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Modifying Reduced Graphene Oxide by Conducting Polymer Through a Hydrothermal Polymerization Method and its Application as Energy Storage Electrodes
Nanoscale Research Letters volume 14, Article number: 226 (2019)
We report chemical in situ deposition of conducting polymer poly (3,4-ethylenedioxythiophene) (PEDOT) on reduced graphene oxide (rGO) nanosheets through a simple hydrothermal polymerization method. The functional groups on graphene oxide (GO) were directly employed as an oxidant to trigger the polymerization of 3,4-ethylenedioxythiophene (EDOT), and the GO nanosheets were reduced into rGO accordingly in an aqueous environment. Well anchoring of ultrathin PEDOT on rGO through this oxidant-free method was confirmed by UV-Vis spectrum, FT-IR spectrum, SEM, and TEM analysis. The obvious enhancement of conductivity was observed after the covering of PEDOT on rGO, and this composite showed high conductivity about 88.5 S/cm. The electrochemical performance results revealed that rGO/PEDOT composite electrode exhibits high specific capacitance about 202.7 F/g. The good synergetic effect between PEDOT and rGO also makes sure highly stable reversibility of composite electrode during charging/discharging process, and more than 90% initial capacitance retains after 9000 times cycles. In addition, the electrode based on rGO/PEDOT deposited on the cotton fabric shows excellent flexible ability with the evidence that 98% of the initial capacitance of electrode maintained after three thousands of free bending, which shows promising energy storage performance for flexible devices.
In this paper, as an easy and facile way, the functional groups on graphene oxide (GO) were directly employed as an oxidizer to trigger the polymerization of 3,4-ethylenedioxythiophene (EDOT) and the GO nanosheets were reduced into rGO accordingly in an aqueous environment. The high specific capacitance and high conductivity of composite electrode were achieved through this simple method. The composite electrode also showed good cycling stability and flexibility, which exhibited a promising future to construct high-performance flexible devices.
In recent years, conducting polymers (CPs) that are highly conductive and electrochemically active have been focused on some promising applications such as solar cell [1,2,3], sensors [4,5,6,7,8], energy storage devices [9,10,11], and bioelectronics [12,13,14]. The energy storage device, such as supercapacitors, has employed the conducting polymer as high-efficiency electrodes, which can afford high pseudocapacitance due to its reversible oxidation/reduction process in electrolytes [15,16,17,18]. In order to obtain conducting polymer-based electrochemical electrode with high stability, incorporating conducting polymer with carbon materials and metal oxide materials with nanostructure has been extensively investigated [19,20,21,22]. Due to the highly stable performance of these materials, the significant improvement of electrochemical stability of conducting polymer has been achieved, which also results in constructing devices with excellent energy storage performance [23, 24]. In these aspects, incorporating conducting polymer with carbon nanomaterials is more suitable to obtain composite electrodes with high energy density and power density simultaneously. Moreover, compared with inorganic materials, the excellent flexibility of conducting polymer also benefits for constructing flexible electrode, even the flexible devices for wearable electronic systems [25,26,27,28,29].
The conducting polymer/carbon nanomaterial electrodes exhibit high energy density due to the combination of pseudocapacitance and electric double layer capacitance (EDLC) [15, 30,31,32]. Hence, the optimized synergistic effect between two components is vital to obtain a composite electrode with high specific capacitance and high stability, which means that the electrode performance depends greatly on the preparation method. In order to obtain heterostructured structures, different methods, such as physical mixing [33,34,35], electrochemical polymerization , and chemical in situ polymerization with oxidant [37,38,39,40], were employed to prepare the conducting polymer and its composite as supercapacitor electrodes. As for the physical mixing method, well distribution and alloying of two components need to be considered carefully to avoid the phase separation during the long time cycling. As well as chemical in situ polymerization with oxidant in a solution or gaseous environment, due to the polymerization of monomer on carbon nanomaterials with a thermodynamic process, excellent synergistic effect has been confirmed in these composite materials [41, 42]. However, both these in situ polymerization methods are suffered with difficulty to wash out the excess oxidant, which will take great influence on the morphology and related performance of as-prepared composites [43, 44]. Therefore, it has great demands to prepare conducting polymer/carbon nanomaterials with an oxidant-free method, which will produce composite through a simple and facile way, coupling the advantages of carbon nanomaterials and conducting polymer.
