Synthesis of Sb2S3 NRs@rGO Composite as High-Performance Anode Material for Sodium-Ion Batteries

Sodium ion batteries (SIBs) have drawn interest as a lithium ion battery (LIB) alternative owing to their low price and low deposits. To commercialize SIBs similar to how LIBs already have been, it is necessary to develop improved anode materials that have high stability and capacity to operate over many and long cycles. This paper reports the development of homogeneous Sb2S3 nanorods (Sb2S3 NRs) on reduced graphene oxide (Sb2S3 NRs @rGO) as anode materials for SIBs. Based on this work, Sb2S3 NRs show a discharge capacity of 564.42 mAh/g at 100 mA/g current density after 100 cycles. In developing a composite with reduced graphene oxide, Sb2S3 NRs@rGO present better cycling performance with a discharge capacity of 769.05 mAh/g at the same condition. This achievement justifies the importance of developing Sb2S3 NRs and Sb2S3 NRs@rGO for SIBs.


Introduction
Until now, secondary batteries are widely used as ecofriendly energy storage. Specifically, the increasing electric car market has accelerated the development of secondary battery materials that have high capacity and stability to endure long-term electrochemical cycling [1][2][3][4][5]. To achieve these goals, it is essential to improve the anode's storage capacity and thus, many possible materials have been tested [6]. Although lithium ion batteries (LIBs) meet the requirements for high energy storage devices with properties of high energy density and voltage, there are limitations in using lithium because of its high price and low earthly deposits [7,8]. As a substitute to LIBs, sodium ion batteries (SIBs) have been predicted as promising batteries because of their plentiful reserves and similar energy storage mechanism to LIBs [7]. However, the large diameter of the sodium atom leads to poor diffusion efficiency of Na + and expands the anode material's volume while intercalating [9]. Therefore, it is challenging to find a proper anode material that maintains good stability with the conditions described above [10]. Among these materials, antimony sulfide (Sb 2 S 3 ) is one of the strongest anode candidates that has high gravimetric energy density and theoretical capacity (946 mA/g) [11]. However, there are downsides to Sb 2 S 3 regarding its low conductivity and volume expansion during the sodiation/desodiation process when using Sb 2 S 3 as energy storage [12]. To solve these problems, homogeneous-width Sb 2 S 3 nanorods (Sb 2 S 3 NRs) and graphene oxide (GO) were used to make Sb 2 S 3 NRs@rGO anchored on reduced graphene oxide (rGO) [13][14][15][16]. Uniform sized Sb 2 S 3 NRs could compensate volume variation to some degrees while intercalation of Na+ than various sized nanorods [17][18][19]. Reduced graphene oxide (rGO) layers not only have enough interstitial spots to receive Na + but also have substantial conductivity making electron transfer easily.
Moreover, the rigid structure of rGO buffer the stress of volume expansion on Sb 2 S 3 NRs not to make dropwise of discharge capacity of the electrode over the long term. These traits of rGO invalidate the drawback of Sb 2 S 3 and enable the intercalation reversibly with a large amount of Na + raising capacity of the electrode [20].
Herein, this research reports the synthesis of homogeneous-width Sb 2 S 3 NRs and Sb 2 S 3 NRs@rGO. Through various electrochemical investigations, Sb 2 S 3 NRs@rGO showed improved discharge capacity of 769.05 mAhg −1 at a current density of 100 mA/g after 100 cycles. Even at a higher current density of 500 mAg −1 , excellent stability could be observed after 300 cycles, which was shown to be better than Sb 2 S 3 NRs@rGO.

Synthesis of Sb 2 S 3 NRs
First, 10 mL of oleylamine (OAm, from Sigma-Aldrich, St. Louis, MO, USA) was heated at 150 • C for an hour under vacuum conditions to remove impurities. After heating OAm, sulfur (S, 0.0412 g, from Sigma-Aldrich, St. Louis, MO, USA) and antimony chloride (SbCl 2 , 0.0661 g, 99%, from Sigma-Aldrich, St. Louis, MO, USA) were added to the welldried OAm. Then the solution was heated to 230 • C over a period of 40 min with stirring and washed with 15 mL of methanol and hexane by centrifugation four times after cooling to room temperature. After that, dark gray Sb 2 S 3 NRs powder was retrieved [21].

