Reduced Graphene Oxide-Wrapped Novel CoIn2S4 Spinel Composite Anode Materials for Li-ion Batteries

In this study, we proposed a novel CoIn2S4/reduced graphene oxide (CoIn2S4/rGO) composite anode using a hydrothermal method. By introducing electronic-conductive reduced graphene oxide (rGO) to buffer the extreme volume expansion of CoIn2S4, we prevented its polysulfide dissolution during the lithiation/de-lithiation processes. After 100 cycles, the pristine CoIn2S4 electrode demonstrated poor cycle performance of only 120 mAh/g at a current density of 0.1 A/g. However, the composition-optimized CoIn2S4/rGO composite anode demonstrated a reversible capacity of 580 mAh/g for 100 cycles, which was an improvement of 4.83 times. In addition, the ex situ XRD measurements of the CoIn2S4/rGO electrode were conducted to determine the reaction mechanism and electrochemical behavior. These results suggest that the as-synthesized CoIn2S4/rGO composite anode is a promising anode material for lithium ion batteries.


Introduction
Technological development and economic growth have led to an increase in energy demands. As a renewable energy, lithium-ion batteries (LIBs) are regarded as the most promising energy storage and conversion materials [1,2]. Their long cycle life and high energy density have afforded them widespread adoption and applications in various areas, including electric vehicles and portable electronic devices [3][4][5]. Graphite is the current commercially available material for LIBs. However, the energy and power density of graphite anodes are insufficient for electric-powered vehicles [6,7]. To replace graphite, scientists are urgently developing novel materials with greater reversible capacity.
According to the storage mechanisms of lithium ions, anode materials are categorized as intercalation based, alloy based, and conversion based. Among these anodes, conversion anodes have garnered great interest due to their high theoretical capacity and remarkable stability for lithium storage. Transition metal sulfides (TMSs), such as Co 9 S 8 [8][9][10], Co 3 S 4 [11,12], CoS [13][14][15], CuS [16][17][18], and NiS [19,20], are some of the most well-known conversion-based anodes because they are inexpensive and environmentally friendly. Compared to the preceding metal sulfides, bimetallic sulfides have superior electrochemical performance. Bimetallic sulfides can provide sufficient active sites and have a higher specific capacity than sulfides composed of a single metal. For bimetallic sulfides, the characteristics of spinel-based metal sulfides have garnered considerable interest because they can result in greater ionic conductivity [21][22][23][24][25]. Verma et al. [26] successfully synthesized carbon-coated CuCo 2 S 4 anode materials for LIBs using a straightforward in situ hydrothermal method. A composition-optimized CuCo 2 S 4 /C composite anode exhibited 361 mAh/g of reversible capacity after 30 cycles at 0.2C current density. In contrast, the CuCo 2 S 4 anode's reversible capacity after 30 cycles at the same current density was only 175 mAh/g. Introducing in situ carbon-coating technology decreased the SEI film resistance and charge transfer resistance, as demonstrated by a Nyquist plot. By altering the solvent ratio of

Synthesis of Pristine CoIn 2 S 4 and CoIn 2 S 4 /rGO Composite
The Hummers' technique was adapted to synthesize GO [31]. CoIn 2 S 4 /rGO was prepared via a simple hydrothermal process. Initially, GO powder was ultrasonically dispersed in 50 mL of deionized (DI) water for 30 min. Subsequently, 1 mmol of Co(NO 3 ) 2 ·6H 2 O (Cobalt(II) nitrate, 98%, SHOWA), 2 mmol of In(NO 3 ) 3 (Indium nitrate, 99.99%, Alfa Aesar, MA, USA), and 8 mmol of CH 3 CSNH 2 (Thioacetamide, 99%, Alfa Aesar, Haverhill) were added to the above solution and stirred for 2 h. Then 15 mmol of CH 4 N 2 O (Urea, 99%, Sigma Aldrich, St. Louis, MO, USA) was added dropwise. After vigorously stirring the mixture for 1 h, it was placed in a 100 mL Teflon-lined stainless steel autoclave and heated at 180 • C for 24 h. The CoIn 2 S 4 powder was obtained by high-speed centrifugation and multiple washes with DI water and ethanol at room temperature before natural cooling. The samples were then vacuum-dried at 70 • C for 12 h. In contrast, pristine CoIn 2 S 4 was synthesized via a similar procedure, excluding the addition of GO to the mixture solution (Scheme 1). centrifugation and multiple washes with DI water and ethanol at room temperature before natural cooling. The samples were then vacuum-dried at 70 °C for 12 h. In contrast, pristine CoIn2S4 was synthesized via a similar procedure, excluding the addition of GO to the mixture solution (Scheme 1).

