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Controllable Preparation of V2O5/Graphene Nanocomposites as Cathode Materials for Lithium-Ion Batteries
Nanoscale Research Letters volume 11, Article number: 549 (2016)
Transition metal oxides and graphene composites have been widely reported in energy storage and conversion systems. However, the controllable synthesis of graphene-based nanocomposites with tunable morphologies is far less reported. In this work, we report the fabrication of V2O5 and reduced graphene oxide composites with nanosheet or nanoparticle-assembled subunits by adjusting the solvothermal solution. As cathode materials for lithium-ion batteries, the nanosheet-assembled V2O5/graphene composite exhibits better rate capability and long-term cycling stability. The V2O5/graphene composites can deliver discharge capacities of 133, 131, and 122 mAh g−1 at 16 C, 32 C, and 64 C, respectively, in the voltage range of 2.5–4.0 V vs. Li/Li+. Moreover, the electrodes can retain 85% of their original capacity at 1C rate after 500 cycles. The superior electrochemical performances are attributed to the porous structures created by the connected V2O5 nanosheets and the electron conductivity improvement by graphene.
Rechargeable lithium-ion batteries, as one of the most important energy storage devices, have been widely used in consumer electronic devices such as cell phones, laptop computers, and hybrid electrical vehicles. However, the increasing demands for better batteries push the researchers to develop new electrode materials with improved performance including higher energy density, better rate capability, and longer lifespan [1–3].
Among the numerous cathode materials, V2O5 is a promising material because of its low cost, abundant resource reservation, and high-energy density . However, the low ionic diffusivity (10−12–10−13 cm2 s−1) and moderate electrical conductivity (10−12–10−13 S cm−1) limit its electrochemical performance . To overcome the drawbacks, great efforts have been endeavored to fabricate nanostructured materials. To date, various V2O5 nanomaterials, such as nanorods , nanotubes , nanowires [5, 8], nanosheets [9, 10], nanospheres [11–13], and nanoflowers [14, 15] were reported with enhanced electrochemical performance due to the kinetics improvement for redox reactions. However, the intrinsic low electronic conductivity of V2O5 is still undressed. More recently, making V2O5 nanocomposites with conductive materials are effective for obtaining high-performance electrode materials. In particular, carbonaceous materials such as carbon nanotubes [16, 17], mesoporous carbon , and graphene [8, 19, 20] are of great popularity in making the nanocomposites. Among them, graphene has attracted particular interest in making nanocomposites due to its excellent physical and chemical properties, including high electronic conductivity, high surface area, and superior mechanical properties. The combination between graphene and nanomaterials can not only increase the conductivity and specific surface area of active materials but also prevent them from agglomerating upon cycling [21–23]. In the past years, vanadium oxides and graphene nanocomposites, such as VO2@graphene , V2O3@graphene , and V3O7@graphene , have been successfully prepared. However, the controllable preparation of vanadium oxides on graphene nanosheets with different structures is rarely reported, which has a big effect on the electrochemical properties.
Herein, we report the structural engineering of V2O5/graphene with different morphologies by a solvothermal approach with subsequent annealing in air. Vanadium precursors with nanosheet or nanoparticle morphology are controllably prepared on the surface of graphene and can be converted into V2O5/reduced graphene oxide nanocomposites with good structural reservation in the calcination process in air. As cathode materials for lithium-ion batteries, the nanosheet-structured V2O5/reduced graphene oxide nanocomposites exhibit much better rate capability and cyclic stability than V2O5 nanoparticles/reduced graphene oxide composites. The relationship between nanostructures and their electrochemical performance is discussed.
The graphene oxide was made by a modified Hummers method . For the composite synthesis, 10 mg dried graphene oxide (GO) nanosheets were dispersed in 30 mL of isopropyl alcohol by ultra-sonication for 30 min. Then, 0.4 mL of vanadium triisopropoxy oxide (Alfa Aesar) was added into the solution immediately. The mixture was stirred for 10 min before transferring to a 50-mL Teflon-lined stainless steel autoclave, which was later kept at 200 °C for 12 h. After cooling down naturally, the precursor precipitates were collected by centrifugation and washed several times by alcohol, before drying at 60 °C for 12 h. Finally, the dried precursor was annealed at 320 °C for 1 h in air. The obtained material was designated as nanoparticle-structured V2O5/reduced graphene oxide composite I (V/GO-I).