Synthesis of Graphene Oxide (GO)
GO was prepared by the well-known Hummers method using graphite powder [20]. First, graphite (Super P, 2 g, from Timcal Ltd., Bodio, Switzerland) was added to a solution of sulfuric acid (H 2 SO 4 , 10 mL, from Samchun, Pyeongtaek, Korea), potassium persulfate (K 2 S 2 O 8 , 2 g, from Sigma-Aldrich, St. Louis, MO, USA), and phosphorus pentoxide (P 2 O 5 , 2 g, from Sigma-Aldrich, St. Louis, MO, USA) at 85 • C. After stirring the mixture for 5 h, it was cooled to room temperature and 500 mL of deionized (DI) water was added for then stirred for another 12 h. The mixture was washed with DI water under vacuum filtration and dried under vacuum at room temperature. The as-prepared products were put into a cold solution of sulfuric acid (H 2 SO 4 , 100 mL, from Samchun, Pyeongtaek, Korea) while cooling in an ice bath. Potassium manganate (KMnO 4 , 10 g, from Sigma-Aldrich, St. Louis, MO, USA) was added gradually to the resultant slurry during 1 h keeping in an ice bath. After removing an ice bath, the mixture was stirred for 24 h at room temperature. Then, 30% hydrogen peroxide (H 2 O 2 , 20 mL, from Samchun, Pyeongtaek, Korea) and DI water (500 mL) were mixed into the solution. After filtration of mixed solution, the resulting precipitate was rinsed with 10 wt % hydrochloric acid (HCl, 1 L, from Samchun, Pyeongtaek, Korea) solution in water followed by washing with DI water (1 L) to remove the acidic components.

Synthesis of Sb 2 S 3 NRs@rGO
Prepared GO was dispersed in ethanol (EtOH, 15 mL, from Samchun, Pyeongtaek, Korea) and DI water (5 mL) using ultrasonication for 1 h. Sb 2 S 3 NRs (10 mg) were also dispersed in ethanol (EtOH, 5 mL) the same way and the two solutions were together, followed by ultrasonication for 1 h. After that, hydrazine (N 2 H 4 , 0.2 mL, from Kanto Chemical, Tokyo, Japan) was added to the solution and placed in a 250 • C oven for over 3 h and sealed with electrical tape to make reduced GO (rGO). After the supernatant liquid was removed, the retrieved product was washed with ethanol three times and dried, finally generating black/gray Sb 2 S 3 NRs@rGO powder.

Structural Refinement
A scanning electron microscope (SEM, JSM-7601F, JEOL, Tokyo, Japan) equipped with an energy dispersive spectrometer (EDS, Ultim Max, Oxford Instruments, Abingdon on Thames, UK) and transmission electron microscope (TEM, FEI RF30ST, Philips, Amsterdam, Netherlands) were used to observe the morphologies and structures of the sample. X-ray diffraction (XRD, D8 Advance A25, Bruker, Billerica, MA, USA) was used to characterize the composition of the samples at 40 kV and 40 mA with a 0.02 s/step. Raman spectra of the samples were obtained using a Raman instrument (Renishaw InVia, Renishaw, Wotton-under-Edge, UK) with a wavelength of 633 nm. X-ray photoelectron spectroscopy (XPS) was measured using a Thermo VG scientific Sigma Probe spectrometer (Sigma probe, Thermo VG scientific, East Grinstead, UK) with a monochromatic photon energy of 1486.6 eV (Al Kα).

Electrochemical Investigation
The half-coin cell (CR-2032) were assembled in a glove box filled with Ar to avoid oxygen and moisture (O 2 < 1 ppm, H 2 O < 1 ppm) contact with the Na metal used as the counter electrode. The electrode was made by mixing Sb 2 S 3 NRs (80 wt %) with polyvinylidene fluoride (PVDF) (10 wt %) binder and super P (10 wt %). A solution of 1 M NaPF 6 in DEGDME is used as the electrolyte in SIBs. For comparison, Sb 2 S 3 NRs were also made in the same way to assess the electrochemical performance. The test of galvanostatic charge-discharge was conducted in the voltage range of 0.01-3.0 V. Cyclic voltammetry (CV) measurements were carried out on a potentiostat (Zive SP1, Wonatech) at a voltage range of 0.01-3.0 V and a scanning rate of 0.05 mV/s. All electrochemical experiments above were performed at room temperature.

