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. 2017 Sep 11;2(9):5684–5690. doi: 10.1021/acsomega.7b00752

Polyoxomolybdate–Polypyrrole/Reduced Graphene Oxide Nanocomposite as High-Capacity Electrodes for Lithium Storage

Mi Zhang †, Tao Wei †,‡, A-Man Zhang †, Shun-Li Li †, Feng-Cui Shen §, Long-Zhang Dong †, Dong-Sheng Li ∥, Ya-Qian Lan †,*
PMCID: PMC6644506  PMID: 31457829

Abstract

graphic file with name ao-2017-007526_0002.jpg

A nanocomposite polyoxomolybdate (PMo12)–polypyrrole (PPy)/reduced graphene oxide (RGO) is fabricated by using a simple one-pot hydrothermal method as an electrode material for lithium-ion batteries. This facile strategy skillfully ensures that individual polyoxometalate (POM) molecules are uniformly immobilized on the RGO surfaces because of the wrapping of polypyrrole (PPy), which avoids the desorption and dissolution of POMs during cycling. The unique architecture endows the PMo12–PPy/RGO with the lithium storage behavior of a hybrid battery–supercapacitor electrode: the nanocomposite with a lithium storage capacity delivers up to 1000 mAh g–1 at 100 mA g–1 after 50 cycles. Moreover, it still demonstrates an outstanding rate capability and a long cycle life (372.4 mAh g–1 at 2 A g–1 after 400 cycles). The reversible capacity of this nanocomposite has surpassed most pristine POMs and POMs-based electrode materials reported to date.

1. Introduction

With the rapid increase in the global demand for portable electronic devices, electrical vehicles, and other energy-demanding equipment, lithium-ion batteries (LIBs) and supercapacitors have shown great prospect for high-density energy storage systems.1 Although great efforts have been made to the rational design of novel anode materials for rechargeable LIBs, high-power LIBs still remain a great challenge resulting from the slow processes of Li+ diffusion. In contrast, supercapacitors work through the redox reactions of the pseudocapacitive active materials or the formation of electrical double-layer capacitors, but their low-energy density hampers their application in electrochemical devices.2−4 To satisfy the increasing demand for high power density and energy density, it is significant to design an electrode that combines the energy of a battery and power of a supercapacitor.

Polyoxometalates (POMs) have already demonstrated great promise for electrochemical energy storage owing to their electron storage.5 Particularly, Awaga and co-workers revealed that [PMo12O40]3– exhibited a reversible 24 electrons redox during charging/discharging between [PMo12O40]3– and [PMo12O40]27–.6−8 However, their application in LIBs and supercapacitors is still hampered because the electronic conductivity of the POMs is poor and their anions are likely to dissolve in the electrolyte.9 To overcome this obstacle, POMs are usually linked to conductive carbon substrates. For example, Song et al. reported that POMs can be anchored on single-walled carbon nanotubes (SWNTs) via π–π stacking or covalent bonding, which improved the affinity of POMs to conductive network, leading to an increased lithium-ion capability.10,11 Graphene oxide (GO) has attracted much interest owing to its unique properties, including chemical stability and high conductivity.12−15 It is theoretically considered that graphene possesses a higher specific surface area than SWNTs.16−18 However, there is still a bottleneck in the course of studies on POMs/reduced graphene oxide (RGO) nanocomposite that the low POMs loadings on graphene results in the poor performance because of the weak interaction between POMs and graphene.19 Accordingly, it is still challenging to develop the appropriate linkage between POMs and graphene.

