( Fig. 20 ). 229

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Conducting polymer fabrics show antimicrobial activity, so they have potential applications in biomedical as well as in different smart materials. They can increase the H 2 O 2 level, which encourages the production of hydroxyl radicals which leads to antimicrobial action. Phytic acid doped polyaniline coated fabric has been studied in which phytic acid provides better crosslinking between polyaniline and the substrate. The antimicrobial action depends on the electrostatic attraction between the polymer backbone and the microbes. The conductivity changes with different values of pH: pH ≥3 gives better conductivity. The antibacterial activity of polyaniline coated cotton and polyester fabric against Gram-positive Staphylococcus aureus ( S. aureus ) and Gram-negative Escherichia coli ( E. coli ) and Klebsiella pneumonia ( K. pneumonia ) incubated for 18 hours at 37 °C was investigated in Mueller–Hinton agar (MHA). The investigation reveals that polyaniline coated polyester shows a better inhibition zone of 10.3 ± 0.04714, and cotton fabric shows no inhibition zone in the case of Escherichia coli ( E. coli ) or Klebsiella pneumonia ( K. pneumonia ). 230

Conducting polymers are extensively used as an antimicrobial and antifungal agents in various fields like the food industry, the medical field, coating industry, etc. Polyaniline and other conducting polymers have an antimicrobial property against Escherichia coli , Staphylococcus aureus , Pseudomonas aeruginosa , Enterococcus faecalis , and Campylobacter jejuni . An Au@PANI–IA–Fe 3 O 4 composite has been studied against Staphylococcus aureus (Gram +ve) and Escherichia coli (Gram −ve) microbes in Mueller–Hinton agar (MHA) plates. It was observed that the composite shows a better zone of inhibition with increasing composite concentration against Staphylococcus aureus while the composite shows an insignificant inhibition zone for E. coli microbes. The antifungal property of the composite has been studied against Candida albicans . The result shows that the composite follows a trend of increased inhibition zone when the composite concentration is increased. 231 The polyaniline NF/Ag nanoparticles have a synergetic effect against microbial action. The antimicrobial mechanism behind the Ag nanoparticles is partially known. The concentration of silver nanoparticles plays a crucial role in the case of Gram-negative microorganisms. The positively charged silver accumulates on the cell periphery, and this permeable particle causes the death of the microorganism. Selcuk Poyraz showed that PANI NF/Ag nanoparticles have more effective inhibition for Gram-negative E. coli than for Gram-positive S. aureus due to the difference in their peptidoglycan layouts because of the synergetic effect of Ag and polyaniline. 232

A summary of studies on the use of conjugated polymers in biomedical applications is given in Table 4 .

Polymer	Application	Type	Analyte
Polyaniline-supported Cu–CuO, core–shell	Sensing	Electrochemical	Glucose
Polypyrrole/CuS@SiO		Voltametric	Glucose
Au@rGO/polyaniline		Electrochemical	Furazolidone and flutamide

Polymer	Application	Type
Polycaprolactone–Polyaniline	Scaffolds	Bone tissue scaffold
Polypyrrole		Muscle tissue scaffolds
PVA/PEDOT		Nerve tissue scaffolds

Polymer	Application	Irradiation	Temperature reached and cell line
PLNP@PANI-GCS	Photothermal therapy	808 nm 1.5 W cm 5 min	52.2 °C and MRSA
DOX–PPy@PNAs nanogel		808 nm 0.5 W cm 5 min	47.9 °C and H22 tumor
Polypyrrole–rhodamine B		808 nm 0.26 W cm 10 min	53 °C and HepG2 cells
S-rGO–Fe O –PANI		808 nm 2 W cm 10 min	80 °C

6.5. Electrochemical gas sensors

The oldest version of an electrochemical sensor, during the 1950s, was useful for oxygen monitoring. Currently, well-designed electrochemical sensors have been successfully developed for the monitoring of combustible and toxic gases in space-related applications. Miniature forms of highly selective electrochemical sensors moved into the limelight with their ability to detect toxic gases in the PEL range. The appearances of various electrochemical sensors for gas sensing may be similar, but these sensors exhibit markedly different functions. Besides, the sensors show various performances attributed to their specificity, response time, sensitivity, and operational life. For example, a highly sensitive gas sensor with low concentration uses a hydrophobic porous membrane, and better sensitivity through sufficient signal production is possible due to less restricted capillary movement to allow the passage of more gaseous molecules. On the other hand, this design permits the escape of electrolyte water molecules to the outer environment. Besides, a highly sensitive electrochemical sensor should have a comparatively low operating life because of the evaporation of water molecules through the porous membrane. The selectivity of an electrochemical sensor for gas detection is based on sensor type, target gas, and the gas concentration the sensor has been developed to detect. Similarly, the chemical reactivity of a specific target gas depends on the composition of electrolyte and electrode material for the sensing process. Additionally, specific electrochemical sensors utilize electrical power to produce a response towards the target gas. 242 The working of electrochemical sensors is based on the reaction with the target gas and generates an electrical signal proportional to the concentration of target gas. An electrochemical sensor is comprised of a working (sensing) electrode and a counter electrode separated by a thin electrolyte layer. Firstly, the gas passes through a tiny capillary kind of opening, followed by diffusion across a hydrophobic barrier and finally enters the electrode surface. This approach is explored to allow more gas molecules to reach the sensor to generate a better electrical signal while restricting the leakage of electrolyte out of the sensor electrode. The gas diffused across the barrier undergoes either an oxidation or a reduction mechanism on the surface of the sensor electrode. The current proportional to the concentration of gas molecules that flows between the anode and the cathode in an electrochemical cell is measured. This electrochemical sensor is usually described as a micro fuel cell or an amperometric gas sensor due to the current generated in this process.

In an electrochemical sensor, the potential at the sensing electrode is not constant due to the continuous electrochemical reaction on the surface of the sensor electrode. Hence it results in a decrease in the performance of electrode as time goes on. So, a reference electrode is used to improve the performance of the sensing electrode. A stable fixed potential is applied to the sensing electrode, and the reference electrode needs to maintain the value of the fixed potential at the sensing electrode without any current flow to or from the reference electrode. The value of fixed potential applied at the sensing electrode determines the specificity of the sensor to a target gas.

6.5.1. Major components

Electrode: the electrode material is crucial for an electrochemical cell reaction. It is a catalytic material for performing the half-cell reaction over extended periods of time. The electrode is usually made of a material such as platinum or gold and is catalytically accelerated for an effective reaction with the target gas molecules. Three electrodes in an electrochemical cell can be composed of different materials according to the overall design of the electrochemical sensor. Electrolyte: this should be compatible with the electrode materials used in the sensor and allows an efficient transfer of ionic charges between the electrodes in order to promote the cell reaction. The signal deterioration will be faster if the electrolyte material evaporates too fast. Gas permeable membrane: This is used to protect the catalyst (sensing) electrode and to control the gas concentration entering at the electrode surface. These barriers are made of thin and low-porosity Teflon membranes, so the sensors are known as membrane clad sensors. In addition, there are sensing electrodes protected with highly-porous Teflon membranes, and the gas flow is controlled by a capillary movement. These sensors are known as capillary-type sensors. In some instances, the membranes are known to function as filters for removing undesirable particulates. The pore size of membranes should permit enough gas molecules to reach the sensing electrode and inhibit the leakage or evaporation of liquid electrolyte to the outer environment. Filter: filters have a different degrees of effectiveness. For example, a scrubber filter is used in front of the sensor to filter out undesirable gases. The most common charcoal filter is shown in the figure, which is used to filter out most gases except hydrogen and carbon monoxide. The proper selection of a suitable filter medium allows an electrochemical sensor to be more selective towards its target gases.

