Synergy Effect of High-Stability of VS4 Nanorods for Sodium Ion Battery

Sodium-ion batteries (SIBs) have attracted increasing interest as promising candidates for large-scale energy storage due to their low cost, natural abundance and similar chemical intercalation mechanism with lithium-ion batteries. However, achieving superior rate capability and long-life for SIBs remains a major challenge owing to the limitation of favorable anode materials selection. Herein, an elegant one-step solvothermal method was used to synthesize VS4 nanorods and VS4 nanorods/reduced graphene oxide (RGO) nanocomposites. The effects of ethylene carbonate/diethyl carbonate(EC/DEC), ethylene carbonate/dimethyl carbonate(EC/DMC), and tetraethylene glycol dimethyl ether (TEGDME) electrolytes on the electrochemical properties of VS4 nanorods were investigated. The VS4 nanorods electrodes exhibit high specific capacity in EC/DMC electrolytes. A theoretical calculation confirms the advance of EC/DMC electrolytes for VS4 nanorods. Significantly, the discharge capacity of VS4/RGO nanocomposites remains 100 mAh/g after 2000 cycles at a large current density of 2 A/g, indicating their excellent cycling stability. The nanocomposites can improve the electronic conductivity and reduce the Na+ diffusion energy barrier, thereby effectively improving the sodium storage performance of the hybrid material. This work offers great potential for exploring promising anode materials for electrochemical applications.


Introduction
Since the successful preparation of graphene in 2004 [1,2], two dimensional transition metal dichalcogenides (TMDs) have aroused increasing research interests for their potential applications in the field of electrochemical storage owing to the unique layered structure and outstanding physical and chemical properties [3][4][5]. Currently, lithium-ion batteries (LIBs) dominate portable electronic devices and smart grids ascribed to their high energy density and excellent long cycling stability [6][7][8]. However, the high cost of lithium caused by limited resource and uneven distribution of lithium hinders the further development in large-scale storage systems. Therefore, it is of great importance to develop desirable battery storage technologies with low prices as an alternative to LIBs [9][10][11]. Sodium-ion batteries (SIBs) have attracted rapidly growing attention for their earth abundance and similar chemistry intercalation mechanism compared with LIBs, and are looking forward to be one of the most promising next generation energy storage devices [12,13]. Despite its great potential, sluggish reaction kinetics caused by the large ionic radius and the lack of suitable electrode materials limit the practical application of SIBs [14,15]. Hence, it is of great importance to explore favorable SIBs anode materials with high specific capacity, excellent rate capability and superior long life cycles. Among the studied TMDs anode materials, vanadium-based chalcogenides [16,17] have received widespread interest due to their unique layered crystal structure and high electronic conductivity [18][19][20]. Specifically, vanadium sulfide (VS 4 ) with a monoclinic phase possesses a unique linear-chain structure consisting of V 4+ and sulfur dimers (S 2 2− ) extending along the c-axis direction, and the individual atomic chains are bonded by weak interchain van der Waals forces, forming a loosely stacked framework [21]. The large open channels (interchain distance of VS 4 is 0.583 nm) can provide abundant active sites for Na-ion diffusion and storage [22]. In addition, VS 4 has a high theoretical capacity of 1196 mAh/g and is considered as a promising candidate anode material for SIBs [21,23]. Nevertheless, the disadvantages of VS 4 electrode materials including low conductivity and large volume expansion lead to poor rate performance and cycling stability during the discharge/charge process, hindering the practical energy storage applications. To promote the electrochemical performance, it has been widely accepted that one strategy is to construct nanosized electrode materials due to the sufficient redox sites and to shorten the electron/ion diffusion distance during sodiaion/desodiation [24,25]. The second strategy is to incorporate nanomaterials into highly conductive graphene that can effectively enhance the conductivity and maintain the whole structure stability of electrodes [26][27][28][29].