Herein, the synthesis of H3PMo12O40 (polyoxomolybdate (PMo12))–polypyrrole (PPy)/RGO nanocomposite (denoted as PMo12–PPy/RGO) via a one-pot hydrothermal strategy is reported together with their applications for high-performance LIBs. We prepared the nanocomposite by using pyrrole (Py) to reduce PMo12 to obtain heteropoly blue, which was further used for the reduction of graphene accompanied by the polymerization of the Py monomer.20−23 It is proved that PPy is not only an efficient reagent to improve the electron transport but also relieves the leaching of POMs into the electrolyte during cycling, leading to the enhancement of battery performance. The nanocomposite exhibits a good cycling reversibility and achieves a high capacity as a LIB anode, which can deliver a discharge capacity of 1082.5 mAh g–1 at 100 mA g–1 after 50 cycles as well as an impressive rate capability. Such an outstanding property of the nanocomposite is ascribed to the hybrid performances, which include both capacitive and battery behavior. Therefore, the synthesis of the PMo12–PPy/RGO paves the way for POMs as anode materials in LIBs.

2. Results and Discussion

2.1. Preparation and Characterization of PMo12–PPy/RGO Nanocomposite

Scheme 1 illustrates the formation of PMo12–PPy/RGO nanocomposite. We obtained PMo12–PPy/RGO nanocomposite using a one-pot hydrothermal strategy by mixing PMo12, Py, and GO. PMo12 serves as a strong oxidant, leading to the polymerization of Py, whereas PMo12 changes to heteropoly blue, which is used to reduce GO to RGO. The PMo12–PPy nanoparticles are well distributed on the surfaces of the RGO nanosheets (NSs), which reduces the restacking of RGO to some extent together with creating a lot of mesopores to improve the accessibility of Li+ and electron.

Scheme 1. Schematic Illustration of the Formation of PMo12–PPy/RGO Nanocomposite.

Scheme 1

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Figure S1a shows the Raman spectrum of the as-synthesized nanocomposite. For comparison, the Raman spectra of pure RGO, PMo12/RGO control samples, and PMo12–PPy/RGO composite are provided. As can be observed, the pure RGO and PMo12/RGO samples represent two typical Raman features at ∼1351 and ∼1599 cm–1, corresponding to D and G bands, respectively. Compared with the D band, the intensity of the G band is apparently stronger, which indicates a higher graphitization degree of the PMo12–PPy/RGO nanocomposite. In addition, a series of characteristic Raman peaks for PPy centered at about 931, 976, 1053, 1244, 1371, 1411, and 1588 cm–1 are observed in the PMo12–PPy/RGO sample,24 indicating that the polymerization of Py by PMo12 is conducted well and the PMo12–PPy nanoparticles are distributed on the graphene sheets.25 Compared with PMo12 and RGO, several new peaks originating from PPy are observed in the spectrum of PMo12–PPy/RGO sample from the Fourier-transform infrared (FTIR) spectroscopy (Figure S1b), where the C=C and C–N stretching vibrations at 1558 and 1453 cm–1, respectively, as well as the C–H in-plane ring-bending modes at 1314 cm–1 and the C–N in-plane ring deformation and bending modes at 1182 cm–1 can be observed.26−28 In the PMo12–PPy/RGO nanocomposite, the four observed characteristic bands centered at 1049, 931, 863, and 790 cm–1 are ascribed to P–Oc, Mo=Ot, Mo–Ob–Mo, and Mo–Oe–Mo stretching vibrations,20,29,30 indicating that the PMo12 component has been successfully implanted into the final nanocomposite.