The proper working of the sensor is based on an adequate supply of oxygen molecules for the completion of the reaction; otherwise, a shortage of oxygen supply will shorten the lifespan of the sensors. It is essential to maintain the sensor at the same pressure; otherwise, changes in pressure may damage the electrochemical sensor. Electrochemical sensors are quite sensitive to temperature. If the temperature is above 25 °C, the sensitivity will be higher. If it is below 250 °C, the sensitivity will be lower. TMDs can be widely used in switching applications attributed to their intrinsic bandgap. Changes in TMD layers can be used for tuning of the bandgap between 1 and 2.05 eV due to quantum confinement. TMD materials with prominent mechanical, electrical, and chemical properties were also widely used for sensing applications. A single transition metal layer is comprised of an atomic plane sandwiched between the two atomic planes of chalcogenide atoms. Whereas in the multilayer form, layers are connected to each other by van der Waals forces. The transition metal atom is covalently attached to the chalcogenide atom. With a large interlayer surface area available for chemical adsorption, there is a notable improvement in electrical signals as it is able to detect the presence of chemical molecules even in low concentrations. TMDs like MoS 2 , MoSe 2 , VS 2 , WS 2 , WSe 2 , etc. are leading candidates in emerging gas sensing technologies due to their flexibility, transparency, and efficient gas adsorption. The main disadvantage of metal oxide and inorganic material gas sensors is their high operational temperature. A high operational temperature affects the durability of the sensors, which will be damaged within a short time. Conducting polymer-based sensors were a big breakthrough because of their fast response time, recovery time, and their low operational temperature. This allows us to work at room temperature, leading to a long lifespan. 243

6.5.2. Sensing mechanism

Charge transfer processes constitute the basis for gas sensing in graphene and similar 2D layered inorganic analogues, in which sensing materials function as either charge donor or acceptor. The exposure of the sensor material to different gases can generate a charge transfer between the adsorbed gas molecules and the sensing materials. This charge transfer involves different directions of transfer and charge quantities, which can change the resistance of the material. If the sensing material is re-exposed to gases, the resistance will return to its initial value and thereby lead to the desorption of gas molecules from the surface of the sensing material. 243 The charge transfer mechanism between the conducting polymers and adsorbed gas molecules, such as NO 2 , O 2 , NH 3 , NO, H 2 O, or CO, has been investigated. As stated before, conducting polymers behave like an insulator or semiconductor in their pristine form but when doped with suitable materials, their conductivity changes to metallic. The backbone of conjugated polymers is constructed from conjugate bonds, consisting of both σ and π bonds. The σ bonds are responsible for the mechanical property of the polymers. Alternating π bonds and their delocalization and overlap with neighboring bonds form the electrical property. 244 When the conjugated polymer is doped, it will generate charge carriers like polarons/bipolarons/solitons, etc. These charge carriers are delocalized along the chain to induce charge transport along the polymer backbone. On the other hand, interchain transport occurs by hopping or by charge tunneling. In the case of a p-type sensing material, an optimum amount of oxygen gets chemisorbed on the material surface, and this absorbed oxygen gets changed to single or double oxygen ions and is ionosorbed on the surface. The addition of oxygen molecules onto the substrate causes the removal of an electron from the sample surface. This causes an increase in hole density on the surface and causes a decrease in resistance. When reducing gases react with ionosorbed species, electrons are pumped into the conduction band of a p-type material. Hence, hole concentration decreases and causes an increase in the resistance. If oxidizing gases come into contact with ionosorbed species, this causes the depletion and removal of an electron from the valance band whereby hole density increases due to recombination, finally resulting in decrease in resistance. The working mechanism is the opposite in the case of n type materials. The dopant type classifies conducting polymers into p type or n type polymers ( Table 5 ).

Sensing response	P type polymer sensor holes (h )	N type polymer sensor electrons (e )	Examples of analytes
Reducing analytes	Resistance increases	Resistance decreases	CO, NH , CH , H , H S, acetone, ethanol
Oxidizing analytes	Resistance decreases	Resistance increases	NO , CO , SO , O , O

Among conducting polymers, polyaniline has been effectively utilized in the sensing field because of its easy synthesis, doping and de-doping behavior, ease of deposition on substrates and reactivity towards gases. Doping will elevate the conductivity range with high reversibility; which is why it is widely using for the sensing of toxic gases like CO, NO 2 , etc. The secondary components in a conducting polymer composite can be metallic, bimetallic, transition metal chalcogenides, carbonaceous materials, polymers, etc. These secondary nanoparticles are stabilized with a polymer matrix by a weak coulombic force or by van der Waals force. The introduction of secondary particles modifies the physical and chemical properties of the conducting polymers and this tendency has been utilized for various applications. Kumar et al. studied the sensing activity of PANI/Au NS as an NH 3 gas sensor, and they observed that Au NS act as a catalyst and the composite gives a better response time of 15 s, which is quicker than that of pure Au NS. The sensing response increases by 52% when a composite is made with polyaniline. 245 The use of graphene is limited in digital circuits on flexible and wearable sensing devices due to the absence of a bandgap. Thus, the semiconducting properties of pristine graphene remain a hindrance for gas sensing applications. The semiconducting properties of sensing materials are a crucial factor for tuning the sensing characteristics of a gas sensor. A composite with a conducting polymer overcomes the above limitations of polyaniline. Wu et al. fabricated a graphene/polyaniline sensor for the detection of NH 3 gas at different concentrations. From their studies, they observed that the sensor acts with conductometric behavior and the resistance of the sensor increases when exposed to analyte gas. The sensor retaliation value varies with analyte concentration. The composite shows sensor responses of 3.65 and 11.33% at concentrations of 20 and 100 ppm of NH 3 analyte. The response time and recovery time of the composite at 100 ppm concentration were noted to have values of 50 s and 23 s. 246 Hydrogen gas is colorless, odorless, and tasteless, and shows explosive behavior above a critical concentration range. Hydrogen gas is used as a fuel in various industries. Due to its high permeability, it can cause explosions. The precise monitoring of hydrogen gas is critical due to the above problems. An exact and precise sensing mechanism is needed for the detection of hydrogen gas leakages. Polyaniline based sensors are used for the detection of hydrogen gas effectively and precisely. Sharma et al. developed Al-SnO 2 /PANI nanofibers via an electrospinning technique, and their sensing activity was studied thoroughly. A 1% Al-SnO 2 /PANI sensor shows a high sensitivity range of ∼275% to H 2 gas at 1000 ppm. The sensor has a rapid sensing and recovery time of 2 s at a concentration range of 1000 ppm at 40 °C. 247 Wang et al. fabricated a polypyrrole/Fe 2 O 3 nanocomposite for the detection of NO 2 gas. Fe 2 O 3 present in the composite enhances the response due to the p–n heterojunction. This sensor shows precise sensing activity even at a lower concentration of 0.1 ppm and the sensor shows a linear response in a concentration range of 0.1–10 ppm. The composite shows a good response of 220.7%, which is higher than in previous available reports. 248 Kwon et al. developed a PEDOT:PSS/PVP composite by an electrospinning technology. The sensor was effectively used for the detection of various vapors like ethanol, methanol, tetrahydrofuran (THF), and acetone. The sensor has improved sensing actions like excellent reversibility, reproducibility, response, and recovery time. The composite maintains almost the same response and recovery time with different cycles but the sensor resistance decreases when exposed to polar protonic solvents. 249

6.6. Conducting polymer hydrogels (CPH) for bioelectronics

Conducting polymer hydrogels are a combination of conducting polymer and hydrogels in order to achieve some novel properties that are not available for conventional materials. The conducting polymer hydrogels consist of conducting polymers like polypyrrole, polyaniline, or polythiophene crosslinked covalently or physically with hydrophilic networks. 250,251 The hydrogel morphology is easily tunable and it has different applications, including sensing, bioelectronics, OECT, tissue engineering and energy storage applications. 252–254 The main advantages of hydrogels are their tunable chemical and physical properties when subjected to doping engineering. In the case of polypyrrole hydrogels, their morphology varies from nanofibres to 3D porous structures in accordance with the doping and nature of the dopant. CPH has high mechanical, electrical, self-healing and biocompatibility properties. 255 They are widely applied in bioelectronics and tissue engineering. Conducting polymers alone are not sufficient for certain applications due to their lack of long-term stability. Some research groups have proposed the use of conducting hydrogels instead of conducting polymers to achieve long-term stability. CPH is fabricated using different techniques like free radicals, click chemistry, condensation and Michael-type addition polymerization. The chemical techniques are studied widely for biomedical applications.

The invention of bioelectricity led to research into understanding the communication between biology and electronics. The electronic response of the nervous system enables the muscular movements, memory and reasoning ability of humans. Generally, bioelectronic interfaces are electrodes which interact with biological tissues. They collect bioelectronic signals and enable personalized self-monitoring of tissues. 256,257 Bioelectronics are widely used in various applications, including electronic skin, the detection of brain activity, soft robotics and wearable and flexible implantable devices. 258 Before the invention of CPH, inorganic materials were widely used for the fabrication of bioelectronic devices. Its replacement is proposed due to its unreliability in signal collection, cytotoxicity and inflammatory response by the body. Bioelectronic devices need to maintain high conductivity and high mechanical properties in accordance with the movement of human body parts, which is very difficult. Transistors like organic electrochemical transistors (OECTs) 259 and electrolyte-gated organic field effect transistors are generally used for bioelectronic sensing. OECTs have aroused great research and industrial interest due to their high transconductance, biocompatibility and processability. 260 An OECT is constructed from a semiconductor/organic film in contact with two electrodes, a drain and a source, an electrode (gate) immersed in a electrolyte. The organic film enables the movement of charge and ions from source to drain. The channels of the OECT are fabricated using PEDOT:PSS, a polypyrrole polymer doped with p-type dopants. 261

Bioelectronic devices are the basic unit for the fabrication of wearable/implantation devices for tissue response monitoring. Conducting polymer hydrogels are used to fabricate pressure and strain sensors due to their ability to decode mechanical signals to electrical signals. Flexible electrodes made up of conducting polymer hydrogels are widely used to monitor electrophysiological signals, including ECG, 262 electromyography and electroencephalography signals. 263 Generally, electrophysiological signals are very weak. The main challenge for device fabrication is to enhance the conductivity and signal-to-noise ratio. Skin adhesion, long-term stability and biocompatibility are also taken into consideration. PAA/PEDOT hydrogels have been designed to detect different electrophysiological signals. Polyaniline based hydrogels are used for real-time glucose and lactate monitoring. 264 OECT is widely used for monitoring electrophysiological signals, including ECG, electromyography, and electroencephalography.