Morphology, Structure and Composition Analysis
The shape of the Sb 2 S 3 NRs was measured by SEM and TEM. As shown in Figure 1a on Thames, UK) and transmission electron microscope (TEM, FEI RF30ST, Philips, Amsterdam, Netherlands) were used to observe the morphologies and structures of the sample. X-ray diffraction (XRD, D8 Advance A25, Bruker, Billerica, MA, USA) was used to characterize the composition of the samples at 40 kV and 40 mA with a 0.02 s/step. Raman spectra of the samples were obtained using a Raman instrument (Renishaw InVia, Renishaw, Wotton-under-Edge, UK) with a wavelength of 633 nm. X-ray photoelectron spectroscopy (XPS) was measured using a Thermo VG scientific Sigma Probe spectrometer (Sigma probe, Thermo VG scientific, East Grinstead, UK) with a monochromatic photon energy of 1486.6 eV (Al Kα).

Electrochemical Investigation
The half-coin cell (CR-2032) were assembled in a glove box filled with Ar to avoid oxygen and moisture (O2 < 1 ppm, H2O < 1 ppm) contact with the Na metal used as the counter electrode. The electrode was made by mixing Sb2S3 NRs (80 wt %) with polyvinylidene fluoride (PVDF) (10 wt %) binder and super P (10 wt %). A solution of 1 M NaPF6 in DEGDME is used as the electrolyte in SIBs. For comparison, Sb2S3 NRs were also made in the same way to assess the electrochemical performance. The test of galvanostatic charge-discharge was conducted in the voltage range of 0.01-3.0 V. Cyclic voltammetry (CV) measurements were carried out on a potentiostat (Zive SP1, Wonatech) at a voltage range of 0.01-3.0 V and a scanning rate of 0.05 mV/s. All electrochemical experiments above were performed at room temperature.