In this paper, based on solution processability of GO and functional groups on GO sheets, conducting polymer poly (3,4-ethylenedioxythiophene) (PEDOT) was anchoring on GO sheets through a simple hydrothermal polymerization method. The functional groups on GO sheets play a role as an oxidant to trigger the polymerization of 3,4-ethylenedioxythiophene (EDOT) monomer, and a reduced graphene oxide (rGO)/PEDOT nanocomposite was obtained. Due to this oxidant-free method, the ultrathin and ultramolecular modification of conducting polymer on rGO nanosheets was achieved. The resultant rGO/PEDOT nanocomposite has been studied as promising electrochemical electrode materials for supercapacitor applications.
Materials and Methods
Graphite flakes used for GO preparation were purchased from Sigma-Aldrich. GO was synthesized from natural graphite flakes prepared through Hummer’s method . For chemical in situ polymerization, EDOT monomer was purchased from Bayer Company. Other chemical reagents with analytical grade were purchased from Chengdu Kelong Chemical Reagent Company and used as received.
Preparation of rGO/PEDOT Nanocomposite
Fifty microliters of EDOT monomer was introduced into 50 ml DI water with magnetic stirring for 2 h to prepare EDOT solution. The stable GO dispersion was prepared by introducing 1.5 g of GO sheets into 30 ml DI water and subjected to magnetic stirring for 1 h followed by centrifugation at 2500 rpm. Subsequently, 10 ml EDOT solution was dropwise into the GO solution with magnetic stirring at 60 °C for 6 h, and then, the reaction temperature was increased to 90 °C at least 2 h for the further polymerization of EDOT and reduction of GO (rGO/PEDOT1). The schematic diagram of EDOT polymerization and reduction of GO is presented in Fig. 1. In order to compare the influence of GO contents on the performance of obtained composite, different masses of GO were added into DI water for the hydrothermal reaction. So, as mentioned in the preparation process above, all the experimental parameters are the same except the GO mass added into DI water. Accordingly, a 3 g, a 4 g, and a 4.5 g GO sheets produced the rGO/PEDOT2, rGO/PEDOT3, and rGO/PEDOT4 composites, respectively. The pure rGO was obtained through the hydrothermal method mentioned above.
Characterization and Electrochemical Performance Test
Surface morphology of GO and rGO/PEDOT was investigated using a scanning electron microscope (SEM, Hitachi, Model S-2400). UV-Vis spectrum of the film was characterized by a UV-1700 spectrometer (SHIMADZU). FT-IR spectrum was obtained with an ALPHA analysis instrument (Germany). For the conductivity test, the obtained rGO and composite powder were compressed into a cylinder shape with the size of 5 mm (radius) × 2 mm (height) and tested in room temperature. Electrical conductivity was tested by a SX193 Four-Probe testing system (Baishen, Suzhou, China). XPS spectra were carried out by using an Escalab 250Xi photoelectron spectrometer (Thermo Fisher Scientific, USA). Raman spectra were recorded on an Alpha300 model with a 532-nm laser (WITec, Germany). Electrochemical performance was investigated by using a CHI600 electrochemistry workstation (Chenhua, Shanghai, China). Cyclic voltammetry (CV), galvanostatic charge–discharge (GCD), and electrochemical impedance spectroscopy (EIS) were performed with 1 mol/L H2SO4 aqueous electrolyte using a platinum sheet as the counter electrode and Ag/AgCl as the reference electrode. All the measurements were performed at ambient temperature.