In this work, we report the fabrication of uniform VS 4 nanorods by a facile solvothermal method. After introducing graphene oxide into the reaction system, VS 4 nanorods/ reduced graphene oxide hybrids (denoted as VS 4 /RGO) were successfully obtained after subsequent annealing treatment. The VS 4 nanorods have an average diameter of 30 nm, and the small VS 4 nanorods grown on the conductive support of RGO nanosheets can elevate the electronic conductivity and effectively interrupt their aggregation. Furthermore, three typical electrolytes [30] are optimized to achieve the high Na ions storage performance for VS 4 nanorods. Using ethylene carbonate/dimethyl carbonate (EC/DMC) as the electrolyte, the as-prepared novel VS 4 /RGO nanocomposites display superior cycling stability with the discharge specific capacity of 100 mAh/g after 2000 cycles at a current density of 2 A/g. The improved performance is attributed not only to the conductive network of large-size RGO nanosheets, but also to the EC/DMC electrolyte with high ionic conductivity, low solvation energy and Lowest Unoccupied Molecular Orbital (LUMO) energy.

Results
The XRD diffraction pattern of VS 4 nanorods is shown in Figure 1a. All the diffraction peaks are perfectly matched to the monoclinic phase of VS 4 (JCPDS no. 87-0603, space group I2/c, lattice constants a = 0.677 nm, b = 1.042 nm, c = 1.211 nm), indicating the high phase purity [21,23]. The two strongest characteristic diffraction peaks at 2θ = 15.7 • and 17 • are in line with the (110) and (020) crystal planes. A Raman spectrum of VS 4 nanorods shows that two typical bands at 190 and 279 cm −1 are attributed to the stretching and bending vibration modes of the V−S bonds, respectively (Figure 1b) [31].
The XRD and Raman spectroscopy analyses confirm that the prepared sample is monoclinic VS 4 . The V 2 p X-ray photoelectron spectroscopy (XPS) of the material in Figure 1c shows two peaks at 517.3 and 524.3 eV, which are ascribed to the 2p 3/2 and 2p 1/2 components of V 4+ , respectively. Two other peaks at 513.9 and 521.5 eV correspond to the V−C bond, which indicates that the VS 4 nanorods are anchored on the graphene surface through it. The scanning at S 2p region demonstrates the existence of S 2 2− dimers (Figure 1d), and the peaks at 162.9 and 164.0 eV are ascribed to S 2p 3/2 and S 2p 1/2 bands, respectively.
As shown in Figure 2, the morphology and microstructure of the as-prepared VS 4 nanorods were performed by field emission scanning electron microscopy (FESEM) and transmission electron microscopy (TEM). The obtained samples are composed of surfacesmoothly and well-dispersed short nanorods with an average diameter about 30 nm. Moreover, these nanorods are randomly stacked together to form large clusters, which may be caused by the anisotropy of the monoclinic phase VS 4 (Figure 2a-c). The TEM image of the products exhibits a rod-like structure. A lattice space of about 0.59 nm is observed by high-resolution transmission electron microscopy (HRTEM), which is consistent with the (002) plane of VS 4  As shown in Figure 2, the morphology and microstructure of the as-prepared VS4 nanorods were performed by field emission scanning electron microscopy (FESEM) and transmission electron microscopy (TEM). The obtained samples are composed of surfacesmoothly and well-dispersed short nanorods with an average diameter about 30 nm. Moreover, these nanorods are randomly stacked together to form large clusters, which may be caused by the anisotropy of the monoclinic phase VS4 (Figure 2a-c). The TEM image of the products exhibits a rod-like structure. A lattice space of about 0.59 nm is observed by high-resolution transmission electron microscopy (HRTEM), which is consistent with the (002) plane of VS4. The fast-Fourier transform (FFT) (Figure 2f) further confirms the monoclinic phase of VS4.   