The nanoparticle-assembled V2O5/graphene composite was prepared by adding extra 2 mL deionized (DI) water into the solvothermal solution, keeping other parameters unaltered. The obtained material was designated as nanoparticle-structured V2O5/reduced graphene oxide composite II (V/GO-II).
The crystal phases were collected using a Rigaku D/max2500 with Cu-Kα radiation (λ = 1.54178 Å) using a step of 0.02o between 10° and 80° (2θ). The morphologies of the samples were studied by scanning electron microscopy (SEM, FEI Nova Nano SEM 230) and transmission electron microscopy (TEM, FEI Tecnai G20). The X-ray diffraction (XRD) patterns of the samples were collected in the range between 10o and 80o with a step size of 0.02°. The weight percentages of graphene in the V2O5/graphene composites were determined by thermogravimetric (TG) analysis with a heating rate of 10 °C min−1. A spectrometer (Raman, LabRAM HR800) with a back-illuminated charge-coupled detector attachment was used to record the Raman spectra.
The electrochemical performances of the electrodes were tested in a coin cell assembly (2016 type coin cell). For the electrode preparation, a mixture of V2O5/reduced graphene oxide composites, acetylene black, and polyvinylidene fluoride (PVDF) in a weight ratio of 70:20:10 was dispersed in an N-methyl-2-pyrrolidone (NMP) solution to make a slurry, which was coated on aluminum foil and dried in a vacuum oven at 100 °C overnight. The cells were assembled in the glove box (Mbraun, Germany) filled with ultra-high-purity argon using polypropylene membrane as the separator, lithium metal as the anode, and 1-M LiPF6 in ethyl carbonate/dimethyl carbonate (1:1 v/v) as the electrolyte. The cyclic voltammetry (CV) measurement was tested on CHI660C (CH Instrument Electrochemical Workstation), and the galvanostatic discharging/charging experiment was tested on a Land battery tester (Land CT 2001A, Wuhan, China). The measurements were all carried out in the voltage range of 2.5–4.0 V (vs. Li/Li+). The electrochemical impedance spectrometry (EIS) was carried out on a ZAHNER-IM6ex electrochemical workstation (ZAHNER Co. Germany) in the frequency range of 100 kHz to 10 mHz using the fresh cell.
Results and Discussion
Figure 1 illustrates the two different synthetic processes of V2O5/graphene nanocomposites with diverse self-assembled subunits. As indicated by process I, vanadium precursor nanosheets are grown on the graphene nanosheets first during the solvothermal process, in which vanadium triisopropoxy oxide (VO(OiPr)3) was used as the vanadium resources. The prepared vanadium precursor and graphene composite can be converted into V2O5 and graphene composite with well-preserved structures. Process II indicates the preparation of nanoparticle-assembled vanadium precursor and graphene composite by adding extra 2 mL de-ion water in the solvothermal solution. Thereafter, the precursor composite can be converted into V2O5 nanoparticles and reduced graphene oxide nanocomposites (V/GO-II).