Morphology, Structure and Composition Analysis
The shape of the Sb2S3 NRs was measured by SEM and TEM. As shown in Figure  1a,b, the Sb2S3 NRs synthesized by the hydrothermal method have smooth surfaces, showing good structural integrity. Figure 1c Figure 2c, demonstrating homogeneity of the synthesized materials. As seen in the EDS data of Figure 2d and Table S1, 59.51 at% and 40.49 at% represent S and Sb, respectively, which proves the successful synthesis of Sb 2 S 3 NRs (Table S1). Mapping data of previous SEM images are shown in Figure 2. The SEM image of Sb2S3 NRs Figure 2a corresponds to the images of Sb Figure 2b and S Figure 2c, demonstrating homogeneity of the synthesized materials. As seen in the EDS data of Figure 2d and Table S1, 59.51 at% and 40.49 at% represent S and Sb, respectively, which proves the successful synthesis of Sb2S3 NRs. (Table S1).  Figure 4a shows the X-ray diffraction (XRD) patterns of Sb2S3 NRs, rGO, and Sb2S3 NRs@rGO. The diffraction peaks of Sb2S3 NRs correspond to the diffraction pattern of Sb2S3 (JCPDS No. 42-1393) [22], and a comparison of each peak corresponds to either Sb2S3 NRs or rGO. The electronic surroundings of C and Sb in rGO, Sb2S3, and Sb2S3 NRs @rGO were compared by X-ray photoelectron spectroscopy (XPS) in Figure 4b,c, Figure S1, Tables S2 and S3. The C 1 s orbital peaks of rGO and Sb2S3 NRs @RGO were deconvoluted into the PC1 (C-C bonding) and the PC2 (C-O bonding) bands. The C 1s orbital peaks of rGO were observed at 284.5 eV, 285.7 eV, and Sb2S3 NRs @rGO were observed at 284.5 eV, 285.8 eV. Compared to rGO, the area of PC1 decreased from 86.7% to 75.1% while that of PC2 increased from 13.3% to 24.9%. The Sb 3d5/2 and Sb 3d3/2 orbital peaks of Sb2S3 NRs were observed 528.9 eV (Sb 3d3/2) and at 538.2 eV (Sb 3d5/2) respectively. Sb2S3 NRs@rGO was deconvoluted into five bands, a PS1 at 530.2 eV and a PS2 at 531.0 eV and a PS3 at 539.5eV and a PS4 at 540.3 eV and a PO1 at 532.7 eV. The PO1 band was mostly detected from rGO. The bands of PS1 and PS3 correspond to Sb 3d5/2 and PS2 and PS4 were observed by the interaction between Sb2S3 NRs and rGO. According to the PC2 of Sb2S3 NRs@rGO in Figure 4b and PS2 and PS4 of Sb2S3 NRs@rGO in Figure 4c, The PS2 and PS4 bands were shifted to higher binding energy because the C atoms in rGO have higher electronegative than Sb atoms in Sb2S3 NRs. The result of XPS was showed that Sb2S3 NRs are incorporated on rGO [23][24][25][26]. These results prove that Sb2S3 NRs@rGO was successfully synthesized. Raman spectra of GO and Sb2S3 NRs@rGO are presented in Figure 4d. The G and D bands of Sb2S3 NRs are The modified Hummers method to synthesize the Sb 2 S 3 NRs@rGO composite is illustrated in Figure 3. Prepared Sb 2 S 3 NRs Figure 3a,b are anchored to rGO Figure 3c,d, where the Sb 2 S 3 NRs particles are covered with rGO layers Figure 3e,f. Figure 4a shows the X-ray diffraction (XRD) patterns of Sb 2 S 3 NRs, rGO, and Sb 2 S 3 NRs@rGO. The diffraction peaks of Sb 2 S 3 NRs correspond to the diffraction pattern of Sb 2 S 3 (JCPDS No. 42-1393) [22], and a comparison of each peak corresponds to either Sb 2 S 3 NRs or rGO. The electronic surroundings of C and Sb in rGO, Sb 2 S 3 , and Sb 2 S 3 NRs @rGO were compared by X-ray photoelectron spectroscopy (XPS) in Figure 4b,c, Figure S1, Tables S2 and S3. The C 1 s orbital peaks of rGO and Sb 2 S 3 NRs @RGO were deconvoluted into the PC1 (C-C bonding) and the PC2 (C-O bonding) bands. The C 1s orbital peaks of rGO were observed at 284.5 eV, 285.7 eV, and Sb 2 S 3 NRs @rGO were observed at 284.5 eV, 285.8 eV. Compared to rGO, the area of PC1 decreased from 86.7% to 75.1% while that of PC2 increased from 13.3% to 24.9%. The Sb 3d 5/2 and Sb 3d 3/2 orbital peaks of Sb 2 S 3 NRs were observed 528.9 eV (Sb 3d 3/2 ) and at 538.2 eV (Sb 3d 5/2 ) respectively. Sb 2 S 3 NRs@rGO was deconvoluted into five bands, a PS1 at 530.2 eV and a PS2 at 531.0 eV and a PS3 at 539.5eV and a PS4 at 540.3 eV and a PO1 at 532.7 eV. The PO1 band was mostly detected from rGO. The bands of PS1 and PS3 correspond to Sb 3d 5/2 and PS2 and PS4 were observed by the interaction between Sb 2 S 3 NRs and rGO. According to the PC2 of Sb 2 S 3 NRs@rGO in Figure 4b and PS2 and PS4 of Sb 2 S 3 NRs@rGO in Figure 4c, The PS2 and PS4 bands were shifted to higher binding energy because the C atoms in rGO have higher electronegative than Sb atoms in Sb 2 S 3 NRs. The result of XPS was showed that Sb 2 S 3 NRs are incorporated on rGO [23][24][25][26]. These results prove that Sb 2 S 3 NRs@rGO was successfully synthesized. Raman spectra of GO and Sb 2 S 3 NRs@rGO are presented in Figure 4d. The G and D bands of Sb 2 S 3 NRs are clearly detected at 1586 cm −1 and 1330 cm −1 , respectively, and a slight shift of the peaks of G and D band can be seen at 1594 cm −1 and 1334 cm −1 , respectively, indicating the reduction of GO [27][28][29].
Materials 2021, 14, x FOR PEER REVIEW 5 of 9 clearly detected at 1586 cm −1 and 1330 cm −1 , respectively, and a slight shift of the peaks of G and D band can be seen at 1594 cm −1 and 1334 cm −1 , respectively, indicating the reduction of GO [27][28][29].