The conductivity of hydrogels can be increased by adding conductive fillers. The conductivity of a polyaniline/phytic acid hydrogel was recorded as 0.21 S cm −1 . After the incorporation of MWCNT, the conductivity increased to 1.54 S cm −1 . 265 Similarly, an enhancement in the specific capacitance of various conducting polymer hydrogels was noted with the introduction of foreign conductive fillers. If the filler loading is beyond a particular amount, the hydrogels show a phase separation between polymer matrix and filler, causing low mechanical stretchability. So, it is very difficult to balance the mechanical stretchability and conductivity. There have been a lot of efforts to maintain stretchability without losing conductivity. The stretchability of a conducting PEDOT:PSS polymer was enhanced by 35% by structural modification in the interconnected fibrillar structure through solvent annealing. The stretchability was also improved by the introduction of plasticizers into the polymer matrix. The conductivity is same with respect to pristine form even after application of a 100% strain condition. 266

7. Conclusion and future directions

To date, there have been a lot of studies done on the fabrication of conducting polymers. The main aim of this review article has been to explore current trends in the synthesis, properties, and applications of conducting polymers. Conducting polymers and their composites are always in the limelight because of their metallic conductivity when doped and excellent physical properties. From literature reviews, it was observed that conducting polymers in their pristine form behave as an insulator or a semiconductor. They show metallic conductivity only when doped with a suitable dopant or when made into a composite with foreign materials. The physical and chemical properties of conducting polymers also depend on morphology; different morphology gives distinguishable properties. Understanding the basic properties is essential for the design of conducting polymers for various applications. The complex structure of conducting polymers and their derivatives poses a difficulty for theoretical modelling; therefore, an understanding of the origin of conductivity and the doping mechanism is essential. Charge carriers are developed on a polymer backbone either when added to or extracted from the delocalized π bond. Various parameters like temperature, dopants, and structural properties have an effect on transport properties.

Conducting polymers are widely used as supercapacitor electrode materials because of their metallic conductivity, flexibility, processability, and ease of fabrication. Most conducting polymers exhibit high specific capacitance, and they deliver energy rapidly. The main disadvantage of conducting polymer-based supercapacitors is their cycle life; symmetric conducting polymer supercapacitors have a lower cycle life than carbonaceous material-based supercapacitors. From the literature, we can observe that the cycle life problem can be overcome by irradiation, sonication during synthesis or compositing with carbonaceous or non-carbonaceous materials. In the case of an asymmetric configuration, conducting polymers and their derivatives as positive electrodes and carbonaceous material as negative electrodes provide a higher cycle life and specific capacitance. From the literature, we can find that stability and cycle life can be improved by incorporating metal oxides, transition metals, transition metal dichalcogenides, and carbonaceous materials. From these studies, we can understand that future developments and research should be carried out into a hybrid conducting polymer composite that will prove effective in achieving better supercapacitor performance.

Due to the environmental and health issues of chromate conversion coatings, researchers have put effort into finding an alternative. Conducting polymers have been widely used for corrosion inhibition of metals and their alloys during the last few decades. They are also used as pigments for organic coatings. Also, multilayers of conducting polymers and their composites act as corrosion inhibitors. The dopants incorporated into the polymer backbone release necessary inhibitors during reduction. Conducting polymer films electrochemically synthesized in the presence of suitable electrolytes act as efficient inhibitors against corrosion, and the film thickness can be modified by controlling the electrochemical parameters. Organic coatings like epoxy, acrylic, polyurethane, etc. added to the conducting polymers improve their corrosion inhibition property. Morphology plays a vital role in corrosion inhibition. The controlled release of inhibitors upon reduction is the main advantage of using polymer coatings. Also, they generate a metal oxide layer beneath the topcoat in aggressive environments, and these metal oxide layers prevent corrosion effectively and efficiently. From an analysis of recent papers, future developments should focus on conducting polymer incorporated organic coatings for better corrosion inhibition activity. The durability of coatings increases with compositing with organic coatings.

The performance of conducting polymer-based photocatalysts depends upon the rate of photoelectron transfer to the CB of particles incorporated on the polymer backbone like metal oxide, TiO 2 , etc. In the literature, it is shown that high photocatalytic activity is achieved only when electron–hole combination is minimized. From a literature review, it is observed that the performance of conducting polymer sensitized TiO 2 photocatalysts depends upon a lot of factors like structural arrangements. The covalent bond enhances electron coupling, and excited electrons in the conducting polymer can be injected to the CB of TiO 2 . Until now, reports have not been available on conducting polymer composite based photocatalysts, so future development should focus on different composites of conducting polymers.

Conducting polymers are new and promising materials in the field of biomedical engineering but have not been wholly explored until now. There are some limitations to conducting polymers for biomedical applications due to their cytotoxic nature and differences in in vivo and in vitro studies. Generally, physical properties and biocompatibility issues are the main problems for conducting polymers. Most of the biocompatibility issues of conducting polymers can be overcome by compositing with Ag or with biodegradable polymers. From the literature, we can observe that polyaniline based composites have good photothermal conversion efficiency and they have a lot of advantages over other conducting polymers. They have high water solubility, high NR absorbance, high therapeutic action, and minimum cytotoxicity. There has been less research on conducting polymers, and future research should focus on different conducting polymer composites.

Among conducting polymers, polyaniline and polypyrrole have been effectively used for electrochemical sensing applications. Nanostructures of conducting polymers have great prospects in sensing action because of their high surface area or high surface to volume ratio for the diffusion of analyte gas molecules into and out of the polymer matrix, compared to their bulk form. The conducting polymer morphology and film thickness play an essential role in the sensing action because of inter-domain spacing, and this will reduce the interaction of analyte gas with the polymer. Polyaniline has better sensing behavior than the others due to its reversible doping mechanism. Hybrid conducting polymers overcome the drawback of selectivity and the high working temperature problem of metal oxide chemiresistors. Polyaniline and polypyrrole conducting polymers, and their combinations, should be explored more for the detection of oxidizing and reducing gases. Future developments should focus on other conducting polymers.

Conflicts of interest

The authors declare no conflict of interest.

Supplementary Material

Acknowledgments.

The authors would like to acknowledge financial support from SERB Early Career Research project (Grant No. ECR/2017/001850), Department of Science and Technology (DST/NM/NT/2019/205(G); DST/TDT/SHRI-34/2018), Karnataka Science and Technology Promotion Society (KSTePS/VGST-RGS-F/2018-19/GRD NO. 829/315), startup grant, Jain University (11 (39)/17/013/2017SG), Nanomission (SR/NM/NS-20/2014) for the characterization facilities.

Biographies

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Namsheer. K received his B-Tech in Polymer engineering from Mahatma Gandhi University (Kerala, India) in 2016 and M-Tech in Nanoscience and technology from Pondicherry Central University (Pondicherry, India) in 2019. He is currently a Nanoscience doctoral student at the Centre for Nano & Material Science, Jain University, working under Prof. Dr Chandra Sekhar Rout. His current research focuses on designing and fabrication of Polymer nanocomposite/2D materials for energy storage applications.

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Dr Chandra Sekhar Rout is Associate Professor at the Centre for Nano & Material Sciences (CNMS), Jain University. Before joining CNMS, he was a DST-Ramanujan Fellow at I.I.T. Bhubaneswar, India (2013–2017). He received his B.Sc. (2001) and M.Sc. (2003) degrees from Utkal University and his Ph.D. from JNCASR, Bangalore (2008) under the supervision of Prof. C. N. R. Rao. He did his postdoctoral research at the National University of Singapore (2008–2009), Purdue University, USA (2010–2012), and UNIST, South Korea (2012–2013). His research interests include 2D materials for sensors, supercapacitors, energy storage devices, field emitters, and electronic devices.

