Facile Fabrication of Polyaniline/Graphene Composite Fibers as Electrodes for Fiber-Shaped Supercapacitors

: Graphene ﬁber-based supercapacitors are known as the potential energy resources for wearable/ﬂexible electronics. However, increasing their speciﬁc capacitance and energy density remains a signiﬁcant challenge. This paper indicates a double layer capacitance of the graphene nanosheets accompanied by pseudocapacitive behavior of the polyaniline to prepare composite ﬁbers with high capacitive response. The polyaniline/graphene composite ﬁbers (PANI/GFs) were synthesized by the self-assembled strategy and chemical reduction by HI. The wrinkle architecture of graphene nanosheets and uniform dispersion of the polyaniline are beneﬁcial to increase the internal electroactive sites and provide a stable structure for the composite ﬁbers. The constructed ﬁber-shaped supercapacitors with solid-state electrolyte deliver an excellent areal speciﬁc capacitance of 370.2 mF cm − 2 and an outstanding areal energy density of 12.9 µ W h cm − 2 . The current work reveals the attractive potential of the as-synthesized composite ﬁbers for constructing ﬁber-shaped supercapacitors with distinguished electrochemical performance, which can be applied in future ﬂexible electronics. Graphene composite ﬁbers exhibit potential advantages as ﬁber electrode for wearable energy storage systems, boosting the further application of graphene ﬁbers in prospective ﬂexible/wearable electronic devices.


Introduction
The rapid development of wearable/flexible electronics has tremendously increased the attraction of flexible power supplies/devices that are lightweight and flexible [1][2][3]. Among various flexible power sources, fiber-shaped supercapacitors not only possess these superiorities of lightweight, small, and mechanical flexibility, but also can be easily woven into textiles, highlighting great advantages in the future flexible, portable, and wearable electronics field [4][5][6]. However, compared with lithium ion batteries or traditional supercapacitors, fiber-shaped supercapacitors display much lower specific capacitance and energy density, which impede their widespread application [7,8]. As we know, the energy density of supercapacitors is proportional to its capacitance depending on the intrinsic charge storage capabilities of electrode materials [9,10]. Therefore, much effort has been committed to exploiting new structural electrode materials to construct high electrochemical performance fiber-shaped supercapacitors for wearable/flexible electronic devices.
For fiber-shaped supercapacitors, carbon-based materials are the most commonly utilized as electrodes because of their many characteristics including exceptional electric conductivity, large surface area, lightweight, low-cost, and chemical stability, as well as wide operating temperature range, especially graphene fibers [11,12]. In 2011, Gao and his coworkers exploited graphene oxides as a liquid crystal spinning solution, and first prepared graphene fibers by the wet-spinning method and chemical reduction [13]. Graphene his coworkers exploited graphene oxides as a liquid crystal spinning solution, and firs prepared graphene fibers by the wet-spinning method and chemical reduction [13]. Gra phene fibers have been utilized extensively as flexible electrodes for wearable superca pacitors, exhibiting flexibility, lightweight, and representative double layer capacitor be havior. The charge-storage ability of the supercapacitors based on carbon materials i mainly dominated by the effective specific surface area. However, the graphene fibers ex hibit graphite-like structures because of the strong π-π bonding existing in graphen nanosheets, which results in a low specific surface area and a poor wettability of the elec trolyte [8,14,15]. The limited specific capacitance and poor energy density of the pure gra phene fibers restrict further application in future wearable/flexible electronics [16][17][18] Therefore, some materials with pseudocapacitive properties, for example, transition meta oxides [19][20][21][22], metal sulfides [14,[23][24][25], and conducting polymers [9,[26][27][28], have bee added into graphene fibers or other carbon materials to promote specific capacitance and energy density. Polyaniline is a potential candidate for the high theoretical specific pseu docapacitance and good electrical conductivity [29,30]. Polyaniline is combined with gra phene fibers, increasing the electroactive sites and providing a stable structure of compo site fiber flexible electrodes in electrochemical measurement processes.
In this research, polyaniline/graphene composite fibers (PANI/GFs) were constructed by the self-assembly method and chemical reduction processes. The synthesis processe are shown in Figure 1. The polyaniline obtained by chemical polymerization exists in gra phene fibers, which could impede the aggregation of graphene nanosheets and guarante the uniform distribution of PANI in the composite fibers. These fiber-shaped supercapac itors consisting of PANI/GFs display an outstanding areal specific capacitance of 370.2 m cm −2 and an excellent energy density of 12.9 μW h cm −2 when the power density is up t 25.3 μW cm −2 on PVA/H2SO4 gel electrolyte. Graphene composite fibers exhibit potentia advantages as fiber electrode for wearable energy storage systems, boosting the furthe application of graphene fibers in prospective flexible/wearable electronic devices.