As shown in Figure 2, the morphology and microstructure of the as-prepared VS4 nanorods were performed by field emission scanning electron microscopy (FESEM) and transmission electron microscopy (TEM). The obtained samples are composed of surfacesmoothly and well-dispersed short nanorods with an average diameter about 30 nm. Moreover, these nanorods are randomly stacked together to form large clusters, which may be caused by the anisotropy of the monoclinic phase VS4 (Figure 2a   The successful formation of the VS 4 /RGO nanocomposite is verified by Raman spectrum analysis in the range of 180-1800 cm −1 ( Figure S1, Supplementary Materials). The two typical bands at 1340 cm −1 and 1585 cm −1 are designated as the D band and G band of RGO, respectively. The D band is associated with edge defects and disordered carbon in hexagonal graphene layers, while the G band is attributed to the in-plane stretching vibration of the sp 2 carbon atoms hybrid and highly ordered graphite [23,32,33]. The two bands at 190 and 279 cm −1 in the low wavenumber region are the vibration dispersion characteristics of VS 4 . Figure 3a shows the FESEM images of VS 4 /RGO nanocomposites. Obviously, the surface of RGO with the large wrinkled sheet structure is not smooth in the hybrid materials. The substantial VS 4 nanorods are grown on the large RGO nanosheets with uniform distribution, indicating that RGO sheets with rich oxygen-containing functional groups not only support the nucleation and growth of VS 4 , but also effectively alleviate the agglomeration of VS 4 nanorods in the VS 4 /RGO nanocomposite. The TEM characterization of VS 4 /RGO nanocomposites are shown in Figure 3b. The VS 4 nanorods are randomly and uniformly dispersed on the surface of the large-sized RGO nanosheets with typical wrinkled structure morphology, which is closely related to the anisotropy of the monoclinic phase VS 4 . The introduction of RGO as a large-area conductive channel plays an important role in enhancing the electrical conductivity and improving the structural stability of VS 4 . The energy dispersive X-ray (EDX) elemental mappings analysis reveals that these elements of V, C and S are uniformly distributed throughout the entire VS 4 /RGO nanocomposite (Figure 3c-f). The growth process of the prepared VS 4 /RGO nanocomposite should be that oxygen-containing functional groups provided a large number of growth sites for VS 4 , so that the VS 4 nanorods grew uniformly on the RGO sheet, thereby obtaining uniform composites of RGO and VS 4 . During the hydrothermal reaction, VS 4 gradually nucleated and grew on the surface of GO, while GO lost most of the oxygen-containing functional groups and was reduced to graphene (RGO). trum analysis in the range of 180-1800 cm −1 ( Figure S1, Supplementary Materials). The two typical bands at 1340 cm −1 and 1585 cm −1 are designated as the D band and G band of RGO, respectively. The D band is associated with edge defects and disordered carbon in hexagonal graphene layers, while the G band is attributed to the in-plane stretching vibration of the sp 2 carbon atoms hybrid and highly ordered graphite [23,32,33]. The two bands at 190 and 279 cm −1 in the low wavenumber region are the vibration dispersion characteristics of VS4. Figure 3a shows the FESEM images of VS4/RGO nanocomposites. Obviously, the surface of RGO with the large wrinkled sheet structure is not smooth in the hybrid materials. The substantial VS4 nanorods are grown on the large RGO nanosheets with uniform distribution, indicating that RGO sheets with rich oxygen-containing functional groups not only support the nucleation and growth of VS4, but also effectively alleviate the agglomeration of VS4 nanorods in the VS4/RGO nanocomposite. The TEM characterization of VS4/RGO nanocomposites are shown in Figure 3b. The VS4 nanorods are randomly and uniformly dispersed on the surface of the large-sized RGO nanosheets with typical wrinkled structure morphology, which is closely related to the anisotropy of the monoclinic phase VS4. The introduction of RGO as a large-area conductive channel plays an important role in enhancing the electrical conductivity and improving the structural stability of VS4. The energy dispersive X-ray (EDX) elemental mappings analysis reveals that these elements of V, C and S are uniformly distributed throughout the entire VS4/RGO nanocomposite (Figure 3c-f). The growth process of the prepared VS4/RGO nanocomposite should be that oxygen-containing functional groups provided a large number of growth sites for VS4, so that the