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Published: 30 March 2020

3D printing of conducting polymers

Hyunwoo Yuk ORCID: orcid.org/0000-0003-1710-9750 1 na1 ,
Baoyang Lu ORCID: orcid.org/0000-0003-4663-4706 2 , 3 , 4 na1 ,
Shen Lin 5 ,
Jingkun Xu 2 , 3 ,
Jianhong Luo 5 &
Xuanhe Zhao ORCID: orcid.org/0000-0001-5387-6186 1 , 4

Nature Communications volume 11 , Article number: 1604 ( 2020 ) Cite this article

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Electronic devices
Gels and hydrogels
Mechanical engineering

Conducting polymers are promising material candidates in diverse applications including energy storage, flexible electronics, and bioelectronics. However, the fabrication of conducting polymers has mostly relied on conventional approaches such as ink-jet printing, screen printing, and electron-beam lithography, whose limitations have hampered rapid innovations and broad applications of conducting polymers. Here we introduce a high-performance 3D printable conducting polymer ink based on poly(3,4-ethylenedioxythiophene):polystyrene sulfonate (PEDOT:PSS) for 3D printing of conducting polymers. The resultant superior printability enables facile fabrication of conducting polymers into high resolution and high aspect ratio microstructures, which can be integrated with other materials such as insulating elastomers via multi-material 3D printing. The 3D-printed conducting polymers can also be converted into highly conductive and soft hydrogel microstructures. We further demonstrate fast and streamlined fabrications of various conducting polymer devices, such as a soft neural probe capable of in vivo single-unit recording.

3D printable high-performance conducting polymer hydrogel for all-hydrogel bioelectronic interfaces

Highly conductive and stretchable nanostructured ionogels for 3D printing capacitive sensors with superior performance

A high-conductivity n -type polymeric ink for printed electronics

Introduction.

Conducting polymers, a class of polymers with intrinsic electrical conductivity, have been one of the most promising materials in applications as diverse as energy storage 1 , flexible electronics 2 , and bioelectronics 3 , owing to their unique polymeric nature as well as favorable electrical and mechanical properties, stability, and biocompatibility. Despite recent advances in conducting polymers and their applications, the fabrication of conducting polymer structures and devices have mostly relied on conventional manufacturing techniques such as ink-jet printing 4 , 5 , 6 , screen printing 7 , aerosol printing 8 , 9 , 10 , electrochemical patterning 11 , 12 , 13 , and lithography 14 , 15 , 16 with limitations and challenges. For example, these existing manufacturing techniques for conducting polymers are limited to low-resolution (e.g., over 100 µm), two-dimensional (e.g., low aspect ratio) patterns, and/or complex and high cost procedures (e.g., multi-step processes in clean room involving alignments, masks, etchings, post-assemblies) 4 , 5 , 7 , 14 , 15 , 16 (Supplementary Table 1 ), which have hampered rapid innovations and broad applications of conducting polymers. Unlike these conventional approaches, three-dimensional (3D) printing offers capabilities to fabricate microscale structures in a programmable, facile, and flexible manner with a freedom of design in 3D space 17 , 18 (Supplementary Table 1 ). For example, recent developments of 3D printable materials such as metals 19 , 20 , liquid metals 21 , hydrogels 22 , 23 , cell-laden bioinks 24 , 25 , 26 , glass 27 , liquid crystal polymers 28 , and ferromagnetic elastomers 29 have greatly expanded the accessible materials library for 3D printing. While intensive efforts have been devoted to 3D printing of conducting polymers, only simple structures such as isolated fibers have been achieved 30 , 31 , 32 owing to insufficient 3D printability of existing conducting polymer inks.

Here we invent a high-performance 3D printable ink based on one of the most widely utilized conducting polymers poly(3,4-ethylenedioxythiophene):polystyrene sulfonate (PEDOT:PSS) to take advantage of advanced 3D printing for the fabrication of conducting polymers. To achieve favorable rheological properties for 3D printing, we develop a paste-like conducting polymer ink based on cryogenic freezing of aqueous PEDOT:PSS solution followed by lyophilization and controlled re-dispersion in water and dimethyl sulfoxide (DMSO) mixture. The resultant conducting polymer ink exhibits superior 3D printability capable of high resolution (over 30 µm), high aspect ratio (over 20 layers), and highly reproducible fabrication of conducting polymers, which are also readily integratable with other 3D printable materials such as insulating elastomers by multi-material 3D printing. Dry-annealing of the 3D-printed conducting polymers provides highly conductive (electrical conductivity over 155 S cm −1 ) and flexible PEDOT:PSS 3D microstructures in the dry state. Moreover, the dry-annealed 3D-printed conducting polymers can be readily converted into a soft (Young’s modulus below 1.1 MPa) yet highly conductive (electrical conductivity up to 28 S cm −1 ) PEDOT:PSS hydrogel via subsequent swelling in the wet environment. We further demonstrate a facile and streamlined fabrication of various functional conducting polymer devices by multi-material 3D printing, including a high-density flexible electronic circuit and a soft neural probe capable of in vivo single-unit recording.

3D printable conducting polymer ink

Conducting polymers are typically used in the form of liquid monomer or polymer solution whose fluidity prevents their direct use in 3D printing 3 , 5 , 33 . In order to endow rheological properties required for 3D printing to conducting polymers, we develop a simple process to convert a commercially available PEDOT:PSS aqueous solution to a high-performance 3D printable ink (Fig. 1 and Supplementary Fig. 1 ). The pristine PEDOT:PSS solution exhibits a dilute dispersion of PEDOT:PSS nanofibrils (Fig. 1a, d ) with low viscosity (below 30 Pa s). Inspired by 3D printability of concentrated cellulose nanofiber suspensions 34 , 35 , we hypothesize that a highly concentrated solution of the PEDOT:PSS nanofibrils can provide a 3D printable conducting polymer ink, due to the formation of entanglements among PEDOT:PSS nanofibrils (Fig. 1b ). To test our hypothesis, we first isolate PEDOT:PSS nanofibrils by lyophilizing the pristine PEDOT:PSS solution. In order to avoid excessive formation of PEDOT-rich crystalline domains among PEDOT:PSS nanofibrils due to slow ice crystal formation during lyophilization at high temperature 36 , we perform lyophilization in a cryogenic condition (i.e., frozen in liquid nitrogen). The isolated PEDOT:PSS nanofibrils are then re-dispersed with a binary solvent mixture (water:DMSO = 85:15 v/v) to prepare concentrated suspensions.

a , b , Pristine PEDOT:PSS solution ( a ) can be converted into a 3D printable conducting polymer ink ( b ) by lyophilization in cryogenic condition and re-dispersion with a solvent. c , 3D-printed conducting polymers can be converted into a pure PEDOT:PSS both in dry and hydrogel states by dry-annealing and subsequent swelling in wet environment, respectively. d CryoTEM image of a pristine PEDOT:PSS solution. e CryoTEM image of a 3D printable conducting polymer ink. f TEM image of a dry-annealed 3D-printed conducting polymer. g – j Images of re-dispersed suspensions with varying PEDOT:PSS nanofibril concentration. k SAXS characterization of conducting polymer inks with varying PEDOT:PSS nanofibril concentration. The d-spacing L is calculated by the Bragg expression L = 2π/ q max . l Apparent viscosity as a function of shear rate for conducting polymer inks of varying PEDOT:PSS nanofibril concentration. m Apparent viscosity of conducting polymer inks as a function of PEDOT:PSS nanofibril concentration. n Shear storage modulus as a function of shear stress for conducting polymer inks of varying PEDOT:PSS nanofibril concentration. o Shear yield stress of conducting polymer inks as a function of PEDOT:PSS nanofibril concentration. For TEM images in ( d – f ), the experiments were repeated ( n = 5) based on independently prepared samples with reproducible results. Scale bars, 100 nm.

With increasing concentration of the PEDOT:PSS nanofibrils, the suspensions gradually transit from liquids to thixotropic 3D printable inks (Fig. 1g–j ) due to the formation of reversible physical networks of the PEDOT:PSS nanofibrils via entanglements within the solvent (Fig. 1e ). We perform small angle X-ray scattering (SAXS) and rheological characterizations to quantify microscopic and macroscopic evolutions of the conducting polymer ink with varying concentrations of the PEDOT:PSS nanofibrils, respectively (Fig. 1k–o ). The SAXS characterizations show that the average distance between PEDOT-rich crystalline domains L (d-spacing calculated by the Bragg expression L = 2π/ q max ) decreases with an increase in the concentration of the PEDOT:PSS nanofibrils (16.1 nm for 1 wt% and 7.0 nm for 10 wt%), indicating closer packing and higher degree of interactions between the adjacent PEDOT:PSS nanofibrils in more concentrated inks (Fig. 1k ).