Characterizations
The crystal structure of the as-prepared sample was confirmed by X-ray diffraction (XRD, Bruker D2 phaser). The morphology of the samples was analyzed using a scanning electron microscope (SEM, JEOL JSM-7600M) equipped with energy-dispersive X-ray spectroscopy (EDX) and a high-resolution transmission electron microscope (HRTEM, Hitachi, H-7100). X-ray photoelectron spectroscopy (XPS, Thermo Fisher Scientific, Waltham, MA, USA) was utilized to determine the elementary binding state and valences. Using the Brunauer-Emmett-Teller (BET) method based on the N2 adsorption-desorption isotherms obtained with a Micromeritics Tristar 3000, the specific surface area of the samples was determined.

Electrochemical Measurements
Active materials, conductive additive (Super-P), and binder (polyvinylidene fluoride, PVDF) were mixed at a weight ratio of 8:1:1 in NMP solvent (N-methyl-2-pyrrolidone) to form the working electrode. This slurry was then used to coat a 10 μm thick copper foil current collector. The electrode was punched into a 14 mm diameter circle before being vacuum-dried at 120 °C for 8 h. The coin-type half cells (CR2032) were assembled in an argon-filled glovebox. Here, less than 0.5 ppm of oxygen and moisture levels must be maintained. Next, 1M LiPF6 was dissolved in a 1:1:1 wt% solution of ethylene carbonate, ethyl methyl carbonate, and dimethyl carbonate (EC:EMC:DMC). The separator we used was a 25 μm trilayer Celgard 2325. The counter was lithium foil with a thickness of 200 μm. The coin cells (CR2032) were tested in the potential range of 0.01-3.0 V at various current densities to determine their stability. The electrochemical workstation (CH Instruments Analyzer CHI 6273E) with a potential range of 0.01-3.0 V and a scan rate of 0.1 mV/s was used to test the cyclic voltammetry (CV) investigations. The frequency ranges for electrochemical impedance spectroscopy (EIS) were 1 MHz-10 mHz.

Characterizations
The crystal structure of the as-prepared sample was confirmed by X-ray diffraction (XRD, Bruker D2 phaser). The morphology of the samples was analyzed using a scanning electron microscope (SEM, JEOL JSM-7600M) equipped with energy-dispersive X-ray spectroscopy (EDX) and a high-resolution transmission electron microscope (HRTEM, Hitachi, H-7100). X-ray photoelectron spectroscopy (XPS, Thermo Fisher Scientific, Waltham, MA, USA) was utilized to determine the elementary binding state and valences. Using the Brunauer-Emmett-Teller (BET) method based on the N 2 adsorption-desorption isotherms obtained with a Micromeritics Tristar 3000, the specific surface area of the samples was determined.

Electrochemical Measurements
Active materials, conductive additive (Super-P), and binder (polyvinylidene fluoride, PVDF) were mixed at a weight ratio of 8:1:1 in NMP solvent (N-methyl-2-pyrrolidone) to form the working electrode. This slurry was then used to coat a 10 µm thick copper foil current collector. The electrode was punched into a 14 mm diameter circle before being vacuum-dried at 120 • C for 8 h. The coin-type half cells (CR2032) were assembled in an argon-filled glovebox. Here, less than 0.5 ppm of oxygen and moisture levels must be maintained. Next, 1M LiPF 6 was dissolved in a 1:1:1 wt% solution of ethylene carbonate, ethyl methyl carbonate, and dimethyl carbonate (EC:EMC:DMC). The separator we used was a 25 µm trilayer Celgard 2325. The counter was lithium foil with a thickness of 200 µm. The coin cells (CR2032) were tested in the potential range of 0.01-3.0 V at various current densities to determine their stability. The electrochemical workstation (CH Instruments Analyzer CHI 6273E) with a potential range of 0.01-3.0 V and a scan rate of 0.1 mV/s was used to test the cyclic voltammetry (CV) investigations. The frequency ranges for electrochemical impedance spectroscopy (EIS) were 1 MHz-10 mHz.