Preparation of Polyaniline
Here, 1 mmol aniline monomer was poured into a 50 mL 1M HCl solution by stirrin for 5 min, and ammonium peroxydisulfate (APS) was dissolved in 1 M HCl solution t obtain a uniform APS solution. Then, aniline solution was slowly poured into the AP solution above by continuous stirring and the chemical reaction was conducted at room temperature for 12 h; the molar ratio of APS to aniline was 1:1. The obtained polyanilin (PANI) nanomaterials were cleaned by the deionized water under high-speed centrifuga processes. The formed PANI suspension was dried by oven at 60 °C and the weight per centages of PANI were calculated to be 8%.

Preparation of Polyaniline
Here, 1 mmol aniline monomer was poured into a 50 mL 1M HCl solution by stirring for 5 min, and ammonium peroxydisulfate (APS) was dissolved in 1 M HCl solution to obtain a uniform APS solution. Then, aniline solution was slowly poured into the APS solution above by continuous stirring and the chemical reaction was conducted at room temperature for 12 h; the molar ratio of APS to aniline was 1:1. The obtained polyaniline (PANI) nanomaterials were cleaned by the deionized water under high-speed centrifugal processes. The formed PANI suspension was dried by oven at 60 • C and the weight percentages of PANI were calculated to be 8%.

Preparation of Polyaniline/Graphene Composite Fibers
All the chemicals were of analytical grade and utilized as received, without further purification. As shown in Figure 1, the synthesis of polyaniline/graphene composite fibers (PANI/GF) had two steps: first, the graphite oxides (GO) suspension was prepared by a modified Hummers method, which maintains excellent stability at room temperature. Then, 10 mL GO solution of 7 mg mL −1 was placed in an ultrasonic bath for 30 min, ensuring the good uniformity of the solution. Further, 0, 0.1, 0.2, or 0.3 g PANI suspensions were mixed with GO solution and mixed under ultrasonication for another 1.5 h. Then, 0.1 g reducing agent was added into the GO and PANI suspension to obtain homogeneous mixtures. Second, the mixture suspension was injected into a PTFE tube, which was sealed, and maintained at 90 • C for 2 h to preliminarily form gel-fibers, and then at 120 • C until fibers fully formed. The formation of PANI/GF was mainly ascribed to the capillary forces and surface tension guided graphene nanosheet interactions. The fabricated fibers were named as GF, PANI/GF1, PANI/GF2, and PANI/GF3, respectively, according to different adding amounts of PANI nanomaterials (0, 0.1, 0.2, and 0.3 g PANI suspension with 8% weight percentages).

Characterization
The morphologies of graphene-based fibers were characterized using scanning electron microscopy (SEM, JEOL JSM-7600F). The TGA (STA 449F3 + ASC) analysis was conducted under a nitrogen atmosphere with a heating rate of 10 • C/min, increasing between 35 • C and 1000 • C. Fourier transform infrared spectra (FTIR, Nicolet Nexus 670) were recorded from 400 to 4000 cm −1 . Additionally, other information of the samples was observed via Raman (JY HR800), XPS (ESCALAB 250), and XRD.

Construction of Fiber-Shaped Supercapacitors and Electrochemical Measurements
The symmetric fiber-shaped supercapacitor was constructed via covering with gel-like solid-state electrolyte (PVA/H 2 SO 4 ) on two parallel PANI/GF electrodes fixed on a flexible PDMS substrate, and the use of a gel-like electrolyte can protect the electrodes from short circuit. The PVA/H 2 SO 4 gel electrolyte was prepared by adding 12 g PVA and 12 g H 2 SO 4 into 120 mL deionized water, and the mixed solution was heated at 95 • C accompanied by continuously stirring until the electrolyte became clear.
For the assembled fiber-shaped supercapacitors, a CHI660E electrochemical workstation was used to evaluate the electrochemical performance including CV, EIS, and galvanostatic charge/discharge cycling. The areal specific capacitance of the flexible supercapacitor was obtained from the following equation: = 4I∆t ∆VA , where I, ∆t, ∆V, and A (cm 2 ) are the discharge current (mA), the discharge time (s), the voltage range (V), and the total surface area of two electrodes, respectively [31]. The energy density (E) and power energy (P) are usually calculated by equations of E = CV 2 8 and = E ∆t , where C (mF cm −2 ), V(V), and ∆t (s) represent the areal specific capacitance, the operated voltage, and the discharge time, respectively [32].