Rheological measurements of the conducting polymer inks clearly show the transition from low viscosity liquids (low concentration PEDOT:PSS nanofibrils) to physical gels (high concentration PEDOT:PSS nanofibrils) with characteristic shear-thinning and shear-yielding properties for 3D printable inks 18 , 19 (Fig. 1l–o and Supplementary Fig. 2 ). The low viscosity and low yield stress of the conducting polymer inks with low PEDOT:PSS nanofibril concentrations (1-4 wt%) cause lateral spreading of 3D-printed inks on the substrate (Fig. 1g, h, m, o ). On the other hand, the conducting polymer inks with too high concentrations of PEDOT:PSS nanofibrils (above 8 wt%) start to clog printing nozzles due to the formation of large aggregates of PEDOT:PSS nanofibrils (Fig. 1j, m, o ). Hence, we find that the intermediate range of PEDOT:PSS nanofibril concentrations (5–7 wt%) provides optimal rheological properties and 3D printability (Fig. 1i, m, o ). The 3D printable conducting polymer ink can be stored under ambient conditions over a month without the significant change in rheological properties and printability (Supplementary Fig. 3 ). After 3D printing, we dry and anneal the 3D-printed conducting polymers to remove solvents (water and DMSO) and facilitate the formation of PEDOT-rich crystalline domains and subsequent percolation among PEDOT:PSS nanofibrils 33 (Fig. 1c, f ) (see Methods for details). The resultant dry pure PEDOT:PSS can also be readily converted into stable pure PEDOT:PSS hydrogels (equilibrium water contents ~ 87%) by swelling in a wet environment 33 .

Superior printability of the conducting polymer ink allows various advanced 3D printing capabilities including printing of high resolution, high aspect ratio, and overhanging structures (Fig. 2 ). To demonstrate high resolution printing in microscale, we print meshes of the conducting polymer ink (7 wt% PEDOT:PSS nanofibril) through 200-, 100-, 50-, and 30-µm diameter nozzles (Fig. 2a–d ). Favorable rheological properties of the conducting polymer ink further enable the fabrication of multi-layered high aspect ratio microstructures (100-µm nozzle, 20 layers) (Supplementary Movie 1 ) as well as overhanging features (Supplementary Movie 2 ) (Fig. 2e, h ). The 3D-printed conducting polymer structures can readily be converted into dry and hydrogel forms without loss of the original microscale structures, owing to the constrained drying (while attached on the substrate) and swelling property of the pure PEDOT:PSS hydrogels 33 (Fig. 2f, g and Supplementary Fig. 4 ). Furthermore, the 3D-printed conducting polymer hydrogels exhibit long-term stability in physiological wet environments without observable degradation of microscale features (e.g., high aspect ratio and overhanging structures) after storing in PBS for 6 months (Supplementary Fig. 5 ).

a – d SEM images of 3D-printed conducting polymer meshes by 200-µm ( a ), 100-µm ( b ), 50-µm ( c ), and 30-µm ( d ) nozzles. e Sequential snapshots for 3D printing of a 20-layered meshed structure by the conducting polymer ink. f 3D-printed conducting polymer mesh after dry-annealing. g 3D-printed conducting polymer mesh in hydrogel state. h Sequential snapshots for 3D printing of overhanging features over high aspect ratio structures by the conducting polymer ink. i 3D-printed conducting polymer structure with overhanging features in hydrogel state. Scale bars, 500 µm ( a ); 200 µm ( b – d ); 1 mm ( a – d , inset panels); 2 mm ( e – i ).

The 3D printable conducting polymer ink can be readily incorporated into multi-material 3D printing processes together with other 3D printable materials. For example, we fabricate a structure that mimics a high-density multi-electrode array (MEA) based on multi-material 3D printing of the conducting polymer ink and an insulating polydimethylsiloxane (PDMS) ink with a total printing time less than 30 min (Supplementary Fig. 6a, b and Supplementary Movie 3 ). The 3D-printed MEA-like structure shows a complex microscale electrode pattern and a PDMS well that are comparable to a commercially available MEA fabricated by multi-step lithographic processes and post-assembly (Supplementary Fig. 6c ).

Properties of 3D-printed conducting polymers

The 3D-printed conducting polymers can achieve electrical conductivity as high as 155 S cm −1 in the dry state and 28 S cm −1 in the hydrogel state, comparable to the previously reported high-performance conducting polymers 5 , 16 , 33 (Fig. 3a , Supplementary Fig. 7 , and Supplementary Table 2 ). Notably, a smaller nozzle diameter yields a higher electrical conductivity for the printed conducting polymers, potentially due to shear-induced enhancements in the PEDOT:PSS nanofibril alignment 22 . Flexibility of the 3D-printed conducting polymers allows mechanical bending with maximum strain of 13% in the dry state (65 µm radius of curvature with 17 µm thickness) and 20% in the hydrogel state (200 µm radius of curvature with 78 µm thickness) without failure (Supplementary Fig. 8 ). To investigate the effect of mechanical bending on the electrical performance, we characterize the electrical conductivity of the 3D-printed conducting polymers (100-µm nozzle, 1 layer) on flexible polyimide substrates as a function of the bending radius as well as the bending cycle (Fig. 3b, c ). The 3D-printed conducting polymers show small changes in the electrical conductivity (less than 5%) across a wide range of tensile and compressive bending conditions (radius of curvature, ±1–20 mm) in both the dry and hydrogel states (Fig. 3b ). Furthermore, the 3D-printed conducting polymers can maintain a high electrical conductivity (over 100 S cm −1 in dry state and over 15 S cm −1 in hydrogel state) after 10,000 cycles of repeated bending (Fig. 3c ).

a Conductivity as a function of nozzle diameter for 3D-printed conducting polymers in dry and hydrogel states. b Conductivity as a function of bending radius for 3D-printed conducting polymers in dry (17 µm, thickness) and hydrogel (78 µm, thickness) states. PI indicates polyimide. c Conductivity as a function of bending cycles for 3D-printed conducting polymers in dry (17 µm, thickness) and hydrogel (78 µm, thickness) states. d Nyquist plot obtained from the EIS characterization for a 3D-printed conducting polymer on Pt substrate (78 µm, thickness) overlaid with the plot predicted from the corresponding equivalent circuit model 38 . In the equivalent circuit models, R e represents electronic resistance, R i represents ionic resistance, R c represents the total ohmic resistance of the cell assembly, CPE dl represents the double-layer constant phase element (CPE), whereas CPE g represents the geometric CPE. CPE is used to account inhomogeneous or imperfect capacitance and are represented by the parameters Q and n where Q represents the peudocapacitance value and n represents the deviation from ideal capacitive behavior. The true capacitance C can be calculated from these parameters by using the relationship C = Q ω max n −1 , where ω max is the frequency at which the imaginary component reaches a maximum 37 . The fitted values for 3D-printed PEDOT:PSS are R e = 107.1 Ω, R i = 105.5 Ω, R c = 14.07 Ω, Q dl = 1.467 × 10 −5 F s n −1 , n dl = 0.924, Q g = 4.446 × 10 −7 F s n −1 , and n dl = 0.647. e CV characterization for a 3D-printed conducting polymer on Pt substrate. f Nanoindentation characterizations for 3D-printed conducting polymers in dry and hydrogel states with the JKR model fits. Values in ( a – c ) represent the mean and the standard deviation ( n = 5 per each testing conditions based on independently prepared samples and performed experiments).

To further investigate the electrical properties, we perform the electrochemical impedance spectroscopy (EIS) of the 3D-printed conducting polymers (100-µm nozzle, 1 layer on Pt) (Fig. 3d ). The EIS data are fitted to the equivalent circuit model shown in Fig. 3d , where R e represents the electronic resistance, R i represents the ionic resistance, R c represents the total ohmic resistance of the electrochemical cell assembly, and CPE dl and CPE g represent the constant phase elements (CPE) corresponding to the double-layer ionic capacitance and the geometric capacitance, respectively 37 , 38 . The semicircular Nyquist plot shape suggests the presence of comparable ionic and electronic conductivity in the 3D-printed conducting polymer hydrogels (Fig. 3d ), which is confirmed by the extracted fitting parameters of the equivalent circuit model where the ionic and electronic resistances show comparable magnitudes ( R i = 105.5 Ω and R e = 107.1 Ω).

The cyclic voltammetry (CV) demonstrates a high charge storage capability (CSC) of the 3D-printed conducting polymers (100-µm nozzle, 1 layer on Pt) compared to typical metallic electrode materials such as Pt with remarkable electrochemical stability (less than 2% reduction in CSC after 1000 cycles) (Fig. 3e ). The CV of the 3D-printed conducting polymers further shows broad and stable anodic and cathodic peaks under varying potential scan rates 39 , suggesting non-diffusional redox processes and electrochemical stability of the 3D-printed conducting polymers (Supplementary Fig. 9 ).