Results and Discussion
The XRD patterns of bare CoIn 2 S 4 and CoIn 2 S 4 /rGO composites ( Figure 1a) were tested from 10 to 80 • . All the diffraction peaks were consistent with CoIn 2 S 4 (ICSD 76-1973). In addition, the diffraction peaks of CoIn 2 S 4 /rGO at 28, 34, 44, and 48 • were attributed to the (311), (400), (511), and (440) crystal planes of CoIn 2 S 4 . Figure 1b depicts the crystal structure of CoIn 2 S 4 . The CoIn 2 S 4 possessed a cubic crystal structure with the space group Fd3m. Cobalt cations were placed in tetrahedral 8a sites, indium cations in octahedral 16d sites, and sulfur anions in tetrahedral 32e sites to form the corner-sharing tetrahedral network. 3 . Cobalt cations were placed in tetrahedral 8a sites, indium cations in octahedral 16d sites, and sulfur anions in tetrahedral 32e sites to form the corner-sharing tetrahedral network. SEM and HRTEM were used to examine the surface morphologies of the as-prepared samples. As depicted in Figure 2a,b, the as-synthesized CoIn2S4 exhibited an irregular morphology, a relatively smooth surface, and inhomogeneous diameters of about 1-2 μm. The EDS mapping of CoIn2S4 is shown in Figure 2c. The computed molar concentrations of Co, In, and S in CoIn2S4 were 6.70, 29.59, and 63.71%, respectively. In addition, the SEM image and the corresponding elemental mapping of the CoIn2S4/rGO composite ( Figure 3) revealed a uniform distribution of Co, In, S and C. The surface morphology and microstructure of pristine CoIn2S4 and as-synthesized CoIn2S4/rGO composite were further characterized by TEM. Figure 4a,b reveals the CoIn2S4 sample at various magnifications. The HRTEM images revealed that the (311) plane of CoIn2S4 was composed of prominent lattice fingers with 0.32 nm interspaces. The TEM images of the CoIn2S4/rGO composite are displayed in Figure 4c,d. The particle size of the as-synthesized CoIn2S4 was about 1 μm. Moreover, rGO was uniformly anchored with CoIn2S4. The selected area electron diffraction pattern (SAED) of the CoIn2S4/rGO sample is shown in the inset of Figure 4c. The SAED pattern revealed the halo of concentric circles. CoIn2S4 was indexed in the (311), (400), (511), and (620) planes for the various rings. We utilized BET analyses to examine the pore size distribution and specific surface area of pristine CoIn2S4 and CoIn2S4/rGO composites. Both CoIn2S4 and CoIn2S4/rGO samples exhibited the characteristic III isotherm curves of mesoporous materials. SEM and HRTEM were used to examine the surface morphologies of the as-prepared samples. As depicted in Figure 2a,b, the as-synthesized CoIn 2 S 4 exhibited an irregular morphology, a relatively smooth surface, and inhomogeneous diameters of about 1-2 µm. The EDS mapping of CoIn 2 S 4 is shown in Figure 2c. The computed molar concentrations of Co, In, and S in CoIn 2 S 4 were 6.70, 29.59, and 63.71%, respectively. 3 . Cobalt cations were placed in tetrahedral 8a sites, indium cations in octahedral 16d sites, and sulfur anions in tetrahedral 32e sites to form the corner-sharing tetrahedral network. SEM and HRTEM were used to examine the surface morphologies of the as-prepared samples. As depicted in Figure 2a,b, the as-synthesized CoIn2S4 exhibited an irregular morphology, a relatively smooth surface, and inhomogeneous diameters of about 1-2 μm. The EDS mapping of CoIn2S4 is shown in Figure 2c. The computed molar concentrations of Co, In, and S in CoIn2S4 were 6.70, 29.59, and 63.71%, respectively. In addition, the SEM image and the corresponding elemental mapping of the CoIn2S4/rGO