Sodium Storage Behavior
The electrochemical performances of Sb2S3 NRs and Sb2S3 NRs@rGO as anode materials in SIBs were analyzed. Figure 5a shows the CV curve of Sb2S3 NRs over the first four cycles at a scanning rate of 0.05 mV/s between 0.01 and 3.0 V (versus Na/Na + ). Compared clearly detected at 1586 cm −1 and 1330 cm −1 , respectively, and a slight shift of the peaks of G and D band can be seen at 1594 cm −1 and 1334 cm −1 , respectively, indicating the reduction of GO [27][28][29].

Sodium Storage Behavior
The electrochemical performances of Sb2S3 NRs and Sb2S3 NRs@rGO as anode materials in SIBs were analyzed. Figure 5a shows the CV curve of Sb2S3 NRs over the first four cycles at a scanning rate of 0.05 mV/s between 0.01 and 3.0 V (versus Na/Na + ). Compared

Sodium Storage Behavior
The electrochemical performances of Sb 2 S 3 NRs and Sb 2 S 3 NRs@rGO as anode materials in SIBs were analyzed. Figure 5a shows the CV curve of Sb 2 S 3 NRs over the first four cycles at a scanning rate of 0.05 mV/s between 0.01 and 3.0 V (versus Na/Na + ). Compared with Figure 5a,b, the cathodic and anodic peaks of Sb 2 S 3 NRs@rGO Figure 5b show remark-able intensity. As seen in the CV of Sb 2 S 3 NRs Figure 5a, notable cathodic peaks were not observed at 0.3 V and 1.2 V but found in Sb 2 S 3 NRs@rGO Figure 5b, which is attributed to the conversion reaction with sulfur (Sb 2 S 3 + 6Na + + 6e − → 2Sb + 3Na 2 S) [29,30]. The anodic peaks centered at 1.1 V, 1.7 V, 2.1 V are related to the alloying reaction (2Na 3 Sb → 2Sb + 6Na + + 6e − ) and formation of Sb 2 S 3 (2Sb + 3Na 2 S → Sb 2 S 3 + 6Na + + 6e − ) in Figure 5a [29,30].
Materials 2021, 14, x FOR PEER REVIEW 6 of 9 with Figure 5a,b, the cathodic and anodic peaks of Sb2S3 NRs@rGO Figure 5b show remarkable intensity. As seen in the CV of Sb2S3 NRs Figure 5a, notable cathodic peaks were not observed at 0.3 V and 1.2 V but found in Sb2S3 NRs@rGO Figure 5b, which is attributed to the conversion reaction with sulfur (Sb2S3 + 6Na + + 6e − → 2Sb + 3Na2S) [29,30]. The anodic peaks centered at 1.1 V, 1.7 V, 2.1 V are related to the alloying reaction (2Na3Sb → 2Sb + 6Na + + 6e − ) and formation of Sb2S3 (2Sb + 3Na2S → Sb2S3 + 6Na + + 6e − ) in Figure 5a [29,30]. After the composite process with rGO, there is still the same change in the cathodic process, and more remarkable peaks around 0.7 V, 1.8 V, and 2.1 V were observed in Figure 5b [29,30]. The cycling performance of Sb2S3 NRs and Sb2S3 NRs@rGO were tested at 100 mAg −1 Figure 5c and 500 mAg −1 Figure 5d, respectively. Sb2S3 NRs deliver a discharge capacity of 564.42 mAh/g at 100 mAg −1 current density after 100 cycles. However, Sb2S3 NRs@rGO presents an improved cyclic performance of 769.05 mAhg −1 at the same conditions. As shown in Figure 5d, likewise at a higher current density of 500 mAg −1 , the capacity can still attain 614.5 mAhg −1 after 300 cycles. From Figure 5d, the discharge capacity of Sb2S3 NRs@rGO decreases from the outset and increases gradually to 300 cycles, reaching the highest discharge capacity of 614.5 mAhg −1 at current of 500mAg −1 . This value keeps maintaining after 300 cycles. The decrease of capacity could be explained by the formation of irreversible solid electrolyte interphase (SEI) layers from the decomposition of the electrolyte [31]. Due to its electronically insulating property, irreversible capacity fading could After the composite process with rGO, there is still the same change in the cathodic process, and more remarkable peaks around 0.7 V, 1.8 V, and 2.1 V were observed in Figure 5b [29,30]. The cycling performance of Sb 2 S 3 NRs and Sb 2 S 3 NRs@rGO were tested at 100 mAg −1 Figure 5c and 500 mAg −1 Figure 5d, respectively. Sb 2 S 3 NRs deliver a discharge capacity of 564.42 mAh/g at 100 mAg −1 current density after 100 cycles. However, Sb 2 S 3 NRs@rGO presents an improved cyclic performance of 769.05 mAhg −1 at the same conditions. As shown in Figure 5d, likewise at a higher current density of 500 mAg −1 , the capacity can still attain 614.5 mAhg −1 after 300 cycles. From Figure 5d, the discharge capacity of Sb 2 S 3 NRs@rGO decreases from the outset and increases gradually to 300 cycles, reaching the highest discharge capacity of 614.5 mAhg −1 at current of 500mAg −1 . This value keeps maintaining after 300 cycles. The decrease of capacity could be explained by the formation of irreversible solid electrolyte interphase (SEI) layers from the decomposition of the