To quantify mechanical properties of the 3D-printed conducting polymers, we conduct nanoindentation tests (Fig. 3f and Supplementary Fig. 10 ). The 3D-printed conducting polymers display relatively high Young’s modulus of 1.5 ± 0.31 GPa in the dry state, similar to the previously reported values for dry PEDOT:PSS 40 (Fig. 3f ). In contrast, the 3D-printed conducting polymers in the hydrogel state exhibit three orders of magnitude reduction in Young’s modulus to 1.1 ± 0.36 MPa, comparable to those of soft elastomers such as PDMS (Young’s modulus, 1–10 MPa) (Fig. 3f ). The softness of 3D-printed conducting polymer hydrogels can offer favorable long-term biomechanical interactions with biological tissues, which may find a particular advantage in bioelectronic devices and implants 3 , 41 , 42 .

3D printing of conducting polymer devices

Enabled by the superior 3D printability and properties, 3D printing of the conducting polymer ink can offer a promising route for facile and streamlined fabrication of high resolution and multi-material conducting polymer structures and devices (Fig. 4 and Supplementary Table 1 ). Highly reproducible 3D printing of conducting polymers in high resolution allows the rapid fabrication of over 100 circuit patterns with less than 100 µm feature size on a flexible polyethylene terephthalate (PETE) substrate by a single continuous printing process with a total printing time less than 30 min (Fig. 4a , Supplementary Fig. 11 , and Supplementary Movie 4 ). The resultant 3D-printed conducting polymer electronic circuits exhibit high electrical conductivity to operate electrical components such as a light emitting diode (LED) (Fig. 4b and Supplementary Movie 4 ) and flexibility to withstand bending without mechanical failure (Fig. 4c ). This programmable, high resolution, and high throughput fabrication of conducting polymer patterns by 3D printing can potentially serve as an alternative to ink-jet printing and screen printing with a higher degree of flexibility in the choice of designs based on applicational demands 4 , 7 .

a Sequential snapshots for 3D printing of high-density flexible electronic circuit patterns by the conducting polymer ink. b Lighting up of LED on the 3D-printed conducting polymer circuit. PETE indicates polyethylene terephthalate. c Bending of the 3D-printed conducting polymer circuit without failure. d Image of the 3D-printed soft neural probe with 9-channels by the conducting polymer ink and the PDMS ink. e Image of the 3D-printed soft neural probe in magnified view. f Images of the implanted 3D-printed soft neural probe (top) and a freely moving mouse with the implanted probe (bottom). g , h Representative electrophysiological recordings in the mouse dHPC by the 3D-printed soft neural probe. Local field potential (LFP) traces (0.5 to 250 Hz) under freely moving conditions ( g ). Continuous extracellular action potential (AP) traces (300 to 40 kHz) recorded under freely moving conditions ( h ). i Principal component analysis of the recorded single-unit potentials from ( h ). j Average two units spike waveforms recorded over time corresponding to clusters in ( i ). Scale bars, 5 mm ( a – c ); 1 mm ( d , e ); 2 mm ( f ).

We further demonstrate a facile fabrication of a soft neural probe for in vivo bioelectronic signal recording (Supplementary Fig. 12 and Supplementary Movie 5 ). The multi-material 3D printing capability in high resolution allows us to print both insulating encapsulation (PDMS ink) and electrodes (conducting polymer ink) of the neural probe by a facile continuous printing process (a total printing time less than 20 min) without the need of post-assemblies or complex multi-step procedures in conventional fabrication methods such as electron-beam lithography 15 , 16 (Fig. 4d , Supplementary Fig. 12 , and Supplementary Movie 5 ). The resultant probe consists of nine PEDOT:PSS electrode channels in the feature size of 30 µm in diameter with the impedance in the range of 50–150 kΩ at 1 kHz, suitable for in vivo recording of neural activities 43 , 44 . After the connector assembly (Supplementary Fig. 13 ), the 3D-printed soft neural probe is implanted to the mouse dorsal hippocampus (dHPC, coordinate: −1.8 mm AP; 1.5 mm ML; −1.0 mm DV) with the help of a plastic catheter (Fig. 4f , top). The 3D-printed soft neural probe can successfully record continuous neural activities in a freely moving mouse (Fig. 4f , bottom) from each channel including the local field potential (LFP; at 1 kHz) (Fig. 4g ) and the action potential (AP; at 40 kHz) (Fig. 4h ) over two weeks. Furthermore, the 3D-printed soft neural probe can record signals from distinctive single units, isolated from individual channel of the probe (Fig. 4i, j ).

In summary, we present a high-performance 3D printable conducting polymer ink based on PEDOT:PSS capable of rapid and flexible fabrication of highly conductive microscale structures and devices both in the dry and hydrogel states. The conducting polymer ink exhibits superior 3D printability and ready integrability into advanced multi-material 3D printing processes with other 3D printable materials. Enabled by this capability, we further demonstrate 3D printing-based fabrication of the high-density flexible electronic circuit and the soft neural probe in a facile, fast, and significantly streamlined manner. This work not only addresses the existing challenges in 3D printing of conducting polymers but also offers a promising fabrication strategy for flexible electronics, wearable devices, and bioelectronics based on conducting polymers.

Preparation of 3D printable conducting polymer ink

A commercially available PEDOT:PSS aqueous solution (Clevios TM PH1000, Heraeus Electronic Materials) was stirred vigorously for 6 h at room temperature and filtered with a syringe filter (0.45 µm). The filtered pristine PEDOT:PSS solution was then cryogenically frozen by submerging in liquid nitrogen bath. The cryogenically frozen PEDOT:PSS solution was lyophilized for 72 h to isolate PEDOT:PSS nanofibrils. The isolated PEDOT:PSS nanofibrils with varying concentrations were re-dispersed with a deionized water-DMSO (Sigma-Aldrich) mixture (water:DMSO = 85:15 v/v), followed by thorough mixing and homogenization by a mortar grinder (RM 200, Retcsh). The prepared conducting polymer ink was kept at 4 °C before use. The detailed procedure for the 3D printable conducting polymer ink preparation is illustrated in Supplementary Fig. 1 .

3D printing procedure

3D printing of the conducting polymer ink and the PDMS ink (SE 1700, Dow Corning) were conducted based on a custom-designed 3D printer based on a Cartesian gantry system (AGS1000, Aerotech) 18 with various size of nozzles (200- and 100-µm nozzles from Nordson EFD; 50-µm nozzles from Fisnar; 30-µm nozzles from World Precision Instrument). Printing paths were generated by CAD drawings (SolidWorks, Dassault Systèmes) and converted into G-code by a commercial software package (CADFusion, Aerotech) and custom Python scripts to command the x-y-z motion of the printer head. The detailed printing paths are provided in Supplementary Figs. 6 , 11 , and 12 .

After printing, the 3D-printed conducting polymer was dried at 60 °C for 24 h followed by multiple cycles of annealing at 130 °C (3 cycles with 30 min per each cycle) to yield pure PEDOT:PSS 33 . To achieve constrained drying of 3D-printed conducting polymers in thickness direction, the 3D-printed conducting polymers were placed on a glass substrate and dry-annealed. The dry-annealed 3D-printed conducting polymer was further equilibrated in PBS to be converted into a hydrogel state.

Electron microscope imaging

Scanning electron microscope (SEM) images of the 3D-printed conducting polymers were taken by using a SEM facility (JSM-6010LA, JEOL) with 5 nm gold sputtering to enhance image contrasts. Transmission electron microscope (TEM) images of the pristine PEDOT:PSS solution, conducting polymer ink, and dry-annealed 3D-printed conducting polymer were taken by using a TEM facility (2100 FEG, JEOL) at 200 kV with a magnification of 10,000 to 60,000. For cryogenic TEM (CryoTEM) imaging, the samples were prepared by a cryo plunger (CP3, Gatan). All Images were recorded under low-dose conditions to avoid sample damage by electron beams.

Small angle X-ray scattering (SAXS) characterizations of the conducting polymer inks were conducted by using a SAXS facility (Pilatus 3 R 300 K, Bruker Nanostar SAXS) with a sample-detector distance of 1059.1 mm and an exposure time of 300 s. The measured scattering intensity was corrected by subtracting the solvent background (water:DMSO = 85:15 v/v). To analyze the average distance between PEDOT crystalline domains in the 3D printable conducting polymer inks, the d-spacing L was calculated by the Bragg expression L = 2π/ q max without further fitting of the SAXS data.

Rheological characterization

Rheological characterizations of the conducting polymer inks were conducted by using a rotational rheometer (AR-G2, TA Instrument) with 20-mm diameter steel parallel-plate geometry. Apparent viscosity was measured as a function shear rate by steady-state flow tests with a logarithmic sweep of shear rate (0.01–100 s −1 ). Shear storage modulus ( G ′) and loss modulus ( G ″) were measured as a function of shear stress via oscillation tests with a logarithmic sweep of shear stress (1–1000 Pa) at 1 Hz shear frequency and oscillatory strain of 0.02. Shear yield stress for each sample was identified as a shear stress at which shear and loss moduli were the same values. All rheological characterizations were conducted at 25 °C with preliminary equilibration time of 1 min.