composite ( Figure 3) revealed a uniform distribution of Co, In, S and C. The surface morphology and microstructure of pristine CoIn2S4 and as-synthesized CoIn2S4/rGO composite were further characterized by TEM. Figure 4a,b reveals the CoIn2S4 sample at various magnifications. The HRTEM images revealed that the (311) plane of CoIn2S4 was composed of prominent lattice fingers with 0.32 nm interspaces. The TEM images of the CoIn2S4/rGO composite are displayed in Figure 4c,d. The particle size of the as-synthesized CoIn2S4 was about 1 μm. Moreover, rGO was uniformly anchored with CoIn2S4. The selected area electron diffraction pattern (SAED) of the CoIn2S4/rGO sample is shown in the inset of Figure 4c. The SAED pattern revealed the halo of concentric circles. CoIn2S4 was indexed in the (311), (400), (511), and (620) planes for the various rings. We utilized BET analyses to examine the pore size distribution and specific surface area of pristine CoIn2S4 and CoIn2S4/rGO composites. Both CoIn2S4 and CoIn2S4/rGO samples exhibited the characteristic III isotherm curves of mesoporous materials. In addition, the SEM image and the corresponding elemental mapping of the CoIn 2 S 4 / rGO composite ( Figure 3) revealed a uniform distribution of Co, In, S and C. The surface morphology and microstructure of pristine CoIn 2 S 4 and as-synthesized CoIn 2 S 4 /rGO composite were further characterized by TEM. Figure 4a,b reveals the CoIn 2 S 4 sample at various magnifications. The HRTEM images revealed that the (311) plane of CoIn 2 S 4 was composed of prominent lattice fingers with 0.32 nm interspaces. The TEM images of the CoIn 2 S 4 /rGO composite are displayed in Figure 4c,d. The particle size of the as-synthesized CoIn 2 S 4 was about 1 µm. Moreover, rGO was uniformly anchored with CoIn 2 S 4 . The selected area electron diffraction pattern (SAED) of the CoIn 2 S 4 /rGO sample is shown in the inset of Figure 4c. The SAED pattern revealed the halo of concentric circles. CoIn 2 S 4 was indexed in the (311), (400), (511), and (620) planes for the various rings. We utilized BET analyses to examine the pore size distribution and specific surface area of pristine CoIn 2 S 4 and CoIn 2 S 4 /rGO composites. Both CoIn 2 S 4 and CoIn 2 S 4 /rGO samples exhibited the characteristic III isotherm curves of mesoporous materials. Figure 5a,c depicts the specific surface area of pristine CoIn 2 S 4 and CoIn 2 S 4 /rGO composites. The specific surface areas of CoIn 2 S 4 and CoIn 2 S 4 /rGO composites were 47.82 and 7.99 m 2 /g, respectively. After adding rGO, the surface area of CoIn 2 S 4 decreased, indicating that rGO completely encapsulated the CoIn 2 S 4 samples. The BJH method was used to calculate the pore size distributions of pristine CoIn 2 S 4 and the CoIn 2 S 4 /rGO composite, as shown in Figure 5b,         The chemical valence state, binding information, and surface elemental composition of the as-synthesized CoIn 2 S 4 /rGO composite were investigated using XPS. As shown in Figure 6a, the deconvolution of Co 2p 1/2 and Co 2p 3/2 resulted in two peaks attributable to Co 3+ (782.9 and 798.0 eV) and Co 2+ (778.3 and 784.3 eV), respectively. The In 3d spectrum consisted of two peaks: In 3d 3/2 (452.3 eV) and In 3d 5/2 (444.9 eV). As shown in Figure 6c, the spectrum of S 2p consisted of three principal peaks and a sulfate peak (169.2 eV). The peaks at 161.8 eV and 162.9 eV corresponded to the 2p 3/2 and 2p 1/2 spectra of S, while the peak at 163.3 eV corresponded to the sulfur-metal (S-M) bond. The peak of S-M (M=Co