electrolyte [31]. Due to its electronically insulating property, irreversible capacity fading could occur. The rise of capacity could be explained by several reasons. First of all, volume expansion of Sb 2 S 3 induces the rise of the specific capacity. As shown in Figure S2a,d, SEM images of Sb 2 S 3 NRs and Sb 2 S 3 NRs@rGO were presented having homogeneous-width rod shapes. However, after several cycling tests, Sb 2 S 3 NRs began to be expanded and defects and broken shapes were observed on its surface Figure S2b,c. As this expansion proceeds making some defects on the surface of Sb 2 S 3 NRs, occluded reaction sites of Sb 2 S 3 NRs also react with Na + . These mounting number of reaction sites induce the increase of the capacity [31]. Secondly, the activation of materials could also attribute to this phenomenon [32][33][34][35][36]. Besides, the SEI layer could be constructed to be more stable during the activation process above [37]. These factors contribute to the gradual rise of the specific capacity during repeated charge and discharge which is a common activation phenomenon for chalcogenide and oxide anodes [32][33][34][35][36]. Even though the rise of discharge capacity looks good, this structure instability causes the variableness of electric capacity for long cycling performances. As can be seen in Figure S2d,e, Sb 2 S 3 NRs@rGO were also expanded, though the degree of swelling was quite smaller than that of Sb 2 S 3 NRs and could keep its rod-like shapes after several cycle performances, suggesting that reduced graphene oxide (rGO) sustains over the volume expansion of Sb 2 S 3 NRs during sodiation and desodiation.
To examine the electrochemical kinetics of the anode materials, the electrochemical impedance spectra (EIS) of Sb 2 S 3 NRs and Sb 2 S 3 NRs@rGO were tested, as shown in Figure 6a [38,39]. The ohmic resistance of Sb 2 S 3 NRs@rGO is not more than that of Sb 2 S 3 NRs, indicating a conductivity improvement. occur. The rise of capacity could be explained by several reasons. First of all, volume expansion of Sb2S3 induces the rise of the specific capacity. As shown in Figure S2a,d, SEM images of Sb2S3 NRs and Sb2S3 NRs@rGO were presented having homogeneous-width rod shapes. However, after several cycling tests, Sb2S3 NRs began to be expanded and defects and broken shapes were observed on its surface. Figure S2b, c As this expansion proceeds making some defects on the surface of Sb2S3 NRs, occluded reaction sites of Sb2S3 NRs also react with Na + . These mounting number of reaction sites induce the increase of the capacity [31]. Secondly, the activation of materials could also attribute to this phenomenon [32][33][34][35][36]. Besides, the SEI layer could be constructed to be more stable during the activation process above [37]. These factors contribute to the gradual rise of the specific capacity during repeated charge and discharge which is a common activation phenomenon for chalcogenide and oxide anodes [32][33][34][35][36].Even though the rise of discharge capacity looks good, this structure instability causes the variableness of electric capacity for long cycling performances. As can be seen in Figure S2d,e, Sb2S3 NRs@rGO were also expanded, though the degree of swelling was quite smaller than that of Sb2S3 NRs and could keep its rod-like shapes after several cycle performances, suggesting that reduced graphene oxide (rGO) sustains over the volume expansion of Sb2S3 NRs during sodiation and desodiation.
To examine the electrochemical kinetics of the anode materials, the electrochemical impedance spectra (EIS) of Sb2S3 NRs and Sb2S3 NRs@rGO were tested, as shown in Figure  6a [38,39]. The ohmic resistance of Sb2S3 NRs@rGO is not more than that of Sb2S3 NRs, indicating a conductivity improvement.  Figure 6b presents the galvanostatic charge/discharge profiles of Sb2S3 NRs@rGO at a current density of 100 mA/g, revealing the characteristic voltage profiles of the Sb2S3 NRs@rGO. As discussed above in Figure 5b, the conversion reaction with sulfur occurs at 0.3 V and 1.2 V, as presented by the two plateaus at similar voltages. Figure 6b alloying and formation of Sb2S3 occurs at 0.8 V, as shown by one plateau in Figure 6b. The initial discharge capacity is 580.4 mAh/g, while the second discharge delivers a capacity of 500.1 mAh/g, representing 86% coulombic efficiency. These different discharge capacities could be due to the solid electrolyte interface, which is irreversible.