Results and Discussion
The amount of PANI in composite fibers is a significant factor for the electrochemical performance of the flexible supercapacitors. This work reports composite fibers with different loading amounts of PANI. The PANI/GF prepared with 0.2 g PANI suspension displays the best electrochemical performance, and the following characterizations are obtained from the composite fibers with 0.2 g PANI suspension. Figure 2 shows the TGA profiles of PANI, GF, and PANI/GF. The mass decreasing around 100 • C in the PANI curve is ascribed to the loss of the H 2 O molecular, and a sharp change at about 500 • C exists in the TGA curve of the PANI [33][34][35][36]. The pure PANI still maintains 45% weight at 1000 • C, suggesting the carbonization of phenyl [37]. After the same procedure, the weight loss of the GF and PANI/GF is approximately 35.6% and 39.2%, respectively. Therefore, the corresponding PANI weight ratio of PANI/GF is 18.6%. This result is consistent with that calculated by adding the amount of PANI in the synthesis process. loss of the GF and PANI/GF is approximately 35.6% and 39.2%, respectively. Therefore, the corresponding PANI weight ratio of PANI/GF is 18.6%. This result is consistent with that calculated by adding the amount of PANI in the synthesis process. In Figure 3, SEM shows the detailed morphology and architecture of the as-synthesized GF and PANI/GF. The diameter of GF is approximately 160 μm, and the GF possess a coarse surface with a wrinkled and crumpled architecture (Figure 3a,b). The cross-section morphology of GF exhibits a hierarchical structure ( Figure 3c). These morphological and structure features help in the transportation and storage of massive electrons, which can fully utilize the electrical double layer capacitance to improve electrochemical performance. In Figure 3d-f, PANI/GF exhibits approximate surface morphology and architecture at the microscale compared with GF. PANI nanomaterials can be found on the surface and cross section of the composite fibers, and the existence of PANI nanomaterials in the composite fibers changes the hierarchical structure (Figure 3g,h). Energy-dispersive X-ray spectroscopic element distribution maps of C, N, and O clearly verify the uniform distribution of the PANI nanomaterials in the composite fibers, as shown in Figure 3i. In Figure 3, SEM shows the detailed morphology and architecture of the as-synthesized GF and PANI/GF. The diameter of GF is approximately 160 µm, and the GF possess a coarse surface with a wrinkled and crumpled architecture (Figure 3a,b). The cross-section morphology of GF exhibits a hierarchical structure (Figure 3c). These morphological and structure features help in the transportation and storage of massive electrons, which can fully utilize the electrical double layer capacitance to improve electrochemical performance.
In Figure 3d-f, PANI/GF exhibits approximate surface morphology and architecture at the microscale compared with GF. PANI nanomaterials can be found on the surface and cross section of the composite fibers, and the existence of PANI nanomaterials in the composite fibers changes the hierarchical structure (Figure 3g,h). Energy-dispersive Xray spectroscopic element distribution maps of C, N, and O clearly verify the uniform distribution of the PANI nanomaterials in the composite fibers, as shown in Figure 3i. loss of the GF and PANI/GF is approximately 35.6% and 39.2%, respectively. Therefore, the corresponding PANI weight ratio of PANI/GF is 18.6%. This result is consistent with that calculated by adding the amount of PANI in the synthesis process. In Figure 3, SEM shows the detailed morphology and architecture of the as-synthesized GF and PANI/GF. The diameter of GF is approximately 160 μm, and the GF possess a coarse surface with a wrinkled and crumpled architecture (Figure 3a,b). The cross-section morphology of GF exhibits a hierarchical structure (Figure 3c). These morphological and structure features help in the transportation and storage of massive electrons, which can fully utilize the electrical double