or In) may provide additional evidence for the formation of CoIn 2 S 4 . Figure 6d depicts the C 1s XPS peak of the CoIn 2 S 4 /rGO composite. The binding energies of 284.2, 284.8, 285.7, and 287.1 eV were associated with C=C-C, C-H/C-C, C-O, and O-C=O, respectively. Consequently, the XPS results confirmed that we successfully obtained a purephased CoIn 2 S 4 /rGO composite with strong chemical bonds via the hydrothermal method. Figure S1 and Table S1 show XPS survey of as-synthesized CoIn 2 S 4 /rGO composite and elemental analysis of CoIn 2 S 4 /rGO based on XPS survey, respectively. The rGO content in CoIn 2 S 4 /rGO composite was estimated to be 25.78 wt%, which was very closed to theoretical values of rGO content of 30 wt%. The chemical valence state, binding information, and surface elemental composition of the as-synthesized CoIn2S4/rGO composite were investigated using XPS. As shown in Figure 6a, the deconvolution of Co 2p1/2 and Co 2p3/2 resulted in two peaks attributable to Co 3+ (782.9 and 798.0 eV) and Co 2+ (778.3 and 784.3 eV), respectively. The In 3d spectrum consisted of two peaks: In 3d3/2 (452.3 eV) and In 3d5/2 (444.9 eV). As shown in Figure 6c, the spectrum of S 2p consisted of three principal peaks and a sulfate peak (169.2 eV). The peaks at 161.8 eV and 162.9 eV corresponded to the 2p3/2 and 2p1/2 spectra of S, while the peak at 163.3 eV corresponded to the sulfur-metal (S-M) bond. The peak of S-M (M=Co or In) may provide additional evidence for the formation of CoIn2S4. Figure 6d depicts the C 1s XPS peak of the CoIn2S4/rGO composite. The binding energies of 284.2, 284.8, 285.7, and 287.1 eV were associated with C=C-C, C-H/C-C, C-O, and O-C=O, respectively. Consequently, the XPS results confirmed that we successfully obtained a pure-phased CoIn2S4/rGO composite with strong chemical bonds via the hydrothermal method. Figure  S1 and Table S1 show XPS survey of as-synthesized CoIn2S4/rGO composite and elemental analysis of CoIn2S4/rGO based on XPS survey, respectively. The rGO content in CoIn2S4/rGO composite was estimated to be 25.78 wt%, which was very closed to theoretical values of rGO content of 30 wt%. The charge/discharge profiles of the as-synthesized CoIn2S4/rGO electrode at 0.1 A/g for the first three cycles are depicted in Figure 7a. In the first cycle, the charge and discharge capacities of CoIn2S4/rGO were 1180 and 850 mAh/g, respectively. At the beginning of the cycle, the coulombic efficiency was 72%. However, the charge and discharge capacities of CoIn2S4/rGO were 838 and 805 mAh/g with a 96% coulombic efficiency after three cycles. The irreversible capacity fading is attributable to the irreversible decomposition of the liquid electrolyte during charging, forming an SEI layer. Figure 7b depicts the rate capability tests of pristine CoIn2S4 and CoIn2S4/rGO electrodes with varying current den- The charge/discharge profiles of the as-synthesized CoIn 2 S 4 /rGO electrode at 0.1 A/g for the first three cycles are depicted in Figure 7a. In the first cycle, the charge and discharge capacities of CoIn 2 S 4 /rGO were 1180 and 850 mAh/g, respectively. At the beginning of the cycle, the coulombic efficiency was 72%. However, the charge and discharge capacities of CoIn 2 S 4 /rGO were 838 and 805 mAh/g with a 96% coulombic efficiency after three cycles. The irreversible capacity fading is attributable to the irreversible decomposition of the liquid electrolyte during charging, forming an SEI layer. Figure 7b depicts the rate capability tests of pristine CoIn 2 S 4 and CoIn 