VS4 nanorods grew uniformly on the RGO sheet, thereby obtaining uniform composites of RGO and VS4. During the hydrothermal reaction, VS4 gradually nucleated and grew on the surface of GO, while GO lost most of the oxygen-containing functional groups and was reduced to graphene (RGO). Electrolytes are essential for the proper functioning of any battery technology, and the emerging Na-ion technology is no exception. Hence, a major focus on battery research is to identify the most appropriate formulation so as to minimize interface reactions and enhance both cell performances and safety aspects. While a number of efforts are being directed to the search for new electrode materials for sodium ion batteries, studies dealing with the electrolyte are much scarcer. Still, some available reports demonstrate that the solid electrolyte interphase (SEI) formed on carbonaceous electrodes is markedly different Electrolytes are essential for the proper functioning of any battery technology, and the emerging Na-ion technology is no exception. Hence, a major focus on battery research is to identify the most appropriate formulation so as to minimize interface reactions and enhance both cell performances and safety aspects. While a number of efforts are being directed to the search for new electrode materials for sodium ion batteries, studies dealing with the electrolyte are much scarcer. Still, some available reports demonstrate that the solid electrolyte interphase (SEI) formed on carbonaceous electrodes is markedly different for sodium-and lithium-based electrolytes, even those using the same solvent. To investigate the effect of different electrolytes on the Na-ion storage performance of VS 4 nanorods electrodes, CR2032 coin-type cells were assembled to obtain the superior electrochemical properties by using 1 M NaClO 4 in ethylene carbonate/diethyl carbonate (1:1, v:v; EC/DEC), ethylene carbonate/dimethyl carbonate (1:1, v:v; EC/DMC), and tetraethylene glycol dimethyl ether (TEGDME) as electrolytes. The galvanostatic charge/discharge (GCD) profiles of pure VS 4 nanorods with the three selected electrolytes in the voltage range of 0.1-2.5 V at the current density of 0.1 C and 0.8 C are shown in Figure 4a-b. When the EC/DMC based electrolyte is used, the discharge specific capacity of VS 4 nanorods is 288 mAh/g at 0.1 C, which is higher than the other two electrolytes (Figure 4a). From Figure 4b and Table S1, taking the charge-discharge curve with a current density of 0.8 C as an example, when the electrolyte is EC/DMC, the Coulombic efficiency of the material is the highest (98%), indicating that the electrolyte can obtain the best electrochemical performance, and its charge-discharge capacity is 186, 190 mAh/g, respectively; when the electrolyte is EC/DEC, its coulombic efficiency is 92%, and the charge-discharge capacity is 148, 161 mAh/g, respectively; when the electrolyte is TEGDME, the coulombic efficiency is the lowest (90%), and the charge-discharge capacity is 96, 106 mAh/g. of the resulting electrolyte and thus increasing ionic mobility, its content should not be too large or too small. It should be optimal when its volume ratio to another solvent is 1:1.  Figure 5a presents the cyclic-voltammetry (CV) curves of the first three cycles of VS4/RGO as SIBs anode material, which are measured in the voltage of 0.1-2.5 V at the scan rate of 0.1 mV/s. During the initial cathodic sweep, a prominent cathodic peak is observed at 1.3 V and disappears in the subsequent cycles, which is ascribed to the formation process of the irreversible SEI film. The redox peaks in the subsequent cycles represent the multiple conversion reaction between VS4 and NaxVS4 [23], and the corresponding reaction equations are as follows: VS4 + x Na + +x e − → NaxVS4 (1) The CV profiles of VS4/RGO electrode materials overlap after the first cycle, indicating high chemical reversibility. The galvanostatic charge/discharge profiles of pure VS4 nanorods, VS4/RGO nanocomposites and RGO in the voltage range of 0.1-2.5 V at a current density of 0.1 C are shown in Figure S2 (Supplementary Material). The VS4/RGO elec- The rate performance of three electrolytes is summarized and compared at various