In contrast to PMo12/RGO (Figure S2a,b), the restacking problem of the PMo12–PPy/RGO nanocomposite (Figure 1a,b) is alleviated obviously and the NSs present rough surfaces and wrinkled edges because of the polymerization of Py homogeneously decorated with PMo12 on the surfaces of the RGO films.31−34 The corresponding transmission electron microscopy (TEM) analysis (Figure 1b) reveals that many of PMo12–PPy nanoparticles with the average size of about 50 nm homogeneously anchored on the RGO sheets. For comparison, we utilized the same strategy to prepare other nanocomposite CoMo6–PPy/RGO based on analogous POMs ([CoMo6O24H6]·7H2O). The TEM and scanning electron microscopy (SEM) images of the CoMo6–PPy/RGO nanocomposite in Figure S2a,b reveal that PMo12–PPy nanoparticles tend to be more homogeneous than CoMo6–PPy nanoparticles on the RGO sheets. The desired spatial distribution of different elements in the PMo12–PPy/RGO nanocomposite has been examined by element mapping analysis. As shown in Figure 1c–g, P and Mo elements mainly exist in the flake-sized grains; N and C elements are uniformly distributed in the entire nanosheets. For comparison, the mappings for PMo12/RGO are given in Figure S3. The correspoing mappings show that P, Mo, O elments of the PMo12−PPy/RGO are more obvious than that of PMo12/RGO.

Figure 1.

Figure 1

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(a) SEM images of the PMo12–PPy/RGO nanocomposite. (b) TEM images of the PMo12–PPy/RGO nanocomposite. (c–g) Energy-dispersive spectrometry mapping of PMo12–PPy/RGO.

The related N2 adsorption–desorption tests analyzed the pore size distribution of the obtained nanocomposite (Figure S4b). Compared with that of PMo12/RGO and CoMo6–PPy/RGO nanocomposite, the PMo12–PPy/RGO nanocomposite has a rather larger and broader average pore size at around 20 nm, which is a result of the spaces between the PMo12–PPy nanoparticles. The PMo12–PPy/RGO nanocomposite presents the largest Brunauer–Emmett–Teller (BET) surface area (91.52 m2 g–1), whereas the BET surface areas of PMo12/RGO and CoMo6–PPy/RGO are 65.5 and 78.1 m2 g–1, respectively (Figure S4a). The larger pore size and the higher specific surface area facilitate the rapid mass transport of Li ions and electron transport, which are all correlated with the increased battery performance. The thermogravimetric analysis (TGA) results of the PMo12–PPy/RGO nanocomposite and PMo12 are presented in Figure S5. The initial mass loss (3.6%) below 188 °C is associated with the release of water adsorbed on the PMo12–PPy/RGO nanocomposite and the further degradation of PPy, as well as the transformation from PMo12 to MoO3, takes place between 188 and 560 °C (Figure S5a). We can calculate from the TGA and experiment that the PMo12–PPy/RGO nanocomposite possesses 72.9 wt % of PMo12 and 20.43 wt % of PPy.

The survey X-ray photoelectron spectroscopy (XPS) spectra of the sample before and after the cycling of LIBs demonstrate the presence of C, Mo, P, N, and O elements in the PMo12–PPy/RGO nanocomposite (Figure S6). As shown in Figure S6b, the Mo 3d spectrum of PMo12–PPy/RGO has two peaks at 232.3 and 235.5 eV before the electrochemical test corresponding to 3d5/2 and 3d3/2 of Mo6+, respectively.35,36 After the discharge to 0.01 V, the peaks at the binding energy of 231.9 eV are related to parts of Mo4+ because of the reduction of Mo6+ (Figure S6f).37 Additionally, by deconvolution of C 1s peak (Figure S6c), the binding energy at 285 eV reveals the presence of the C–N group in the obtained nanocomposite. The corresponding fine XPS spectrum of N 1s (Figure S6d) shows that the binding energy of N 1s is about 398.3 eV, implying the existence of pyrrole N in the PMo12–PPy/RGO nanocomposite. Thus, combining the fine XPS spectra for C 1s and N 1s, the existence of PPy in the obtained nanocomposite can be confirmed. From the XPS result, we can also observe the drop in the number of oxygen-containing groups, demonstrating a reduction of GO.