2 S 4 /rGO electrodes with varying current densities. The charge capacities of the CoIn 2 S 4 /rGO electrode were 781, 680, 574, 478, 277, and 265 mAh/g at current densities of 0.1, 0.2, 0.5, 1, 2, and 5 A/g, respectively. When the current density was switched back to 0.1 A/g, the reversible capacity of CoIn 2 S 4 /rGO was 563 mAh/g. Figure 7c depicts the cycle performance of bare CoIn 2 S 4 and CoIn 2 S 4 /rGO composites. The initial current density used for electrode formation was 0.1A/g. Between the fourth and hundredth cycles, the current density decreased to 0.2 A/g. After 100 cycles, the pristine CoIn 2 S 4 exhibited a capacity of 84 mAh/g. The rGO matrix buffered the dramatic volume expansion of CoIn 2 S 4 during the lithiation and de-lithiation processes, resulting in a higher reversible capacity of 670 mAh/g for the CoIn 2 S 4 /rGO electrode. where R is the ideal gas constant; T is room temperature; A is the surface area of the electrode; n is the number of electrons; F is the Faraday constant; C is the concentration of Li + ; σ is the slope of the fitting line. As a result, there is a linear relationship between Z' and ω −1/2 of the pristine CoIn2S4 and the as-synthesized CoIn2S4/rGO composites. The diffusion coefficients of pristine CoIn2S4 and CoIn2S4/rGO were calculated to be 2.29 × 10 −14 cm 2 /s and 9.38 × 10 −14 cm 2 /s, respectively. The CoIn2S4/rGO electrode had nearly four times the DLi + value of the pristine CoIn2S4 electrode.  The reduction and oxidation potentials of CoIn2S4/rGO were determined in the potential range of 0.01 V-3.0 V (V vs. Li/Li + ) using cyclic voltammetry (CV) measurements. As demonstrated in Figure 9a, the irreversible peak at 1.1 V in the initial lithiation process is attributable to the reduction of CoIn2S4 to metal Co. [27,[32][33][34] The formation of SEI  Figure 8a depicts the electrochemical impedance spectroscopy (EIS) plots of pristine CoIn 2 S 4 and CoIn 2 S 4 /rGO composites after 2.5 cycles. The semicircle in the middle frequency range represents the solid electrolyte interphase (SEI) resistance (R SEI ) and charge transfer resistance (R ct ) at the electrode/electrolyte interface. The straight line in the lowfrequency region is related to the diffusion resistance of lithium ions. The R SEI /R CT values of pristine CoIn 2 S 4 and CoIn 2 S 4 /rGO composites were 145.7/125.9 Ω and 68.3/14.0 Ω, respectively, based on the equivalent circuit fitting results. Due to the contribution of the rGO matrix, both SEI and charge transfer resistances for CoIn 2 S 4 /rGO decreased, indicating improved electronic conductivity of the electrode and enhanced electrochemical kinetics. To interpret the kinetic behavior of the electrochemical reaction, the Li + diffusion coefficient (D Li + ) is calculated. D Li + can be defined as: where R is the ideal gas constant; T is room temperature; A is the surface area of the electrode; n is the number of electrons; F is the Faraday constant; C is the concentration of Li + ; σ is the slope of the fitting line. As a result, there is a linear relationship between Z' and ω −1/2 of the pristine CoIn 2 S 4 and the as-synthesized CoIn 2 S 4 /rGO composites. The diffusion coefficients of pristine CoIn 2 S 4 and CoIn 2 S 4 /rGO were calculated to be 2.29 × 10 −14 cm 2 /s and 9.38 × 10 −14 cm 2 /s, respectively. The CoIn 2 S 4 /rGO electrode had nearly four times the D Li + value of the pristine CoIn 2 S 4 electrode.  