current densities from 0.8 C to 1.6 C in Figure 4c. The capacities of VS 4 nanorods in the EC/DMC electrolyte are 288, 202, 174, 156 and 104 mAh/g at current densities of 0.1, 0.2, 0.4, 0.8 and 1.6 C, respectively. When the current density is restored to 0.1 C, the discharge specific capacity still remains a high reversible capacity of 280 mAh/g, demonstrating the remarkable rate performance of the samples. The corresponding GCD curves are presented in Figure 4d. The cycling performance at 0.4 C of VS 4 nanorods with different electrolytes are shown in Figure 4e. For the EC/DMC electrolyte, the initial discharge specific capacity of VS 4 is 440 mAh/g, corresponding to an initial coulombic efficiency (CE) of 70%. The irreversible capacity loss may be caused by the formation of an SEI film and the pre-activation process of electrode materials. The CE of VS 4 nanorods is close to 98% in the following cycles. The capacity of VS 4 nanorods is stable (182 mAh/g) after 100 cycles, indicating outstanding cycling stability compared to other electrolytes. To further explore the electrochemical performance and charge-transfer kinetics of the three electrolytes, electrochemical impedance spectroscopy analysis (EIS) was tested by the Nyquist plots (Figure 4f). The semicircle mainly reflects the charge transfer resistance (R c ) of the electrode, including an ohmic resistance (R 1 ) and a charge-transfer process (R c /C 2 ) of the electrolytes, as indicated in the proposed equivalent circuit. The ohmic resistance R 1 is related to the ionic conductivity of the discharge of the materials, and the Warburg impedance (W) responds to the diffusion of Na + ions [34,35]. As shown in Figure 4f, the significant difference between the three impedance spectra is that the EC/DMC (red line) has much lower (R c ) than the EC/DEC and TEGDME. Meanwhile, it was found that the EC/DMC electrolytes had higher frequencies in the onset between the semicircle and the slopping straight line than the control cell. This is another indication for the higher reaction kinetics of the EC/DMC electrolytes. Based on these results, the improved performance by EC/DMC electrolytes can be attributed to a smaller resistance (R c ), or in other words to an increase in the cell reaction kinetics of the EC/DMC electrolytes. All of the results demonstrate that the EC/DMC electrolyte contributes to the boosting of the Na-ion storage performance of VS 4 nanorods. To better understand this issue, the viscosity of binary solvent EC-based electrolytes, which are proportional to the viscosity of the co-solvent (EC:DEC > EC:DMC), is discussed, while in single solvent-based electrolytes (TEGDME), the viscosity of the electrolyte is higher, which also proves that the presence of EC can allow good dissociation of the salt. In addition, the electrochemical stability of the binary solvent-based electrolyte EC/DMC is greater than that of EC/DEC. Therefore, EC/DMC is the optimal electrolyte. Because EC is a co-solvent that increases ionic conductivity by improving salt dissociation (if the dielectric constant is high) and/or by reducing the viscosity of the resulting electrolyte and thus increasing ionic mobility, its content should not be too large or too small. It should be optimal when its volume ratio to another solvent is 1:1. Figure 5a presents the cyclic-voltammetry (CV) curves of the first three cycles of VS 4 /RGO as SIBs anode material, which are measured in the voltage of 0.1-2.5 V at the scan rate of 0.1 mV/s. During the initial cathodic sweep, a prominent cathodic peak is observed at 1.3 V and disappears in the subsequent cycles, which is ascribed to the formation process of the irreversible SEI film. The redox peaks in the subsequent cycles represent the multiple conversion reaction between VS 4 and Na x VS 4 [23], and the corresponding reaction equations are as follows: VS 4 + x Na + +x e − → Na x VS 4 (1) The CV profiles of VS 4 /RGO electrode materials overlap after the first cycle, indicating high chemical reversibility. The galvanostatic charge/discharge profiles of pure VS 4 nanorods, VS 4 /RGO nanocomposites and RGO in the voltage range of 0.1-2.5 V at a current density of 0.1 C are shown in Figure S2 (Supplementary Material). The VS 4 /RGO electrode exhibits superior sodium storage capacity (395 mAh/g) compared to VS 4 nanorods (300 mAh/g) and RGO (35 mAh/g) anodes. There are two advantages for the outstanding Na-ion storage performance of VS 4 /RGO nanocomposites: RGO, as one of the most desirable carbon materials, can enhance the electronic conductivity of VS 4 . Moreover, the large scale RGO nanosheets with abundant oxygen-containing functional groups can provide sufficient redox active sites to effectively alleviate the aggregation of VS 4 nanorods. When the current density is 0.4 C, for the EC/DMC electrolyte, the first-cycle discharge capacity of the VS 4 electrode material is 571 mAh/g, which is due to the irreversible capacity loss caused by the formation of the SEI film during the first charge-discharge process ( Figure S3 VS4 nanorods dispersed uniformly on the surface of RGO nanosheets with high conductivity, which provides sufficient conductive channels and electroactive sites for fast electron transport and sodium ions insertion/extraction and increases the effective contact between the surface of the electrode material and the electrolyte, thus facilitating the redox reactions. Furthermore, the introduction of layered RGO can offer a stable substrate for superior long-term cycling performance. Density functional theory (DFT) calculations were carried out to further illustrate the influence of electrolytes on VS4 nanorods. As shown in Figure 6, the solvation energy of 1 M NaClO4 in EC/DMC, EC/DEC and TEGDME electrolytes are −1.52606 eV, −1.54102 eV and −1.43974 eV, respectively ( Table 1). The lower solvation energy demonstrates a weak The rate capabilities of VS 4 nanorods and VS 4 /RGO nanocomposites are measured and compared at various current densities ( Figure 5b). As the current density increases from 0.1 C to 1.6 C, the discharge capacity of VS 4 /RGO nanocomposites slowly delay. When returning to the initial density of 0.1 C, the average capacity of hybrid electrode materials remains about 400 mAh/g. As a consequence, Figure 5c demonstrates the cycling performance of VS 4 and VS 4 /RGO at the current density of 1.6 C. A long-term and stable cycling performance of VS 4 /RGO nanocomposites is achieved with the discharge capacity retention of 100 mAh/g over 2000 cycles. This is closely related to the layer structure of VS 4 nanorods dispersed uniformly on the surface of RGO nanosheets with high conductivity, which provides sufficient conductive channels and electroactive sites for fast electron transport and sodium ions insertion/extraction and increases the effective contact between the surface of the electrode material and the electrolyte, thus facilitating the redox reactions. Furthermore, the introduction of layered RGO can offer a stable substrate for superior long-term cycling performance.
Density functional theory (DFT) calculations were carried out to further illustrate the influence of electrolytes on VS 4 nanorods. As shown in Figure 6, the solvation energy of 1 M NaClO 4 in EC/DMC, EC/DEC and TEGDME electrolytes are −1.52606 eV, −1.54102 eV and −1.43974 eV, respectively ( Table 1). The lower solvation energy demonstrates a weak interaction between salt and solvent, favoring Na + diffusion and desolvation. For carbonatebased electrolytes (EC/DMC and EC/DEC), the values of solvation energy is very close. In addition, the LUMO energy of EC/DMC electrolyte (−0.61146 eV) is lower than that of EC/DEC (−0.66178 eV) and TEGDME (−0.74174 eV), suggesting that it is easier to reduce [32]. Electrolyte ionic conductivity is one of the most crucial factors for sodium ion storage performance [36]. Therefore, the electrical conductivity and viscosity of three electrolytes are also measured (Table S2 and Figure S4, Supplementary Materials). The highest conductivity value of 1 M NaClO 4 in EC/DMC electrolyte is presented (7.88 mS/cm) due to its lower viscosity values as compared to other electrolytes. In conclusion, the lower viscosity of an electrolyte can improve the ionic mobility. These results indicate that an optimized EC/DMC electrolyte can facilitate Na-ion diffusion/desolvation for superior cycling stability of electrode materials.