Conclusions
In summary, high gravimetric energy density and theoretical capacity (946 mA/g) of Sb2S3 has been introduced as high-performance anode material for sodium ion batteries. To overcome the volume expansion of the Sb2S3, 0.9 nm Sb2S3 NRs were synthesized and then made into a composite with reduced graphene oxide. Through this work, Sb2S3 NRs@rGO showed improved discharge capacity of 769.05 mAh/g at a current density of 100 mA/g after 100 cycles and excellent stability after 300 cycles, which was shown to be  Figure 6b presents the galvanostatic charge/discharge profiles of Sb 2 S 3 NRs@rGO at a current density of 100 mA/g, revealing the characteristic voltage profiles of the Sb 2 S 3 NRs@rGO. As discussed above in Figure 5b, the conversion reaction with sulfur occurs at 0.3 V and 1.2 V, as presented by the two plateaus at similar voltages. Figure 6b alloying and formation of Sb 2 S 3 occurs at 0.8 V, as shown by one plateau in Figure 6b. The initial discharge capacity is 580.4 mAh/g, while the second discharge delivers a capacity of 500.1 mAh/g, representing 86% coulombic efficiency. These different discharge capacities could be due to the solid electrolyte interface, which is irreversible.

Conclusions
In summary, high gravimetric energy density and theoretical capacity (946 mA/g) of Sb 2 S 3 has been introduced as high-performance anode material for sodium ion batteries. To overcome the volume expansion of the Sb 2 S 3 , 0.9 nm Sb 2 S 3 NRs were synthesized and then made into a composite with reduced graphene oxide. Through this work, Sb 2 S 3 NRs@rGO showed improved discharge capacity of 769.05 mAh/g at a current density of 100 mA/g after 100 cycles and excellent stability after 300 cycles, which was shown to be better than Sb 2 S 3 NRs. This paper has developed a novel synthetic process for Sb 2 S 3 NRs and Sb 2 S 3 NRs@rGO and presents an avenue in determining more suitable anode materials for SIBs.

Supplementary Materials:
The following are available online at https://www.mdpi.com/article/10 .3390/ma14247521/s1, Figure S1: XPS survey spectrum of Sb 2 S 3 NRs and Sb 2 S 3 NRs@rGO, Figure S2: SEM images of Sb 2 S 3 NRs before cyclic test (a) and after several cyclic test (b), Table S1: EDS elemental  qualification results, Table S2: Fine-scanned data of C 1s in rGO and Sb 2 S 3 NRs@rGO, Table S3: Fine-scanned data of Sb 3d and O 1s in Sb 2 S 3 NRs and Sb 2 S 3 NRs@rGO.