Nanoindentation

Nanoindentation characterizations of 3D-printed conducting polymers were conducted by using an atomic force microscope (AFM) facility (MFP-3D, Asylum Research) with indentation depth of 50 nm (for dry state) and 1 µm (for hydrogel state). A spherical tip with 50 nm radius (biosphere TM , Asylum Research) was used for the nanoindentation measurements. Young’s moduli of the samples were obtained by fitting force vs. indentation curve with a JKR model 45 (Fig. 3f ).

Electrical conductivity measurement

Electrical conductivity of the 3D-printed conducting polymers was measured by using a standard four-point probe (Keithley 2700 digital multimeter, Keithley). To prepare conductivity measurement samples, one layer of the conducting polymer ink was printed into a rectangular shape (30 mm in length and 5 mm in width) with 100-µm nozzles on glass substrates (17 µm and 78 µm in thickness for dry-annealed and hydrogel samples, respectively). Copper wire electrodes (diameter, 0.5 mm) were attached onto the surface of dry-annealed 3D-printed conducting polymer by applying silver paste, while platinum wire electrodes (diameter, 0.5 mm) were employed for hydrogels to avoid the corrosion in wet environments (Supplementary Fig. 7 ). The electrical conductivity σ of the samples was calculated as

where I is the current flowing through the sample, L is the distance between the two electrodes for voltage measurement, V is the voltage across the electrodes, W is the width of the sample, and T is the thickness of the sample.

For electrical conductivity measurements under cyclic bending, one layer of the conducting polymer ink was printed into a rectangular shape (30 mm in length and 5 mm in width) with 100-µm nozzles on polyimide substrates (17 µm and 78 µm in thickness for dry-annealed and hydrogel samples, respectively). Cyclic bending of the sample was performed by using a custom-made fixture with controllable bending radius of curvature.

Electrochemical measurement

Cyclic voltammetry (CV) of the 3D-printed conducting polymer was performed by using a potentiostat/galvanostat (VersaSTAT 3, Princeton Applied Research) with a range of scan rates (50 to 500 mV s −1 ). Pt wires (diameter, 1 mm) were employed as both working and counter electrodes, and an Ag/AgCl electrode was used as the reference electrode. Prior to all measurements, the working and counter electrodes were cleaned successively with abrasive paper, deionized water, and ethyl alcohol. PBS was used as the supporting electrolyte.

Electrochemical impedance spectroscopy (EIS) measurements of the 3D-printed conducting polymer were carried out by using a potentiostat/galvanostat (1287 A, Solartron Analytical) and a frequency response analyzer (1260 A, Solatron Analytical) in an electrochemical cell installed with Pt sheet as both working and counter electrodes and Ag/AgCl as a reference electrode. The frequency range between 0.1 and 100 kHz was scanned in PBS with an applied bias of 0.01 V vs. Ag/AgCl. The EIS data for the 3D-printed conducting polymer were fitted by using an equivalent circuit model for further analysis (Fig. 3d ).

In vivo electrophysiology by 3D-printed soft neural probe

Young adult mice (60-70 days old, Balb/C Male Jackson Laboratory Stock # 000651) were used in the electrophysiological experiments. Mice were maintained under a 12 h light/dark cycle at 22–25 °C, and given ad libitum access to tap water and standard chow. All procedures were approved by the Animal Advisory Committee at Zhejiang University and followed the US National Institutes of Health Guidelines for the Care and Use of Laboratory Animals. For all surgeries, mice were anesthetized with 1% pentobarbital (Sigma-Aldrich), and then fixed in a stereotaxic frame. A craniotomy was performed at −1.80 mm anterior to bregma and 1.5 mm lateral to the midline. The incision was closed with tissue glue (VetBond TM , 3 M). Electrophysiological recording in the dHPC was carried out by using the 3D-printed soft neural probe coupling with Neuro Nano Strip Connectors (Omnetics). All data shown in Fig. 4g–j were collected from BALB/c mice in the dHPC with a 64-channel multi-electrode recording system (Plexon). After the probe implantation, mice were allowed to recover for at least 3 days. Neuronal signals were referenced to two connected skull screws (above the prefrontal cortex and cerebellum). Spike sorting was carried out in Offline Sorter software (Plexon). In the principal component analysis, a rough separation of units from PNs and interneurons in the dHPC was mainly based on their differences in spike wave shapes and mean baseline firing rates.

Reporting summary

Further information on research design is available in the Nature Research Reporting Summary linked to this article.

Data availability

The data that support the findings of this study are available from the corresponding author upon reasonable request.

Code availability

The custom codes used this study for 3D printing are available from the corresponding author upon reasonable request.

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Acknowledgements

The authors thank Dr. Alan F. Schwartzman in MIT DMSE Nanomechanical Technology Laboratory for his help with AFM nanoindentation experiment and Dr. Dong Soo Yun in MIT Koch Institute Nanotechnology Materials Core for his help with TEM imaging. This work is supported by MIT. H.Y. acknowledges the financial support from Samsung Scholarship. B.L. acknowledges the financial support from National Natural Science Foundation of China (51763010 & 51963011), Technological Expertise and Academic Leaders Training Program of Jiangxi Province (20194BCJ22013), and Research Project of State Key Laboratory of Mechanical System and Vibration (MSV202013).

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These authors contributed equally: Hyunwoo Yuk, Baoyang Lu.

Authors and Affiliations

Department of Mechanical Engineering, Massachusetts Institute of Technology, Cambridge, MA, 02139, USA

Hyunwoo Yuk & Xuanhe Zhao

Flexible Electronics Innovation Institute, Jiangxi Science and Technology Normal University, Nanchang, 330013, China

Baoyang Lu & Jingkun Xu

School of Pharmacy, Jiangxi Science and Technology Normal University, Nanchang, 330013, China

Baoyang Lu, Kai Qu & Jingkun Xu

Department of Civil and Environmental Engineering, Massachusetts Institute of Technology, Cambridge, 02139, USA

Baoyang Lu & Xuanhe Zhao

Department of Neurobiology, Key Laboratory of Medical Neurobiology of the Ministry of Health of China, Collaborative Innovation Center for Brain Science, Zhejiang University of Medicine, Hangzhou, Zhejiang, 310058, China

Shen Lin & Jianhong Luo

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Contributions

H.Y. and B.L. conceived the idea. H.Y. and X.Z. developed the 3D printing platform. H.Y. and B.L. developed the materials and method and conducted experiments. K.Q. and J.X. conducted the electrical conductivity measurements. S.L. and J.L. designed and conducted the in vivo bioelectronic experiments. H.Y., B.L., and X.Z. analyzed the results and wrote the manuscript with inputs from all authors.

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Correspondence to Xuanhe Zhao .

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H.Y., B.L., and X.Z. are inventors of a U.S. patent application that covers the 3D printing of conducting polymers. All other authors declare no competing interests.

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Yuk, H., Lu, B., Lin, S. et al. 3D printing of conducting polymers. Nat Commun 11 , 1604 (2020). https://doi.org/10.1038/s41467-020-15316-7

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Recent developments in conducting polymers: applications for electrochemistry.

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a Research Center for Tropical and Infectious Diseases, Kerman University of Medical Sciences, Kerman, Iran

b Environment Department, Institute of Science and High Technology and Environmental Sciences, Graduate University of Advanced Technology, Kerman, Iran E-mail: [email protected]

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Scientists have categorized conductive polymers as materials having strongly reversible redox behavior and uncommon combined features of plastics and metal. Because of their multifunctional characteristics, e.g. , simplistic synthesis, acceptable environmental stability, beneficial optical, electronic, and mechanical features, researchers have largely considered them for diverse applications. Therefore, their capability of catalyzing several electrode reactions has been introduced as one of their significant features. A thin layer of the conducting polymer deposited on the substrate electrode surface can augment the electrode process kinetics of several solution species. Such electrocatalytic procedures with modified conducting polymer electrodes can create beneficial utilization in diverse fields of applied electrochemistry. This review article explores typical recent applications of conductive polymers (2016–2020) as active electrode materials for energy storage applications, electrochemical sensing, and conversion fields such as electrochemical supercapacitors, lithium-ion batteries, fuel cells, and solar cells.

Graphical abstract: Recent developments in conducting polymers: applications for electrochemistry

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This work was supported by the National Natural Science Foundation of China (62304112), the Natural Science Foundation of Jiangsu Province of China (BK20230359), the Natural Science Foundation of the Higher Education Institutions of Jiangsu Province (22KJB430038), and the Natural Science Research Start-up Foundation of Recruiting Talents of Nanjing University of Posts and Telecommunications (NY221111).