layer capacitance to improve electrochemical performance. In Figure 3d-f, PANI/GF exhibits approximate surface morphology and architecture at the microscale compared with GF. PANI nanomaterials can be found on the surface and cross section of the composite fibers, and the existence of PANI nanomaterials in the composite fibers changes the hierarchical structure (Figure 3g,h). Energy-dispersive X-ray spectroscopic element distribution maps of C, N, and O clearly verify the uniform distribution of the PANI nanomaterials in the composite fibers, as shown in Figure 3i. In Figure 4, there are two characteristic peaks of D and G associated with graphene nanosheets in the Raman curves of GO, GF, and PANI/GF, which are ascribed to the reduction in the size of the in-plane vibration of sp 2 carbon atoms and the K-point phonons of A 1g symmetry [38,39]. The information corresponding to carbon structural changes can be obtained from Raman spectra [40]. For the PANI/GF, besides the D and G bands of GF, the typical peaks at 575 cm −1 and 1169 cm −1 relate to the out-of-plane C-H deformation and C-H binding of the quinoid ring, respectively [25,32,35]. In Figure 4, there are two characteristic peaks of D and G associated with graphene nanosheets in the Raman curves of GO, GF, and PANI/GF, which are ascribed to the reduction in the size of the in-plane vibration of sp 2 carbon atoms and the K-point phonons of A1g symmetry [38,39]. The information corresponding to carbon structural changes can be obtained from Raman spectra [40]. For the PANI/GF, besides the D and G bands of GF, the typical peaks at 575 cm −1 and 1169 cm −1 relate to the out-of-plane C-H deformation and C-H binding of the quinoid ring, respectively [25,32,35].  Figure 5, the XRD patterns of GO, GF, and PANI/GF are analyzed. GO has a typical diffraction peak (001) located at 11.6°, while GF shows a characteristic peak at 25.5° related to the (002) plane of stacked graphene sheets [29,41]. The XRD pattern of PANI/GF and GF indicate similar features, and the (002) diffraction peak reveals the superimposed intensity of GF and PANI, which is due to a typical peak near 25° for both [25,42].   Figure 5, the XRD patterns of GO, GF, and PANI/GF are analyzed. GO has a typical diffraction peak (001) located at 11.6 • , while GF shows a characteristic peak at 25.5 • related to the (002) plane of stacked graphene sheets [29,41]. The XRD pattern of PANI/GF and GF indicate similar features, and the (002) diffraction peak reveals the superimposed intensity of GF and PANI, which is due to a typical peak near 25 • for both [25,42]. duction in the size of the in-plane vibration of sp 2 carbon atoms and the K-point ph of A1g symmetry [38,39]. The information corresponding to carbon structural chang be obtained from Raman spectra [40]. For the PANI/GF, besides the D and G bands the typical peaks at 575 cm −1 and 1169 cm −1 relate to the out-of-plane C-H deformati C-H binding of the quinoid ring, respectively [25,32,35].  Figure 5, the XRD patterns of GO, GF, and PANI/GF are analyz has a typical diffraction peak (001) located at 11.6°, while GF shows a characterist at 25.5° related to the (002) plane of stacked graphene sheets [29,41]. The XRD pat PANI/GF and GF indicate similar features, and the (002) diffraction peak reveals perimposed intensity of GF and PANI, which is due to a typical peak near 25° fo [25,42].  Additionally, high-resolution XPS of the C1s and N1s peaks can show electronic states between elements. In Figure 6a, the peaks at 284.7, 286, 287, and 288.3 eV were assigned to the C-C in the aromatic rings, C-O of epoxy, C=O, and O=C-OH groups, respectively [43]. Compared with the GO spectrum, the oxygen content in GF and PANI/GF are decreased significantly (Figure 6b,c). As shown in Figure 6d, the N1s of PANI/GF contains three kinds electronic states of the quinoid imine (-N=) at 398.5, the benzenoid amine (-NH-) at 399.1, and the nitrogen cationic radical (N + ) at 400.5 eV, respectively [26,44]. The XPS results and the XRD spectra indicate the PANI structure in the composite fibers.