2.2. Electrochemical Performances of PMo12–PPy/RGO Nanocomposite

To investigate the electrochemical activity of the PMo12–PPy/RGO nanocomposite, the cyclic voltammetry (CV) measurements were tested at a constant scan rate of 0.2 mV s–1 (Figure 2a). The peak at about 0.6V reflects the formation of a solid electeolyte interface(SEI) film in the first cycle and then the peak disappears in the following cycles.38 Although the CV curves of the first cycle are quite different in shape due to the irreversible side reactions on the electrode surfaces and interfaces, the subsequent CV curves are analogous. In the subsequent scans, broad cathodic peaks centered at about 1.2 V, as well as anodic peaks centered at around 1.6 V, are observed for the PMo12–PPy/RGO electrodes, demonstrating that the reduction and oxidation of Mo39 (XPS results in Figure S6) is occurring during the charging/discharging processes.

Figure 2.

Figure 2

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(a) Cyclic voltammetry measurements of PMo12–PPy/RGO during the first three cycles at a scan rate of 0.2 mV s–1. (b) Discharge–charge curves of PMo12–PPy/RGO for different cycles constantly at 100 mA g–1. (c) Charge/discharge capacity and Coulombic efficiency (CE) of PMo12–PPy/RGO, PMo12/RGO, and PMo12 at 100 mA g–1. (d) Rate performance of the PMo12–PPy/RGO at various current densities.

The charge/discharge profiles of the PMo12–PPy/RGO nanocomposites for cycle numbers 1, 2, 10, and 50 are shown in Figure 2b. In the discharge profiles, the first lithiation curve is different from the others due to the SEI formation. It is worth noting that the curves almost overlapped after the first discharge, which indicates the formation of a stable SEI film and a good electrochemical reversibility of the PMo12–PPy/RGO nanocomposite. The capacity performance of the three nanocomposites is displayed in Figure 2c. The PMo12–PPy/RGO nanocomposite showed a discharge 1777.8 mAh g–1 and a Coulombic efficiency (CE) of 59.54% in the initial cycle. The initial irreversible loss is ascribed to the formation of the SEI layer. In addition, the reversible capacity of the PMo12–PPy/RGO nanocomposite can reach 1013 mAh g–1 after 50 cycles, whereas the control samples only deliver discharge capacities of 1507.3 mAh g–1 and the remaining capacity is 500.9 mAh g–1 after 50 cycles (PMo12/RGO) and discharge capacities of 856.2 mAh g–1 and the residual capacity is 270.3 mAh g–1 up to 50 cycles (PMo12). The above results demonstrate that the chemisorptions of PMo12 between the interfaces of PPy and RGO gives a superior electrode performance in LIBs compared with that of PMo12/RGO and pure PMo12. The capacity performance of the PMo12–PPy/RGO nanocomposite is also superior to that of the CoMo6–PPy/RGO nanocomposite and the (NH4)6Mo7–PPy/RGO nanocomposite (Figure S7a). This cycling capacity is higher than most of the pristine POMs and POMs-based nanocomposite electrodes that ever reported (Table S1 in the Supporting Information).

Because the high rate capability is beneficial to the design of high-power-type LIBs anode materials, excellent rate performance of the electrode is also an important aspect for evaluating many practical application of LIBs. It can be found that the discharge capacity of PMo12–PPy/RGO nanocomposite remains at 1057.5, 905.9, 688.0, 510.7, and 316.4 mAh g–1 at a rate of 0.1, 0.2, 0.5, 1, and 2 A g–1, respectively. Moreover, when reducing the current back to 0.1 A g–1, a high capacity of 1030.2 mAh g–1 is quickly resumed, suggesting a good reversibility of the PMo12–PPy/RGO nanocomposite (Figure 2d). In contrast, the CoMo6–PPy/RGO nanocomposite and the (NH4)6Mo7–PPy/RGO nanocomposite electrodes show a faster capacity fading as the charge/discharge rates increase (Figure S7b). In addition, a long-term cycling is achievable for PMo12–PPy/RGO, which maintained a capacity of 372.24 mAh g–1 after 400 cycles at 2 A g–1 (Figure S9). For proving the structural stability of PMo12–PPy/RGO, we performed the SEM analysis after 50 cycles at 500 mAh g–1. As shown in Figure S10, the good structural integrity is well retained compared with the CoMo6–PPy/RGO and the (NH4)6Mo7–PPy/RGO, indicating the stability of the electrode.