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Li, Y., Li, T., Ji, Y. et al. Manufacture the conducting polymer with light. Sci. China Chem. (2024). https://doi.org/10.1007/s11426-024-2239-4

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Received : 08 July 2024

Accepted : 04 August 2024

Published : 06 September 2024

DOI : https://doi.org/10.1007/s11426-024-2239-4

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Conducting polymers: a comprehensive review on recent advances in
Conducting polymers are extensively studied due to their outstanding properties, including tunable electrical property, optical and high mechanical properties, easy synthesis and effortless fabrication and high environmental stability over conventional inorganic materials. Although conducting polymers have a lot of 2021 Reviews in RSC Advances Conducting polymers
Conducting polymers: a comprehensive review on recent advances in
1. Introduction Polymers were considered to be electrical insulators before the invention of conducting polymers (conjugate polymers), but these organic polymers have unique electrical and optical properties similar to those of inorganic semiconductors. 1 A conjugated carbon chain consists of alternating single and double bonds, where the highly delocalized, polarized, and electron-dense π ...
Conducting polymers: a comprehensive review on recent advances in
solitons, bipolarons, etc., and the polymer transforms from a nonlinear excitation state to a metallic state.5-7 Here in this comprehensive review, we eﬀectively discuss the diﬀerent synthesis approaches, properties and various applications of conducting polymers (Fig. 1). 2. Conducting polymers and their synthesis 2.1. Polyacetylene
The journey of conducting polymers from discovery to application
Here we summarize the impact of (semi)conducting polymers on fundamental research, synthetic accessibility at scale, industrial applicability and the future. You have full access to this article ...
Conducting polymers forward
Twenty years after the Nobel Prize in Chemistry for the discovery of conducting polymers, we reflect on the open research questions and the status of commercial development of these materials.
A critical review on intrinsic conducting polymers and their
Introduction. Polymers are created by long chains of molecules known as monomers. Polymers can be compounded with other materials to create conductive polymers (CPs) [1].CPs are perceived as a part of organic materials with remarkable optical and electrical properties [2].Numerous attempts have been made to enhance the electrical conductivity of rubbers and plastics by incorporating specific ...
Conducting polymers: a comprehensive review on recent advances in
An in-depth analysis of composites of conducting polymers with carbonaceous materials, metal oxides, transition metals and transition metal dichalcogenides etc. is used to study them effectively.
Introduction to Conducting Polymers
1 Introduction. Over the years, the concept of conducting polymers (CPs) continues to fascinate the scientific community as several research papers regarding this material have been annually increased. CP is an organic macromolecule that integrates both conventional polymers and metal properties into one system.
Recent trends on synthetic approaches and application studies of
Conducting polymers (CPs) have been the subject of extensive investigation due to their electrical, optical and mechanical properties, easy of synthesis and ease of fabrication and high environmental stability. The present review discusses the fundamentals properties of CPs associated with charge generation, followed by various chemical and electrochemical methods of polymerization of these ...
Conducting polymers: a comprehensive review on recent advances in
Conducting polymers are extensively studied due to their outstanding properties, including tunable electrical property, optical and high mechanical properties, easy synthesis and effortless fabrication and high environmental stability over conventional inorganic materials. Although conducting polymers have a lot of limitations in their pristine ...
PDF Conducting polymers forward
The discovery of electrical conductivity has endowed conjugated polymers with incredible appeal. Once mainly a playground for chemists, materials scientists and process engineers, they are now one ...
Conducting polymers in industry: A comprehensive review on the
Polymer/glass coating, high conductive shell, nano-fiber electrodes, solar cells and so on [23], [44], [82]. Polyparaphenylene (PPP) is identified as an important class of CP made of repeating p-phenylene units. Application of an oxidant or a dopant leads to the conversion of this polymer to its conducting form [83], [84], [85], [86].
Recent developments in conducting polymers: applications for
Polyacetylene instability in air has resulted in the discovery of diverse, novel conducting polymers (CPs) to be utilized in basic studies and industrial applications. 14-16 Therefore, since Heeger, MacDiarmid, and Shirakawa were jointly granted the Nobel Prize in Chemistry in 2000 for their leading research on CPs, academic and industrial ...
Recent Advances in Nanostructured Conducting Polymers: from ...
Conducting polymers (CPs) have been widely studied to realize advanced technologies in various areas such as chemical and biosensors, catalysts, photovoltaic cells, batteries, supercapacitors, and others. ... Feature papers represent the most advanced research with significant potential for high impact in the field. A Feature Paper should be a ...
(PDF) Conducting Polymers and Their Applications
Campus, 59030, Tekird ag, Turkey; Tel: +90 282 2933866 (236); Fax: +90 282 2934 149; E-mail: [email protected]. from a boron trifluoride-di ethyl ether solu tion with th iophene. monomer by electro ...
(PDF) Conducting Polymers: Concepts and Applications
PDF | On Aug 30, 2018, Abhishek Kumar Mishra published Conducting Polymers: Concepts and Applications | Find, read and cite all the research you need on ResearchGate
Conducting polymers: a comprehensive review on recent advances in
1. Introduction. Polymers were considered to be electrical insulators before the invention of conducting polymers (conjugate polymers), but these organic polymers have unique electrical and optical properties similar to those of inorganic semiconductors. 1 A conjugated carbon chain consists of alternating single and double bonds, where the highly delocalized, polarized, and electron-dense π ...
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The 3D-printed conducting polymers can achieve electrical conductivity as high as 155 S cm −1 in the dry state and 28 S cm −1 in the hydrogel state, comparable to the previously reported high ...
A comprehensive overview of common conducting polymer-based
1. Introduction. Nowadays, conducting polymers (CP) play a significant role in conductive materials, and hence have gained wide-spread applicability and been recognized for their unique optical and electrical properties [1], [2].Recently, with the discovery of nanostructure-based materials, such as nanoparticles, nanotubes, and nanowires, nanocomposites have rapidly captured the consideration ...
Synthesis, characterization and applications of conductive polymers: A
In view of increasing applications of electro-conductive polymers in various fields such as electronics, smart textiles, sensors, energy storage, and medical. Researchers & Scientists from all over the world have continuously investigating the intrinsic conductive polymers (CPs) and its doping process to gain appreciable electrical conductivity ...
Recent developments in conducting polymers: applications for
Scientists have categorized conductive polymers as materials having strongly reversible redox behavior and uncommon combined features of plastics and metal. Because of their multifunctional characteristics, e.g., simplistic synthesis, acceptable environmental stability, beneficial optical, electronic, and mechanica Conducting polymers 2020 Reviews in RSC Advances
(PDF) A review on the conducting polymers
During last few decades, many researchers have worked and are working in the field of conducting polymers. The focus of this. review is to give details of methods of synthesis and applications of ...
Conducting polymer based nanocomposites for supercapacitor applications
Research Papers. Conducting polymer based nanocomposites for supercapacitor applications: A review of recent advances, challenges and future prospects. ... Conducting polymers (CPs) have gained a lot of interest because of their distinctive properties like conductivity, stability, and corrosion resistance and their application in different ...
Conductive Polymers: Opportunities and Challenges in Biomedical
Research pertaining to conductive polymers has gained significant traction in recent years, and their applications range from optoelectronics to material science. For all intents and purposes, conductive polymers can be described as Nobel Prize-winning materials, given that their discoverers were awarded the Nobel Prize in Chemistry in 2000. In this review, we seek to describe the chemical ...
Manufacture the conducting polymer with light
Manufacture the conducting polymer with light Download PDF. Yang Li 1, Tianyu Li 1, Yan Ji 1 & … Baoguang Liu 1 ... (22KJB430038), and the Natural Science Research Start-up Foundation of Recruiting Talents of Nanjing University of Posts and Telecommunications (NY221111). ...

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Conducting polymers: a comprehensive review on recent advances in synthesis, properties and applications

Chandra Sekhar Rout

1. Introduction

2. Conducting polymers and their synthesis

2.2. Polyaniline

2.3. Polypyrrole

2.4. Poly( p -phenylene)s

2.5. Poly( p -phenylene vinylene)

2.6. Polythiophenes

3. Electrical and electronic properties

3.1. Charge carrier transport models

3.1.1. Mott model

3.1.2. Schaefer–Siebert–Roth model

4. Optical property

4.1. Electroluminescence, electrochromic and photochromic effects of conjugated polymers

5. Mechanical properties

5.1. Elasticity and Young's modulus

5.2. Structure–property relationship

6. Applications of conducting polymers

6.2. Corrosion inhibition applications

6.3. Photocatalytic applications

6.4. Biomedical and antimicrobial application

6.5. Electrochemical gas sensors

6.5.1. Major components

6.5.2. Sensing mechanism

6.6. Conducting polymer hydrogels (CPH) for bioelectronics

7. Conclusion and future directions

Conflicts of interest

Supplementary Material

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3D printing of conducting polymers

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