Figure 2a shows the SEM image of the solvothermal products from process I, which indicates the homogenous distribution of vanadium precursor on graphene nanosheets. As we know, graphene oxides have large amount of functional groups on its surface, which is helpful for the growth of vanadium precursors. The vanadium precursors are composed of nanosheets and uniformly grew on the reduced graphene oxide substrates. The vanadium precursor nanosheets are about 1 μm in-plane and connect with neighboring nanosheets to form porous structure on the surface of graphene nanosheets. In the formation of the composite, graphene functions as a planar templates and the growth of nanosheets on its surface can greatly prevent their restacking and improve the electrolyte penetration. Figure 2b shows the FESEM image of the nanoparticle-assembled vanadium precursor and graphene composite. The vanadium precursor is of nanoparticle morphology and distributes homogeneously on the graphene nanosheets. Additional file 1: Figure S1 shows the XRD patterns of the solvothermally prepared two composites. The detection of broad XRD peaks around 30° can be attributed to the reduced graphene nanosheets. No other distinguishable XRD peaks are detected for the nanosheet-assembled vanadium precursor/GO composite, indicating the amorphous feature of the vanadium-precursor nanosheets. However, the XRD peak of the nanoparticle-assembled vanadium precursor/reduced graphene composite can be attributed to VO2 phase (space group: P42/mnm (136); a = 0.4556 nm, b = 0.4556 nm, c = 0.285 nm, JCPDS card no. 76-0677). The formation of VO2 phase can be attributed the reduction of V2O5·nH2O by alcohol during solvothermal process, in which V2O5·nH2O is prepared by the hydrolysis of vanadium triisopropoxy oxide with water. The result indicates the structures of the vanadium precursor can be adjusted by the addition of 2 mL de-ion water. The addition of water can speed the hydrolysis reaction between vanadium triisopropoxy oxide and water to form brown colored V2O5·nH2O, which may generate more nucleation on the graphene nanosheets, but sacrificing their parcel growth. However, due to the amorphous feature of the vanadium precursor nanosheets, it is difficult to give the exact reaction during the solvothermal process. The formation of the amorphous nanosheets may be attributed to the decomposition of vanadium triisopropoxy oxide under the condition of high temperature and high pressure during the solvothermal process. Much less nuclei seeds are formed on the reduced graphene oxide and grow continuously to form the nanosheet morphology without the addition of water.
Figure 3 shows the powder X-ray diffraction (XRD) patterns of the V/GO-I composite and the V/GO-II composite. After calcination, the identified diffraction peaks can be indexed to the orthorhombic V2O5 phase (space group: Pmmn (no. 59); a = 1.1516 nm, b = 0.3565 nm, c = 0.4372 nm, JCPDS card no. 41-1426). The existence of reduced graphene oxides in the composite was confirmed by the Raman results, as shown in Fig. 4. The characteristic peaks at 1350 and 1580 cm−1 correspond to the typical G and D bands of graphene. Moreover, the intensity ratio between G and D bands become larger, indicating the partial reduction of graphene oxide. All other Raman peaks for the V/GO-I composite and the V/GO-II composite can be characterized on the basis of the vanadium oxide (Table 1) [28–30]. The weight percentage of graphene in the composite was determined by TG analysis and the result is shown in Fig. 5. The gentle weight loss before 200 oCcan be ascribed to the evaporation of physical adsorbed water, and the fast weight drop thereafter can be attributed to the burning out of reduced graphene oxides. Therefore, the content of reduced graphene oxide in the composite is approximately 7%.
Figure 6 shows the structural characterization of the V/GO-I composite, which is obtained by annealing the nanosheet-assembled vanadium precursor and reduced graphene oxides in air. According to FESEM image (Fig. 6a), the nanosheet morphology of the vanadium precursor can be well-preserved after conversion into V2O5. Moreover, the existence of graphene in the composite is also demonstrated by the broken part of the composite, as shown in Fig. 6b. The result is in good accordance with the Raman and TG analysis results. The high-magnification FESEM image (Fig. 6c) shows the V2O5 nanosheets are unparalleled to each other to form a porous three-dimensional structure, which may be of advantage of preventing the re-stack of graphene nanosheets and the electrolyte penetration. Figure 6d shows the elemental mapping results of the nanosheet-assembled V2O5 and reduced graphene oxide composites, which reveals the uniform distribution of C, V, and O elements in the composite. Figure 6e, f shows the TEM images of V2O5 nanosheets and graphene oxide composite, indicating the porous feature of the vanadium oxides and their high uniformity.
Figure 7 shows the FESEM and TEM images of the nanoparticle-assembled V2O5 and reduced graphene oxides. According to the FESEM images (Fig. 7a, b), the V2O5 nanoparticles in the composite is homogeneously distributed on reduced graphene oxide nanosheets, similar to the morphology of the nanoparticle-assembled vanadium precursor and reduced graphene oxide composite in Fig. 2b. The TEM images give more detailed information the structure. The nanoparticles are about 50–100 nm in-plane size. The HRTEM image (Fig. 7d) reveals the stacking feature of the nanoparticles and each nanoparticle is further composed of several closely stacked small nanosheets. Moreover, the lattice fringes are well observed with a distance of 0.576 nm, in good agreement with the planar distance of (200).