Results and Discussion
The UV-Vis spectrum of GO, hydrothermal-treated rGO, and hydrothermal-polymerized rGO/PEDOT is shown in Fig. 2. The pure GO shows two main absorption bands, and the maximum peak presents in 225 nm, attributing to the π→π* transition of C=C bond. A weak absorption peak at 297 nm resulting from the n→π* transition of C=O bond is also observed . After hydrothermal treatment, the obtained rGO shows different characteristic peaks with the evidence that the 225-nm peak shifts to 241 nm and the 297-nm peak disappears. This result indicates that the hydrothermal treatment partly removes the functional groups on the GO sheets. The color of GO solution also changes from the yellow to deep black after this hydrothermal treatment (as shown in Fig. 1). From Fig. 2, we can see that rGO/PEDOT composite shows an absorption peak at 270 nm, which comes from the π→π* transition of rGO . Furthermore, a broad absorption peak from 450 nm to near-infrared wavelength appears in the spectrum due to the typical absorption of polarons and bipolarons in polymerized PEDOT . After the addition of monomer EDOT into GO solution, hydrothermal treatment triggers the polymerization of EDOT and the GO is reduced to rGO accordingly, and this oxidant-free polymerization method produces the rGO/PEDOT composite in an aqueous environment successfully. It also can be seen from Fig. 2 that with the increase of GO mass during the hydrothermal polymerization, the obtained rGO/PEDOT shows more obvious shift of absorption peak, rising from π→π* transition to longer wavelength than pure rGO. This result reveals that more functional groups in GO were employed to trigger the polymerization of EDOT in the oxidant-free condition.
The FT-IR and Raman analysis were employed to further confirm what functional groups trigger the polymerization of EDOT monomer during the hydrothermal treatment. Figure 3a shows the FT-IR spectrum of GO, hydrothermal-treated rGO, and different rGO/PEDOT composites. The absorption peaks at 3395 cm−1 and 1726 cm−1 come from the stretching vibration of C–OH bond and C=O bond located at GO edge. The 1620 cm−1 peak represents the vibration absorption of C=C bond and 1420 cm−1 peak rising from the deformed –OH bond on the GO plane . The 1188 cm−1 peak results from the vibration of C–O bonds . After the hydrothermal treatment, the peaks located at 3395 cm−1 and 1419 cm−1 were weakened obviously, indicating the partly removal of the –OH group. The peak density located at 1726 cm−1 and 887 cm−1 resulted from –OH and C–O–C absorption, which is also weaken distinctly and even disappears, indicating that the above functional groups were reduced and are realized as possible active sites for the polymerization of EDOT [49, 50]. The reduction of GO is also confirmed with the evidence that the peak density of 1571 cm−1 enhances obviously, resulting from the C=C bond absorption, which indicates the recovery of plain conjugated structure of rGO .
After the hydrothermal treatment of EDOT/GO solution, the FT-IR spectrum of composite shows characteristic peaks of PEDOT polymer. It can be seen that the spectrum of composite shows series peaks at 687 cm−1, 839 cm−1, 930 cm−1, and 980 cm−1, which rise from the vibration of C-S bond in PEDOT [52, 53]. In addition, the peaks located at 1026 cm−1, 1137 cm−1, and 1195 cm− 1 were also observed due to the stretching absorption of C–O–C bond in alkylenedioxy [54, 55]. Therefore, comparing the FT-IR spectrum of GO with rGO/PEDOT, the distinct disappearance of –OH (located at 1420 cm−1) and C–O–C (located at 887 cm−1) absorption was observed, indicating that these two functional groups trigger the polymerization of EDOT primarily during hydrothermal treatment .
The Raman spectrum of GO, hydrothermal-treated rGO, and hydrothermal-polymerized rGO/PEDOT is shown in Fig. 3b. Compared with pure GO and rGO, the rGO/PEDOT shows new characteristic peaks at 1427 cm−1 and 1501 cm−1, and these peaks are attributed to the symmetric and asymmetric stretching vibration of C=C bond in PEDOT. The peaks located at 1361 cm−1 and 1267 cm−1 are attributed to Cβ–Cβ and Cα–Cα of thiophene ring. The peak located at 987 cm−1 rises from the deformed vibration of oxyethylene ring . Two peaks at 2856 cm−1 and 2939 cm−1 are attributed to doped PEDOT [58,59,60].