The reduction and oxidation potentials of CoIn2S4/rGO were determined in the potential range of 0.01 V-3.0 V (V vs. Li/Li + ) using cyclic voltammetry (CV) measurements. As demonstrated in Figure 9a, the irreversible peak at 1.1 V in the initial lithiation process is attributable to the reduction of CoIn2S4 to metal Co. [27,[32][33][34] The formation of SEI during the first cathodic cycle is attributable to the 0.6 V reduction peak. The reversible peaks at 0.7, 1.6, and 1.9 V in the first anodic cycle can be ascribed to the oxidation of Co and in [28,29]. The cathodic peaks shifted to a higher potential in subsequent cycles than The reduction and oxidation potentials of CoIn 2 S 4 /rGO were determined in the potential range of 0.01 V-3.0 V (V vs. Li/Li + ) using cyclic voltammetry (CV) measurements. As demonstrated in Figure 9a, the irreversible peak at 1.1 V in the initial lithiation process is attributable to the reduction of CoIn 2 S 4 to metal Co. [27,[32][33][34] The formation of SEI during the first cathodic cycle is attributable to the 0.6 V reduction peak. The reversible peaks at 0.7, 1.6, and 1.9 V in the first anodic cycle can be ascribed to the oxidation of Co and in [28,29]. The cathodic peaks shifted to a higher potential in subsequent cycles than in the first. The activation phase can be distinguished during the initial discharge. Moreover, the CV curves of the CoIn 2 S 4 /rGO composite during the second and third lithiation/delithiation cycles nearly overlapped, demonstrating excellent cycling stability. To clarify the lithium reaction mechanism, ex situ XRD analyses of the CoIn 2 S 4 /rGO electrode were also performed (Figure 9b). At 28, 34, and 48 • , three diffraction peaks were observed for the fresh CoIn 2 S 4 /rGO electrode, attributed to the (311), (400), and (440) planes of the CoIn 2 S 4 . After charging to 1.4 V (lithiation), the corresponding peaks of CoIn 2 S 4 disappeared, suggesting that Co metal was produced first during the conversion of CoIn 2 S 4 . At the end of the charge stage (0.01 V), the peak at 2Θ = 33 • represented the In metal diffraction peak. Next, it was demonstrated that there was no obvious peak during the subsequent lithiation. Based on ex situ XRD results, the following reaction mechanism for CoIn 2 S 4 with Li ions was proposed: The reversible capacity of rGO decreased with the increase in sintering temperature from~1000 to~200 mAh/g, which resulted from the content and types of functional groups in rGO. In this study, we used 350 • C as the sintering temperature, thus, the reversible capacity of rGO-350 • C was~1250 mAh/g. The theoretical capacity of CoIn 2 S 4 was 514.4 mAh/g. In this study, we introduced 30% rGO in the CoIn 2 S 4 anode. So, the reversible capacity of CoIn 2 S 4 /rGO was 1250 × 0.3 + 514.4 × 0.7 = 375 + 360.08 = 735 mAh/g. That is the reason why our CoIn 2 S 4 /rGO exceeded the theoretical capacity of CoIn 2 S 4 . peared, suggesting that Co metal was produced first during the conversion of CoIn2S4. At the end of the charge stage (0.01 V), the peak at 2Θ = 33° represented the In metal diffraction peak. Next, it was demonstrated that there was no obvious peak during the subsequent lithiation. Based on ex situ XRD results, the following reaction mechanism for CoIn2S4 with Li ions was proposed: CoIn2S4 + 8Li + + 8e - Co + 2In + 4Li2S (1) Figure 9. (a) CV curves of CoIn2S4/rGO at a scan rate of 0.1 mV/s in the first three cycles; (b) ex situ XRD measurements of as-synthesized CoIn2S4/rGO electrodes after different charge and discharge states; (c) the corresponding discharge/charge profile of CoIn2S4/rGO electrodes of potential indication at the 1st cycle.