The V2O5 and reduced graphene oxide composites were assembled into coin cells to evaluate their electrochemical properties and the results are shown in Fig. 8. Figure 8a shows the first consecutive five CV curves for the V/GO-I composite at a scan rate of 0.1 mV s−1. Two pairs of redox peaks are clearly observed for each cycle, which indicates the multiple step phase transitions for V2O5 and reduced graphene oxide composite. The cathodic peaks at 3.39 and 3.19 V correspond to the phase transition from V2O5 to ε-Li0.5V2O5, then to δ-Li1.0V2O5, respectively. And the two corresponding anodic peaks at 3.23 and 3.43 V are related to the phase transformations from δ-Li1.0V2O5 to ε-Li0.5V2O5, and then to V2O5 in return [31–33]. No distinct peak intensity and potential position changes for the subsequent cycles are detected, suggesting the good reversibility of the electrode. Moreover, two weak redox peaks between 2.8 and 2.9 V can be detected, which may be attributed to the surface adoption or desorption of Li+ ions upon cycling. Comparing to the CV curves for V/GO-II composite (Additional file 1: Figure S2), the V/GO-I composite exhibit higher peak intensity and smaller polarization .
Figure 8b shows the rate performances of the composites. Both V/GO-I and V/GO-II composite electrodes exhibit good rate capability. The capacities vary slightly for the composites less than 8C. However, the rate performance of the V/GO-I composite becomes obvious at rates higher than 16C. A specific capacity of 133 mA h g−1 can be obtained for V/GO-I composite even at 16C, which is very close to the theoretical capacity of 147 mA h g−1 for one lithium-ion intercalation per formula. Moreover, almost no capacity fade is detected at 32C and 40C. Even at 64C, the V/GO-I composite can still deliver a specific discharge capacity of 122 mAh g−1. However, the capacity decreases much faster at high rates (>16C) for V/GO-II composite. The corresponding charge/discharge curves are shown in Additional file 1: Figure S3. The composite electrodes deliver specific discharge capacities of 108, 85, 74, and 50 mA h g−1 at 16C, 32C, 40C and 64C, respectively. When the discharge/charge rates were reset to 1C, high discharge capacity of 139 mAh g−1 can be recovered for both composites. The coulombic efficiency of V/GO-I composite is close to 100% in the whole discharge/charge process.
Figure 8c shows the charge/discharge profiles of the V/GO-I composite at various rates. The working potentials decrease gradually and the discharge/charge plateaus can still be observed even at higher rates. The voltage gap is much smaller and the capacity is larger than those for V/GO-II composite. The result indicates the lower polarization of the nanosheet-assembled V2O5/graphene composite, which may be attributed to the porous structures created by the nanosheets.
Figure 8d shows the long-term cycling performance for the two V2O5/graphene composites. The V/GO-I composite deliver an initial high specific capacity of 142 mAh g−1 at 2C and retain a capacity of 121 mA h g−1 after 500 cycles. The average capacity fading is only 0.03% per cycle. For comparison, the V/GO-II composite only retains a capacity of 80 mA h g−1 after 500 cycles at the same rate. Additional file 1: Figure S4 shows the charge/discharge profiles of the first, tenth, 100th, and 500th cycles at 2C for the two composites. As shown in Additional file 1: Figure S4a, The initial discharge and charge capacities are 142.1 and 141.6 mA h g−1, respectively, for the V/GO-I composite and the coulombic efficiency can be of 99.6%. After 500 cycles, the plateaus can still be easily detected. Additional file 1: Figure S4b shows the discharge/charge profiles for V/GO-II composite, which indicates the significant change of the plateaus for the 500th cycle. The result demonstrates the improved cycling stability of the V/GO-I composite.