In order to further investigate the obtained composite, the XPS analysis is utilized to confirm the reduction of GO and polymerization of EDOT monomer. Figure 4 shows the full XPS spectra of the composite after the hydrothermal treatment. It clearly shows that only C, S, and O elements distribute in the composite. The peak at 980 eV is corresponding to the Auger peak of O element, and the peak at 529~537 eV is attributed to the O1s. The peaks at 229 eV and 165 eV result from S1s and S2p, respectively. According to the relative contents of C, O, and S in composite, the calculated atom ratio of C/O, C/S, and O/S is 3.42, 14.95, and 4.38, respectively. It has been found that the actual atom ratio of C/S and O/S is higher than pure PEDOT (10.33 and 4.07). We concluded that the -OH and C-O-C trigger the polymerization of EDOT monomer primarily, and some other functional groups in GO will not be reduced in this process. So, the residual groups in rGO will increase the C and S atom ratio accordingly.
Figure 4 b, c, and d show the fitting C1s, O1s, and S2p peaks of rGO/PEDOT characterized by XPS. In C1s spectra, the high-intensity peak located at 284.8 eV is attributed to the sp2 hybridization in C–C/C=C bonds . The peaks located at 285.8 eV and 288.8 eV rise from the C–S bond in PEDOT and unremoved carboxyl, respectively. The peak present in 286.7 eV results from the C-O-C bond in thiophene ring. As for O1s peaks, the peak located at 533.1 eV is attributed to the epoxy group and C–O–C bond in PEDOT, and peaks at 531.8 eV and 533.7 eV come from the unremoved carboxyl and carbonyl groups at rGO edge. The fitting S2p spectra show two peaks at 163.9 eV and 165.1 eV, which result from the S2p3/2 and S2p1/2 spinning peaks in C–S–C of PEDOT . Moreover, it has been found that compared with the XPS spectrum of pure rGO obtained through hydrothermal method , the shift of binding energy about 0.6 eV was observed in composite rGO/PEDOT, and we attribute this to the interaction between the rGO and polymerized PEDOT, which is consistent with the FT-IR results. Combining the FT-IR and XPS analysis, we can further confirm that the oxhydryl and epoxy groups in GO sheets act as primary active sites triggering the polymerization of EDOT monomer, and rGO composite modified by conducting polymer was prepared through simple oxidant-free hydrothermal polymerization method. From the results above, we tentatively explain the polymerization mechanism. For example of C-O-C groups, acting as polymerization trigger at the water bath heating environment, the C-O bond in the GO ring begins to break, making the O atom negatively charged, and the C-H bond in the EDOT begins to break simultaneously. Therefore, under the electrostatic action, the unpaired free electrons in O atom of GO ring oxygen group attract the broken H+ from EDOT monomer. Accordingly, an O-H bond at the position of the epoxy group is formed and the EDOT monomer becomes EDOT− radical. By combining with two H+ ions, the O atom in the epoxy group breaks away from the GO to form a water molecule, and the new EDOT molecule becomes EDOT− radical again. After this step, the EDOT radical binds to a new neutral EDOT molecule and EDOT dimer radical is formed. At the same time, other EDOT monomers continue to combine with GO and GO is gradually reduced, accompanied by water generation. Then, the EDOT dimer radicals formed by step 2 move to the epoxy group in GO due to electrostatic interaction, then PEDOT with high polymerization degree is formed. The total schematic reaction illustration is shown in Fig. 5. Moreover, a possible connection of the graphene sheets by the EDOT binder through a redox reaction would also improve the conductive performance of composite.