The reversible capacity of rGO decreased with the increase in sintering temperature from ~1000 to ~200 mAh/g, which resulted from the content and types of functional groups in rGO. In this study, we used 350°C as the sintering temperature, thus, the reversible capacity of rGO-350 °C was ~1250 mAh/g. The theoretical capacity of CoIn2S4 was 514.4 mAh/g. In this study, we introduced 30% rGO in the CoIn2S4 anode. So, the reversible capacity of CoIn2S4/rGO was 1250 × 0.3 + 514.4 × 0.7 = 375 + 360.08 = 735 mAh/g. That is the reason why our CoIn2S4/rGO exceeded the theoretical capacity of CoIn2S4. Figure 10a,b depicts SEM images of pristine CoIn2S4 and CoIn2S4/rGO electrodes before cycling. There was no discernible distinction between the two electrodes. After 30 cycles of discharge/charge testing, the surface morphology of the pristine CoIn2S4 electrode, as depicted in Figure 10c, exhibited voids and fractures. Nevertheless, the CoIn2S4/rGO electrode (Figure 10d) maintained its compact structure and surface morphology. The ex situ SEM results indicated that rGO could prevent the cracking of the CoIn2S4 anode during the charge and discharge processes. Overall, the as-synthesized rGO-wrapped CoIn2S4 anode significantly improved the electrochemical performance. The following characteristics should be highlighted: not only can the highly electronicconductive rGO 3D network structure provide the CoIn2S4 anode material with a batchcovered matrix that buffers severe volume changes during charging and discharging, but its porous structure also provides additional channels for Li ions during charging and discharging.  Figure 10a,b depicts SEM images of pristine CoIn 2 S 4 and CoIn 2 S 4 /rGO electrodes before cycling. There was no discernible distinction between the two electrodes. After 30 cycles of discharge/charge testing, the surface morphology of the pristine CoIn 2 S 4 electrode, as depicted in Figure 10c, exhibited voids and fractures. Nevertheless, the CoIn 2 S 4 /rGO electrode (Figure 10d) maintained its compact structure and surface morphology. The ex situ SEM results indicated that rGO could prevent the cracking of the CoIn 2 S 4 anode during the charge and discharge processes. Overall, the as-synthesized rGO-wrapped CoIn 2 S 4 anode significantly improved the electrochemical performance. The following characteristics should be highlighted: not only can the highly electronic-conductive rGO 3D network structure provide the CoIn 2 S 4 anode material with a batch-covered matrix that buffers severe volume changes during charging and discharging, but its porous structure also provides additional channels for Li ions during charging and discharging.

Conclusions
In summary, a novel spinel-based CoIn2S4/rGO composite anode was demonstrated by a hydrothermal reaction. The CoIn2S4/rGO composite anode provided eight times the capacity performance of the pure CoIn2S4 electrode (84 mAh/g at 0.2 A/g), with a reversible capacity of 670 mAh/g at 0.2 A/g. Furthermore, the CoIn2S4/rGO composite electrode exhibited greater cyclic and rate-specific capabilities than the pure CoIn2S4 electrode. In addition, Nyquist impedance analysis revealed that the improved performance of the CoIn2S4/rGO anode could be attributed to the incorporation of rGO, which shortens the ion diffusion pathway and prevents aggregate formation. Furthermore, ex situ XRD results revealed the Li storage mechanism of CoIn2S4, which involves the formation of amor-

Conclusions
In summary, a novel spinel-based CoIn 2 S 4 /rGO composite anode was demonstrated by a hydrothermal reaction. The CoIn 2 S 4 /rGO composite anode provided eight times the capacity performance of the pure CoIn 2 S 4 electrode (84 mAh/g at 0.2 A/g), with a reversible capacity of 670 mAh/g at 0.2 A/g. Furthermore, the CoIn 2 S 4 /rGO composite electrode exhibited greater cyclic and rate-specific capabilities than the pure CoIn 2 S 4 electrode. In addition, Nyquist impedance analysis revealed that the improved performance of the CoIn 2 S 4 /rGO anode could be attributed to the incorporation of rGO, which shortens the ion diffusion pathway and prevents aggregate formation. Furthermore, ex situ XRD results revealed the Li storage mechanism of CoIn 2 S 4, which involves the formation of amorphous Co and In metals. The excellent electrochemical performance of CoIn 2 S 4 /rGO makes it a promising anode for LIBs.