On the basis of the excellent performance of PMo12–PPy/RGO, effects of different concentrations of PMo12 on the electrocatalytic activity of PMo12–PPy/RGO-3 and PMo12–PPy/RGO-4 were investigated. As seen from Figure S8a, they showed a relatively poor capacity performance. PMo12–PPy/RGO-1 and PMo12–PPy/RGO-2 also exhibited poor capacity performance (Figure S8b), which can be attributed to the low concentration of GO loading with poor conductivity and low electron transfer efficiency. In contrast, a high-concentration loading may lead to the restacking of GO and affect the distribution of the mesopores for improving the accessibility of Li+ and electrons.

To profoundly explain the better performance of the PMo12–PPy/RGO nanocomposite electrodes, we carried out an analysis of the electrochemical impedance spectroscopy (EIS) of PMo12–PPy/RGO anode after three cycles (Figure 3a). The EIS data were analyzed via fitting to the equivalent circuit model (the detail inset in Figure 3a).40 The R1 consists of the total resistance of the electrolyte, separator, and electrical contacts, R2 is the charge transfer resistance, Wo is the Warburg impedance, and constant phase element of the electrode/electrolyte interface (CPE) is associated with the interfacial resistance. It can be observed that the charge transfer resistance of PMo12–PPy/RGO is 90.25 Ω, which is much lower than that of PMo12 (645 Ω). These results confirm that the incorporation of PPy coating and RGO can be favorable to charge transfer and improve the Li+ kinetics during the charge/discharge processes.

Figure 3.

Figure 3

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(a) Nyquist plots of PMo12-–PPy/RGO and microcrystal PMo12 electrodes after three cycles. (b) CV curves of PMo12–PPy/RGO at various scan rates. (c) The b-value determination of 1.2 and 0.1 V cathodic current. (d) Capacitive-controlled charge storage contributions separated by cyclic voltammogram at 5 mV s–1 scan.

The reversible capacity of PMo12–PPy/RGO is about 1082.5 mAh g–1 at 100 mA g–1, whereas the theoretical capacity of PMo12–PPy/RGO was calculated to be about 835 mAh g–1 (details can be seen in Supporting Information). Herein, we speculate this value exceeds the theoretical one on the account of a hybrid battery–supercapacitor consisting of POMs, RGO, and PPy. The battery component is caused by the reversible redox reactions of metal ions (Mo) during the lithiation/delithiation cycles. At the same time, the capacitive behavior also promotes the performances, which is ascribed to RGO and PPy.41 To investigate the electrochemical behavior of PMo12–PPy/RGO, the CV profiles at different scan rates (0.2–10 mV s–1) were performed between 0.01 and 3.0 V (Figure 3b). The voltammetric response of the PMo12–PPy/RGO electrode was analyzed by the power law I = a × vb, where I represents the current, v is the scan rate, and a is an alterable parameter. When b = 0.5, the electrode reaction is regarded as a behavior that is controlled by the diffusion of Li+,41−44 whereas b = 1 indicates a surface-controlled charge storage process. As shown in Figure 3c, it is worth noting that the b value at 0.1 V was determined to be about 0.6349, whereas the b value at 1 V was about 0.6796, suggesting a hybrid of both. To further understand the energy storage mechanism of PMo12–PPy/RGO, the equations as discussed below are utilized to calculate the contributions of the capacitance and intercalation capacity.

2.2.

or

2.2.

where k1v and k2v0.5 correspond to the current contributions “i” arising from the surface capacitive effect and the diffusion-controlled process, respectively, at a give potential “v.”45−47Figure 3d shows that the capacitive-controlled capacity contributed about 27.1% of the total Li+ storage for PMo12–PPy/RGO at 5 mV s–1 (the blue-shaded area of Figure 3d).