Figure 6 shows the SEM images of hydrothermal-treated rGO and rGO/PEDOT. After the hydrothermal treatment, the obtained rGO exhibits the typical wrinkle morphology (as shown in Fig. 6b), which shows no distinct difference to the GO sheets (as shown in Fig. 6a). As for rGO/PEDOT composite, the morphology with rGO sheets covered by PEDOT particle is presented (as shown in Fig. 6c), which is also confirmed by the TEM analysis (as shown in Fig. 6d). These results reveal that the PEDOT particles are successfully anchored on rGO sheets through an oxidant-free hydrothermal polymerization method. The EDS analysis also confirms the anchoring of PEDOT layer on rGO sheets with the evidence that the S and O element distribution is presented in the composite layer.
Due to the reduction of GO into rGO and anchoring highly conductive PEDOT on rGO sheets, the obtained rGO/PEDOT composite would be beneficial for enhanced conductivity. Table 1 shows the conductivity of GO, rGO, and rGO/PEDOT after the hydrothermal treatment. An obvious enhancement of conductivity is achieved after the hydrothermal stirring, indicating the partly reduction of GO into rGO. Moreover, after the hydrothermal reaction with the addition of EDOT monomer, the obtained composite shows the drastic enhancement of conductive capability. Compared with hydrothermal-treated rGO, almost 4 orders of magnitude of conductivity increase are observed in rGO/PEDOT, due to the thorough reduction of GO and covering of highly conductive PEDOT on rGO sheets. Table 1 also indicates that the mass ratio of GO shows distinct influence on the conductive performance of obtained composite and an optimized addition of 4 g GO results in highest conductivity, which results from efficient polymerization of EDOT and anchoring of PEDOT on rGO.
This highly conductive composite can be deposited on different substrate easily through spraying or spin-coating methods as electrode materials and the electrochemical performances are evaluated. Figure 7 shows the cyclic voltammetry (CV) curves of hydrothermal-treated rGO and hydrothermal-polymerized rGO/PEDOT electrodes (Fig. 7a–d). It can be seen that a distinct increase of CV area was achieved after the modification of PEDOT on rGO sheets. Both the pseudocapacitance of PEDOT and electric double layer capacitance (EDLC) of rGO attribute to the total capacitance of composite electrodes. With the increase of scanning rate, the relative increase of CV cure area is observed, indicating the excellent capacitance performance of composite electrodes. Figure 7e shows the CV curves of rGO/PEDOT composite electrodes prepared with different GO/EDOT mass ratios. It has been shown that with the increase of GO contents at a constant content of EDOT monomer, the obtained rGO/PEDOT electrodes present larger specific capacitance (SC) due to more GO are reduced into rGO and the EDOT monomer polymerized into PEDOT more efficiently. This result is also consistent with conductive performance investigation and indicates that proper GO content in hydrothermal reaction needs to be optimized to obtain composite with both good conductive and electrochemical performance.
Constant current charging and discharging (GCD) curves of different rGO/PEDOT electrodes are also tested, which are shown in Fig. 8a–c. With the increase of scanning current density, the relative increase of GCD cure area is observed, indicating the excellent charge/discharge performance of composite electrodes. The GCD performance of composite electrodes also shows a GO content-dependent relationship, which is shown in Fig. 8d. With the increase of GO contents during the hydrothermal polymerization, the increasing GCD curve area of obtained composite electrodes is observed, indicating the enhanced energy storage performance can be achieved at an optimized GO mass ratio during the hydrothermal reaction, which shows the same tendency with CV performance.