As shown in
Appl. Sci. 2021, 11, x FOR PEER REVIEW 6 o Additionally, high-resolution XPS of the C1s and N1s peaks can show electro states between elements. In Figure 6a, the peaks at 284.7, 286, 287, and 288.3 eV were signed to the C-C in the aromatic rings, C-O of epoxy, C=O, and O=C-OH groups, resp tively [43]. Compared with the GO spectrum, the oxygen content in GF and PANI/GF decreased significantly (Figure 6b,c). As shown in Figure 6d, the N1s of PANI/GF conta three kinds electronic states of the quinoid imine (-N=) at 398.5, the benzenoid amin NH-) at 399.1, and the nitrogen cationic radical (N + ) at 400.5 eV, respectively [26,44]. XPS results and the XRD spectra indicate the PANI structure in the composite fibers. We evaluated in detail the electrochemical properties of fiber-shaped flexible sup capacitors assembled by covering the gel-state polyvinyl alcohol supported H2SO4 e trolyte on the as-synthesized graphene-based composite fibers in a two-electrode syst Figure 7a-c show cyclic voltammogram (CV) profiles of the flexible supercapacitors c structed by GF and PANI/GF, which are measured in a narrow electrochemical wind of 0-0.8 V at various scan rates of 10 mVs −1 , 20 mVs −1 , 30 mVs −1 , 40 mVs −1 , and 50 mV The CV analysis is beneficial to further understanding of the electrochemical behavior a stability during electrochemical measurement processes [45]. As shown in Figure 7 with scan rates increasing, the CV curves of the GF also display an approximate rect gular shape (Figure 7a), indicating apparent electrochemical double-layer capacitive havior. Figure 7b shows the typical redox peaks and rectangle shape in the CV curve PANI/GF, and the capacitance of the as-constructed flexible energy storage devices c sists of pseudocapacitance and double-layer capacitance [43]. Notably, the area of the curves of PANI/GF almost increases with the scan rate in the proportion, revealing t the specific capacitance of PANI/GF is not influenced by the scan rate. Figure 7c displ the CV profiles of GF and PANI/GF at 10 mVs −1 . The CV profiles of PANI/GF displa larger integrated CV area with obvious redox peaks compared with those of GF, indi ing faster ion diffusion and higher energy storage properties. The enhanced electroche ical performance of PANI/GF is mainly ascribed to the more internal electroactive s and the structural stability of PANI/GF [46]. In addition, Figure 7d shows EIS of GF a We evaluated in detail the electrochemical properties of fiber-shaped flexible supercapacitors assembled by covering the gel-state polyvinyl alcohol supported H 2 SO 4 electrolyte on the as-synthesized graphene-based composite fibers in a two-electrode system. Figure 7a-c show cyclic voltammogram (CV) profiles of the flexible supercapacitors constructed by GF and PANI/GF, which are measured in a narrow electrochemical window of 0-0.8 V at various scan rates of 10 mVs −1 , 20 mVs −1 , 30 mVs −1 , 40 mVs −1 , and 50 mVs −1 . The CV analysis is beneficial to further understanding of the electrochemical behavior and stability during electrochemical measurement processes [45]. As shown in Figure 7a,b, with scan rates increasing, the CV curves of the GF also display an approximate rectangular shape (Figure 7a), indicating apparent electrochemical double-layer capacitive behavior. Figure 7b shows the typical redox peaks and rectangle shape in the CV curves of PANI/GF, and the capacitance of the as-constructed flexible energy storage devices consists of pseudocapacitance and double-layer capacitance [43]. Notably, the area of the CV curves of PANI/GF almost increases with the scan rate in the proportion, revealing that the specific capacitance of PANI/GF is not influenced by the scan rate. Figure 7c displays the CV profiles of GF and PANI/GF at 10 mVs −1 . The CV profiles of PANI/GF display a larger integrated CV area with obvious redox peaks compared with those of GF, indicating faster ion diffusion and higher energy storage properties. The enhanced electrochemical performance of PANI/GF is mainly ascribed to the more internal electroactive sites and the structural stability of PANI/GF [46]. In addition, Figure 7d shows EIS of GF and PANI/GF to evaluate the ion transport mechanisms, which can indicate the contact between the electrode and electrolyte. In the high frequency region, the x-intercept of PANI/GF is significantly smaller than that of GF. This is because the doping of conductive polymer increases its conductivity and reduces the corresponding equivalent resistance value. The low frequency curve of PANI/GF has a larger slope [9,10,47]. The greater slope of the curve of PANI/GF implies better capacitive behavior and fast ion migration capability, improving the electrochemical performance [17,32,48].
Appl. Sci. 2021, 11, x FOR PEER REVIEW PANI/GF to evaluate the ion transport mechanisms, which can indicate the con tween the electrode and electrolyte. In the high frequency region, the x-inter PANI/GF is significantly smaller than that of GF. This is because the doping of con polymer increases its conductivity and reduces the corresponding equivalent res value. The low frequency curve of PANI/GF has a larger slope [9,10,47]. The greate of the curve of PANI/GF implies better capacitive behavior and fast ion migratio bility, improving the electrochemical performance [17,32,48].   Figure 8d.