close. In addition, the LUMO energy of EC/DMC electrolyte (−0.61146 eV) is lower than that of EC/DEC (−0.66178 eV) and TEGDME (−0.74174 eV), suggesting that it is easier to reduce [32]. Electrolyte ionic conductivity is one of the most crucial factors for sodium ion storage performance [36]. Therefore, the electrical conductivity and viscosity of three electrolytes are also measured (Table S2 and Figure S4, Supplementary Materials). The highest conductivity value of 1 M NaClO4 in EC/DMC electrolyte is presented (7.88 mS/cm) due to its lower viscosity values as compared to other electrolytes. In conclusion, the lower viscosity of an electrolyte can improve the ionic mobility. These results indicate that an optimized EC/DMC electrolyte can facilitate Na-ion diffusion/desolvation for superior cycling stability of electrode materials.

Synthesis of VS4 Nanorods and VS4/RGO Nanocomposite
All chemical reagents used in the experiments were of analytical grade without further purification. In a typical fabrication process, 2 mmol ammonium vanadate (NH4VO3) was first dissolved in 30 mL deionized water/ethanol (1:1) mixed solution and stirred vigorously for 1 h at room temperature to form a homogeneous suspension, followed by the addition of 10 mmol thioacetamide (CH3CSNH2). The obtained precursor suspension was then transferred to a 50 mL Teflon-lined stainless-steel autoclave and heated at 160 °C for 12 h. After naturally cooling down to room temperature, the precipitate was filtered and washed thoroughly with deionized water and absolute ethanol for several times, and dried in a vacuum oven at 60 °C overnight. For comparison, 50 mg of graphene oxide (GO) power prepared by the modified Hummers method [37] was dispersed into the above suspension of VS4 nanorods and then underwent a similar procedure of solvothermal

Synthesis of VS 4 Nanorods and VS 4 /RGO Nanocomposite
All chemical reagents used in the experiments were of analytical grade without further purification. In a typical fabrication process, 2 mmol ammonium vanadate (NH 4 VO 3 ) was first dissolved in 30 mL deionized water/ethanol (1:1) mixed solution and stirred vigorously for 1 h at room temperature to form a homogeneous suspension, followed by the addition of 10 mmol thioacetamide (CH 3 CSNH 2 ). The obtained precursor suspension was then transferred to a 50 mL Teflon-lined stainless-steel autoclave and heated at 160 • C for 12 h. After naturally cooling down to room temperature, the precipitate was filtered and washed thoroughly with deionized water and absolute ethanol for several times, and dried in a vacuum oven at 60 • C overnight. For comparison, 50 mg of graphene oxide (GO) power prepared by the modified Hummers method [37] was dispersed into the above suspension of VS 4 nanorods and then underwent a similar procedure of solvothermal treatment. Finally, the precursors were annealed at 400 • C for 1 h to thermally reduce GO to RGO to obtain the VS 4 /RGO nanocomposite.

Material Characterizations
The phase purity and crystal structure of the products were investigated by X-ray diffraction on a MiniFlex 600 (Rigaku, Tokyo, Japan) with Cu Kα radiation (λ = 0.15406 nm) under the accelerated voltage and current of 40 kV and 15 mA, respectively. The morphology and microstructure of as-prepared samples were characterized by field emission scanning electron microscopy (FESEM, SU-8020) (Hitachi High-Technologies Corporation, Japan.) and transmission electron microscopy (TEM, JEM-2800) (JEOL, Tokyo, Japan) with an energy dispersive X-ray detector (EDX). Raman spectra were examined using a Ren-ishaw in Via Raman microscope (Renishaw, Wotton-under-Edge, UK) with an excitation wavelength of 532 nm.