Table 2 shows the calculated specific capacitance (SC) of rGO and different rGO/PEDOT electrodes. From the table, we can see that the proper ratio of GO mass shows a distinct influence on SC performance of obtained composite electrodes. The SC of composite electrode increases from 120.5 F/g to 202.7 F/g with the GO mass increasing from 1.5 g to 4 g, which is reasonable for more thorough reduction of GO and production of polymerized PEDOT. When the GO mass ratio was increased to 4.5 g, a reduced SC of composite electrode about 183.3F/g was presented. This result is good which consists of the conductive investigation presented in Table 1. We conclude that the excessive addition of GO resulted in distinct aggregation and the reduction of specific capacitance of composite electrode occurred accordingly. After the anchoring of PEDOT particle on the rGO sheets at the proper GO concentration, the introduction of PEDOT pseudocapacitance would enhance the specific capacitance obviously than pure rGO electrode. Our composite electrodes show higher specific capacitance (SC) than reported pure rGO electrodes with varied architecture [64, 65], our previously reported rGO/PEDOT composite electrode prepared through an oxidant polymerization method , composite rGO/PEDOT:PSS electrodes [67, 68], composite rGO/Polypyrrole (PPY) , and our PEDOT/rGO electrode obtained from physical mixing (Table 3). These electrodes also show comparable SC performance with a high SC rGO/polyaniline (PANi) electrode , but show higher conductivity which is a benefit to construct high power density devices. Furthermore, as porous electrode materials, our composite electrode exhibits a 66.5F cm−3 volumetric capacitance (VC), which was comparable for the high VC electrode constructed from graphene aerogel/conducting polymers .
Figure 9 a shows the Nyquist plots of rGO and different rGO/PEDOT composite electrodes. It can be seen that the composite electrodes show smaller inner resistant (Rs) than pure rGO. The smallest Rs electrode comes from the optimized hydrothermal reaction under optimized GO/EDOT mass ratio, which can trigger the polymerization of EDOT efficiently and reduction of GO thoroughly, and the obtained electrodes exhibit higher conductive capability. This Rs result is also well consistent with the conductivity result of different electrodes mentioned above. The rate performance of composite rGO/PEDOT electrodes and rGO prepared through hydrothermal reaction is also evaluated, and this performance is vital for actual application for energy storage applications. As shown in Fig. 9b, the rGO/PEDOT electrodes exhibit good cycling ability, and the specific capacitance maintained above 90% after more than 9000 times cycle at a 1.0 A/g scan current density. As we know that the pure conductive polymer will exhibit poor electrochemical stability after long time cycling, our rGO/PEDOT composite electrodes show good stability after long time cycles. We attribute this to the excellent mechanical strength of rGO, which affords stable support for PEDOT polymer during charging/discharging process. Furthermore, this composite electrode also shows excellent flexible ability, which is characterized and shown in Fig. 9c. It can be seen that more than 95% of the initial capacitance of electrode maintains after three thousands of free bending, which shows promising performance to construct flexible energy storage devices.
The rGO/PEDOT nanocomposite has been successfully prepared by a hydrothermal polymerization method. The ultrathin conducting PEDOT layer was constructed on rGO sheets through an oxidant-free polymerization method in aqueous GO solution. In this hydrothermal reaction, the functional groups on the GO sheets trigger the polymerization of EDOT, and the GO are reduced to rGO accordingly. The results of conductive and electrochemical performance indicated that the PEDOT-anchored rGO exhibited high conductivity and showed enhanced energy storage capability than pure hydrothermal-prepared rGO. Furthermore, the excellent mechanical ability of rGO affords robust support for conducting PEDOT simultaneously during the energy storage process. This highly conductive nanostructure of conducting polymer PEDOT on rGO shows promising application for high-performance electrochemical electrodes and flexible devices.
Availability of Data and Materials
All datasets are presented in the main paper or in the additional supporting files.
Electric double layer capacitance
Polymerization of 3,4-ethylenedioxythiophene
Electrochemical impedance spectroscopy
Reduced graphene oxide
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The authors acknowledge funding contributions from the National Science Foundation of China (NSFC) (Grant No. 61471085, Grant No. 61371046 and 61774030), the National Science Funds for creative Reach Groups of China (Grant No. 61421002), and the Chongqing Postdoctoral Science Special Foundation (Grant No. Xm2017051).
The authors declare that they have no competing interests.
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Li, S., Chen, Y., He, X. et al. Modifying Reduced Graphene Oxide by Conducting Polymer Through a Hydrothermal Polymerization Method and its Application as Energy Storage Electrodes. Nanoscale Res Lett 14, 226 (2019) doi:10.1186/s11671-019-3051-6
- Hydrothermal polymerization
- Reduced graphene oxide
- Conducting polymer