The superior electrode performance can be ascribed to the structure and composition of the PMo12–PPy/RGO nanocomposite. First, the RGO films are employed here for their intrinsically excellent conductivity; they can also be used as excellent supports. The PMo12–PPy nanoparticles can be distributed homogeneously on the flaky RGO films, which hampers restacking among the layers, thus relieving the structure destruction taking place in the electrodes during cycling.48 Second, the PMo12–PPy/RGO nanocomposite shows a hybrid behavior of battery and supercapacitor. The battery behaviors of PMo12 are achieved by the redox of metal ions (Mo). At the same time, the capacitive behavior also promotes the performance, which is ascribed to RGO and PPy. Third, the porous structure of the PMo12–PPy/RGO nanocomposite offers a lot of active sites for Li+ storage, as well as sufficient contact between the PMo12–PPy/RGO electrode and electrolyte. Accordingly, the specific capacity and rate capability of PMo12–PPy/RGO are enhanced.

3. Conclusions

In conclusion, we synthesized the PMo12–PPy/RGO nanocomposite through a simple one-pot hydrothermal method. The charge/discharge measurements of the PMo12–PPy/RGO nanocomposite represent the highest capacity and the most robust charge/discharge rate among the microcrystal PMo12, PMo12/RGO, CoMo6–PPy/RGO, and (NH4)6Mo7–PPy/RGO. Furthermore, the PMo12–PPy/RGO exhibits a high capacity over 1000 mAh g–1, a long-term cycling with more than 400 cycles at 2 A g–1, and a good rate performance. The results demonstrates that we have successfully immobilized POMs to RGO via the wrapping of PPy and the anode materials also exhibits a hybrid behavior of a battery−supercapacitor for superior lithium storage, which inspires us to explore advanced and insoluble framework materials consisting of electroactive molecule or cluster units for Li- and Na-storage.

4. Experimental Section

4.1. Reagents

All of the chemicals were purchased and used without further purification. The water used in the experiments was ultrapurified water (18.25 MΩ). The natural graphite powder was purchased from Aladdin. Potassium permanganate (KMnO4, ≥99%), hydrogen peroxide (H2O2, 30%), hydrazine hydrate (HCl, 36%), concentrated sulfuric acid (H2SO4, 98%) hexaammonium molybdate ((NH4)6Mo7O24·4H2O), and phosphomolybdic acid (H3PMo12O40·nH2O) were purchased from Sinopharm Chemical Reagent Co., Ltd. Phosphorus pentoxide (P2O5, ≥98.0%), potassium persulfate (K2S2O8, ≥99.5%), and were purchased from Shanghai Lingfeng Chemical Reagent Co., Ltd. Pyrrole (C4H5N, ≥98.0%) was purchased from Shanghai Kefeng Industry & Commerce Co., Ltd.

GO was prepared by modified Hummer’s method.49 The POMs clusters (NH4)4[CoMo6O24]·7H2O (CoMo6) was synthesized according to the literature method.50