Figure 9 shows the electrochemical impedance spectroscopy (EIS) measurement results for both electrodes, which acquired from fresh cells. The semi-cycle for V/GO-I is much smaller than that for V/GO-II composite. According to the simulation result, the charge transfer resistance for V/GO-I is about 55.03 Ω, which is far less than 104 Ω for the V/GO-II composite. The result demonstrates the improved charge transfer kinetics for the nanosheet-assembled V2O5 and reduced graphene oxide composite. According to the electrochemical analysis results, the nanosheet-assembled V2O5/graphene composite exhibit better rate capability, cycling stability, and lower charge transfer resistance than the nanoparticle-assembled V2O5/graphene composite. The electrochemical performance of V/GO-I composite is also much better than many previously reported V2O5 electrodes, such as hollow structured V2O5 microspheres  and three-dimensional porous V2O5 . Table 2 lists the rate performance of V2O5-based electrodes in this work and from many previous reported literatures. As shown in Table 2, the nanosheet-assembled V2O5/r-GO composite exhibit higher capacity and better rate capability than many other V2O5-based electrodes. The excellent rate performance and superior cyclic stability can be attributed to the synergistic effects between V2O5 and graphene substrates, which include the following aspects: (1) the growth of V2O5 nanosheets on reduced graphene oxide can ensure the good electronic conductivity of the electrode materials; (2) the porous space created by the interconnected large nanosheets can improve the accessibility of the electrolyte with the electrode materials; (3) the ultra-thin nanosheet thickness can greatly reduce the Li+ ions diffusion and electron transportation distances; and (4) the porous structure may better accommodate the volume changes upon cycling.
In summary, nanosheet- or nanoparticle-assembled V2O5/reduced graphene oxide composites are synthesized by adjusting the solvothermal condition. The vanadium precursor can grow homogeneously on the reduced graphene oxides and the obtained composites can be converted into V2O5/reduced graphene oxide composites with good structural reservation. As cathode materials for lithium-ion batteries, the nanosheet-assembled V2O5/reduced graphene oxide nanocomposites (V/GO-I) exhibit better rate capability and cycling stability than the nanoparticle-assembled V2O5/graphene nanocomposites (V/GO-II). The superior electrochemical performance is attributed to the synergistic effects between V2O5 nanosheets and reduced graphene oxides.
Field emission scanning electron microscopy
Transmission electron microscopy
Nanosheet-structured V2O5/reduced graphene oxide composite I
Nanoparticle-structured V2O5/reduced graphene oxide composite II
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The financial supports by National Natural Science Foundation of China (No.51302323), Program for New Century Excellent Talents in University (NCET-13-0594), Research Fund for the Doctoral Program of Higher Education of China (No.201301621200), and Natural Science Foundation of Hunan Province, China (14JJ3018), are acknowledged. Prof. Guozhong Cao from University of Washington is acknowledged for the discussion.
YL and YW did the most experiments in this work. YZ carried out the TG analysis. AP and YW made the research plan. SL gave some advices on the work. All authors read and approved the final manuscript.
The authors declare that they have no competing interests.
XRD patterns of vanadium precursors, CV curves, charge/discharge profiles of the V@GO-II composite. Discharge/charge voltage profiles of the V@GO-I composite. Raman peaks and their assignments of V2O5. Figure S1. XRD patterns of the nanosheet-assembled vanadium precursor/GO composite (blue line) and the nanoparticle-assembled vanadium precursor/GO composite (red line). Figure S2. CV curves of the V/GO-II composite at a scan rate of 0.1 mV s−1. Figure S3. Charge/discharge profiles of the V@GO-II composite at different densities. Figure S4. Discharge/charge voltage profiles of the V@GO-I composite (a) and the V@GO-I composite (b) at a current rate of 2C. (DOC 4760 kb)
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Liu, Y., Wang, Y., Zhang, Y. et al. Controllable Preparation of V2O5/Graphene Nanocomposites as Cathode Materials for Lithium-Ion Batteries. Nanoscale Res Lett 11, 549 (2016) doi:10.1186/s11671-016-1764-3
- Vanadium oxides
- Reduced graphene oxide
- Lithium-ion batteries