Electrochemical Measurements
Electrochemical tests were evaluated by assembling CR2032 coin type half-cells in an argon-filled glove box (O 2 < 0.1 ppm, H 2 O < 0.1 ppm). The working electrodes were fabricated by mixing 70 wt% of as-prepared active materials, 20 wt% acetylene black and 10 wt% polyvinylidene fluoride (PVDF) binder using N-methyl pyrrolidone as solvent and the mass loading of an electrode of 0.62 mg/cm 2 . Sodium disks were cut into a round shape with 13 mm and employed as the counter electrode and glass fiber was used as the separator. The obtained homogeneous slurry was coated onto the current collector (Al foil) and dried in a vacuum oven at 60 • C overnight. In the cells, 1 M NaClO 4 in ethylene carbonate/diethyl carbonate (EC/DEC, 1:1 v/v), ethylene carbonate/dimethyl carbonate (EC/DMC, 1:1 v/v) with the addition of 5% fluoroethylene carbonate, and tetraethylene glycol dimethyl ether (TEGDME) were used as the electrolytes for SIBs. Galvanostatic discharge/charge tests were collected on a Neware multichannel battery system between 0.1 V and 2.5 V. Cyclic voltammetry (CV) profiles were carried out using a CHI660E electrochemical analyzer (CH Instruments Inc., Shanghai, China) and electrochemical impedance spectroscopy (EIS) was performed on an Autolab electrochemical workstation.

Conclusions
In summary, VS 4 nanorods with an average diameter of 30 nm were successfully prepared by a fast and simple one-pot solvothermal process. To further increase the electric conductivity of VS 4 materials and improve the electron transportation, small VS 4 nanorods were uniformly anchored into the conductive network of large-sized RGO nanosheets to obtain VS 4 /RGO nanocomposites. When tested as anode materials at the half-cell of SIBs, VS 4 nanorods in the EC/DMC electrolyte exhibit outstanding electrochemical performance in terms of a high reversible capacity (185 mAh/g at a current density of 0.8 C), good rate capability and long cycle life (182 mAh/g after 100 cycles at 0.4 C) compared to the EC/DEC and TEGDME electrolytes. This is ascribed to the high ionic conductivity, lower solvation energy and LUMO energy for the EC/DMC electrolyte, which is favorable for Na + diffusion and desolvation. Moreover, VS 4 /RGO nanocomposites can deliver a discharge capacity of 100 mAh/g after 2000 cycles at a large current density of 1.6 C, which indicates excellent long-term cycling properties compared to pure VS 4 nanorods. The outstanding electrochemical performance of VS 4 /RGO nanocomposites is mainly attributed to the synergistic effect between the introduction of graphene, the rational synthesis of VS 4 nanorods and the optical electrolytes, which can effectively shorten the transportation path for electrons/ions, meanwhile greatly improving the electronic conductivity and structure stability of electrode materials.

Supplementary Materials:
The following supporting information can be downloaded at: https: //www.mdpi.com/article/10.3390/molecules27196303/s1, Figure S1: Raman spectrum of VS 4 /RGO nanocomposites; Figure S2: Galvanostatic charge and discharge profiles at the current density of 0.1 C of VS 4 /RGO nanocomposites in comparison with VS 4 nanorods and RGO; Figure S3. Electrochemical measurements of VS 4 nanorods with different electrolytes: the charge-discharge curves of the first cycle at the current density of 0.4 C; Figure S4. Conductivity and viscosity distribution of VS 4 nanorods with various electrolytes; Table S1. Coulombic efficiencies of VS 4 electrode materials under three electrolyte conditions at a current density of 0.8 C; Table S2: The electrical conductivity and viscosity of three electrolytes.