To evaluate the practical application of PANI/GF-based supercapacitors, th term cycling stability at a current density of 0.35 mA cm −2 under continuous char charge operation is shown in Figure 9a. Satisfactorily, PANI/GF exhibits a steadily uous charge/discharge process for 2365 cycles without any noticeable degradation maintains a capacitance retention of 96%. In Figure 9b, surface (Ι-Π) and cross-se (Ш-ΙѴ) SEM images of PANI/GF images are obtained after a long-term cycling te little gel-like electrolyte is found on the surface of PANI/GF. The SEM images exh proximate surface morphology and architecture at the microscale compare   Figure 8d.
To evaluate the practical application of PANI/GF-based supercapacitors, the long-term cycling stability at a current density of 0.35 mA cm −2 under continuous charge/discharge operation is shown in Figure 9a. Satisfactorily, PANI/GF exhibits a steadily continuous charge/discharge process for 2365 cycles without any noticeable degradation, which maintains a capacitance retention of 96%. In Figure 9b, surface (I-Π) and cross-sectional (III-IV) SEM images of PANI/GF images are obtained after a long-term cycling test. The little gel-like electrolyte is found on the surface of PANI/GF. The SEM images exhibit approximate surface morphology and architecture at the microscale compared with PANI/GF before cycling measurement, which indicates excellent cycling stability of PANI/GF-based supercapacitors.
Appl. Sci. 2021, 11, x FOR PEER REVIEW PANI/GF before cycling measurement, which indicates excellent cycling stabi PANI/GF-based supercapacitors.  The fiber-shaped supercapacitors display good specific capacitance and excell ergy density. Many publications report pure graphene fibers or conducting polym phene composite fibers as electrode materials for flexible supercapacitors, and th summarized in Table 1. In brief, the fiber-shaped supercapacitors construct PANI/GF and gel-like electrolyte indicate good electrochemical properties because more internal electroactive sites, the designed wrinkling, and the stable architectu tween PANI and graphene sheets in composite fibers. This work will provide a fabr method and theory foundation for high-performance graphene composite fiber flexible supercapacitors for future wearable electronic devices. Appl. Sci. 2021, 11, x FOR PEER REVIEW 8 PANI/GF before cycling measurement, which indicates excellent cycling stabilit PANI/GF-based supercapacitors.  The fiber-shaped supercapacitors display good specific capacitance and excellen ergy density. Many publications report pure graphene fibers or conducting polymer phene composite fibers as electrode materials for flexible supercapacitors, and these summarized in Table 1. In brief, the fiber-shaped supercapacitors constructed PANI/GF and gel-like electrolyte indicate good electrochemical properties because o more internal electroactive sites, the designed wrinkling, and the stable architecture tween PANI and graphene sheets in composite fibers. This work will provide a fabrica method and theory foundation for high-performance graphene composite fiber-b flexible supercapacitors for future wearable electronic devices. The fiber-shaped supercapacitors display good specific capacitance and excellent energy density. Many publications report pure graphene fibers or conducting polymer/graphene composite fibers as electrode materials for flexible supercapacitors, and these are summarized in Table 1. In brief, the fiber-shaped supercapacitors constructed by PANI/GF and gel-like electrolyte indicate good electrochemical properties because of the more internal electroactive sites, the designed wrinkling, and the stable architecture between PANI and graphene sheets in composite fibers. This work will provide a fabrication method and theory foundation for high-performance graphene composite fiber-based flexible supercapacitors for future wearable electronic devices.

Conclusions
In summary, this paper proposes a double layer capacitance of the chemically reduced graphene oxides accompanied by pseudocapacitive behavior of polyaniline to produce composite fibers with a high capacitive response. We synthesized polyaniline/graphene composite fibers (PANI/GFs) by the self-assembly method and chemical reduction processes. The composite fiber-shaped supercapacitors with solid-state electrolyte deliver high area specific capacitance of 370.2 mF cm −2 and energy density of 12.9 µW h cm −2 at the power density of 25.3 µW cm −2 , which is mainly attributed to the crumpled morphology, the more internal electroactive sites, and the structural stability of the polyaniline in the composite fibers. The current work highlights the excellent potential of the as-constructed fiber-shaped supercapacitors for wearable/flexible electronic devices.

Conflicts of Interest:
The authors declare no conflict of interest.