4.2. Synthesis of the PMo12–RGO Nanocomposite

GO is dispersed in deionized water (10 mL) and sonicated to form a suspension with a concentration of 2 mg mL–1, followed by the introduction of the solution of 109 μL Py in 1 mL of ethanol. Then, magnetic stirring was maintained for about 30 min. After that, PMo12 (0.25 mmol, 0.456 g) was added into the PPy/GO mixture with continuous stirring. The mixture was transferred into a stainless steel vessel maintained at 180 °C for 12 h. The product was filtrated and washed with water and ethanol at least three times. After drying in vacuum oven at 60 °C for about 24 h, the resulting sample was obtained. On the basis of the experiment, we obtained the as-prepared composite PMo12–PPy/RGO (0.2991 g) and calculated the content of RGO to be about 6.67%. For comparison, CoMo6–PPy/RGO and (NH4)6Mo7–PPy/RGO were synthesized in similar method, except that PMo12 was replaced by CoMo6 and (NH4)6Mo7 in the respective reactions, and PMo12/RGO was synthesized by identical experimental without adding Py. In control experiments, PMo12–PPy/RGO-1, PMo12–PPy/RGO-2, PMo12–PPy/RGO-3, and PMo12–PPy/RGO-4 were synthesized by the similar synthetic method. The samples defined as PMo12–PPy/RGO-1 and PMo12–PPy/RGO-2 were obtained by altering the GO loading, corresponding to 1 and 3 mg mL–1, respectively. The samples defined as PMo12–PPy/RGO-3 and PMo12–PPy/RGO-4 were obtained by altering the concentration of PMo12, corresponding to 20 and 30 mM, respectively.

4.3. Material Characterization

The FTIR was collected on a Nexus 670 spectrometer. The Raman measurements were carried out using a Renishaw inVia Raman Microscope (532 nm). The thermogravimetric analysis (TGA) was carried out by using a Shimadzu-60 thermoanalyzer in air argon with a heating rate of 10 °C min–1 from room temperature to 1100 °C. Nitrogen adsorption–desorption isotherms were evaluated at 77 K on a Micromeritics ASAP 2050 system, whereas the pore size distributions were calculated according to the Barrett–Joyner–Halenda formula. The TEM and high-resolution TEM images were captured by JEOL-2100F apparatus and JEOL JSM-6700 M scanning electron microscope, respectively. The energy-dispersive X-ray (EDX) was performed on JSM-5160LV-Vantage typed energy spectrometer. The XPS measurements was collected on a scanning X-ray microprobe (PHI 5000 Verasa; ULAC-PHI, Inc.) using the excitation energy of 1486.6 eV (Al Kα) and the C 1s line at 284.8 eV as energy reference.

4.4. Electrochemical Characterization

To prepare a working electrode, a mixture of PMo12–PPy/RGO (or PMo12, PMo12/RGO, CoMo6–PPy/RGO, (NH4)6Mo7–PPy/RGO), carbon black, and poly(vinylidene fluoride) with a weight ratio of 7:2:1 were coated on a piece of copper foil. The active materials loading for the electrode was around 1 mg. The half-coin cells were assembled in an argon-filled glovebox utilizing Li metal as the negative electrode, a solution of 1 M LiPF6 in ethylene carbonate, dimethyl carbonate (1:1 in volume) as the electrolyte, and a Celgard 2400 membrane as the separator. The galvanostatic charge/discharge measurement was conducted by a LAND CT2001A multichannel battery between 0.01 and 3.0 V. The EIS measurements and CV were conducted on CHI 660D (Shanghai, China) electrochemical workstation.

Acknowledgments

This work was financially supported by NSFC (Nos. 21622104, 21371099, and 21471080); the NSF of Jiangsu Province of China (Nos. BK20130043 and BK20141445); the Priority Academic Program Development of Jiangsu Higher Education Institutions; and the Foundation of Jiangsu Collaborative Innovation Center of Biomedical Functional Materials.

Supporting Information Available

The Supporting Information is available free of charge on the ACS Publications website at DOI: 10.1021/acsomega.7b00752.

  • Structure and morphology characterizations including Raman, FTIR, SEM, TEM, EDX, N2 adsorption–desorption isotherm, TGA, XPS for PMo12–PPy/RGO and other control samples (Figures S1–S6 and S10); cycle-life performance and rate capability test for PMo12–PPy/RGO and other control samples (Figures S7 and S8); comparison of PMo12–PPy/RGO with other POMs-based anodes (Table S1) (PDF)

Author Contributions

⊥ M.Z. and T.W. contributed equally to this work.

The authors declare no competing financial interest.

Supplementary Material

ao7b00752_si_001.pdf (3.2MB, pdf)

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