Article | Open

Bulk antimony sulfide with excellent cycle stability as next-generation anode for lithium-ion batteries

  • Scientific Reports 4, Article number: 4562 (2014)
  • doi:10.1038/srep04562
  • Download Citation
Published online:


Nanomaterials as anode for lithium-ion batteries (LIB) have gained widespread interest in the research community. However, scaling up and processibility are bottlenecks to further commercialization of these materials. Here, we report that bulk antimony sulfide with a size of 10–20 μm exhibits a high capacity and stable cycling of 800 mAh g−1. Mechanical and chemical stabilities of the electrodes are ensured by an optimal electrode-electrolyte system design, with a polyimide-based binder together with fluoroethylene carbonate in the electrolyte. The polyimide binder accommodates the volume expansion during alloying process and fluoroethylene carbonate suppresses the increase in charge transfer resistance of the electrodes. We observed that particle size is not a major factor affecting the charge-discharge capacities, rate capability and stability of the material. Despite the large particle size, bulk antimony sulfide shows excellent rate performance with a capacity of 580 mAh g−1 at a rate of 2000 mA g−1.


Lithium-ion batteries (LIB) have been in the market for more than 20 years. They are now ubiquitous and can be found in numerous applications ranging from cell phones, laptop, power tools and electric vehicles. Even though many engineering advances have been made to a cell to enhance its energy density and stability, the basic materials in commercial cell remain almost the same as 20 years ago. In particular, graphite is still the primary material used as anode in LIB. Theoretical capacity of graphite is 370 mAhg−1, and practical capacity close to that value is routinely obtained in commercial cells. To increase the energy density further, new materials have to be developed. Elements such as Sn and Si1,2,3, metal oxide materials such as SnO2, SiO, Fe2O34, and metal sulfides such as CuxS, NixS, SnS2, MoS2, Sb2S3, etc.5,6,7,8,9,10,11,12 have been investigated as potential candidates for new generation anode materials. These materials undergo conversions reaction and/or alloying with Li, resulting in a capacity of >500 mAhg−14. However, poor cycling stability has prevented their immediate commercialization. Much work has been conducted to improve cycle stability by nano-sizing the materials. Yet, large-scale synthesis and processibility of nano-materials remain a challenge. The purpose of this study is to identify the major factors affecting the stability of the new anode materials and to find out if it is possible to stabilize their bulk counterparts by different electrode formulations. This will bring greater technological impact to battery applications.

In this article, our focus is on alloy-based metal sulfide (MxS) as anode materials because they can undergo both conversion reaction between Li and MxS and alloying reaction of the remaining metal with Li, resulting in higher charge and discharge capacities. Capacity degradation observed in these materials is typically attributed to large volume expansion/contraction during charge and discharge, and also dissolution of polysulfide from the active material. However, very few studies attempted to isolate the mechanical and chemical influences on the stability of the electrode. In particular, most of the research work on metal sulfides focused only on the synthesis and application of nano-sizes, nanomorphologies and graphene-based composites to suppress the volume expansion13,14,15,16. Here we want to identify and overcome the challenges when bulk materials are used. In this study, we have shown that particle size is in fact not the most crucial factor on the stability of the active materials. We achieved excellent cycle performance and rate capability using bulk materials by ensuring the mechanical and chemical stabilities of the electrodes. To understand the mechanical and chemical stabilities of the electrode, the effects of binder and electrolyte additive on the cycle performance of the metal sulfide electrodes were analysed systematically. Antimony sulfide (Sb2S3) is chosen as the model system for this work because it is commercially available and can also be synthesized easily. Sb2S3 also has a working potential of around 1 V vs. Li/Li+, far away from the potential of Li dendrite formation, making it a safer anode material for fast charging applications. Different factors affecting the electrochemical performance of the Sb2S3 electrode are identified and the issues are resolved by using a proper electrode-electrolyte system. These results can be equally applicable to other metal sulfides materials such as SnS and In2S3, etc.

Theoretically, Sb2S3 can undergo both conversion reaction and alloy formation, as described by Equation 1 and 2.

Theoretical capacity for the conversion reaction is 473 mAh g−1 (3 electrons transfer per mole of Sb) where as that for full reaction is 946 mAh g−1 (6 electrons transfer). Electrodes with polyvinylidene fluoride (PVdF), carboxymethyl cellulose sodium salt (CMC) or polyimide binder were compared to understand the mechanical influence on electrode stability. Systematic analyses were carried out to isolate the contribution from volume change, surface reaction and polysulfide dissolution in each of these cases. At the end of the paper, the effect of particle size on capacity and rate performance was assessed using the optimal cell configuration.


Physical characterization

Before electrochemical evaluation, the crystal structure of the materials was investigated by X-ray diffraction (XRD). Both bulk crystalline Sb2S3 and the Sb2S3 wire show an orthorhombic structure with a Pbnm space group (see Figure 1a), as reported in literature9,14,17. All the peaks match well with that of Sb2S3 (ICDD 00-042-1393).

Figure 1: Structure and morphology of Sb2S3 samples.
Figure 1

(a) XRD of bulk Sb2S3 and synthesized Sb2S3 wires; (b) SEM images of bulk Sb2S3 (scale bar: 10 μm) and (c) Sb2S3 wires (scale bar: 2 μm).

The morphologies of the materials were characterized by scanning electron microscopy (SEM). SEM images of the materials are shown in Figure 1. Bulk crystalline Sb2S3 from Sigma Adrich had a particle size ranging from 10–20 μm (Figure 1b). In contrast, the Sb2S3 wire obtained from hydrothermal synthesis showed a width of about 1 μm and a length of about 10 μm (Figure 1c).

Mechanical and chemical contributions to cycle stability

Initial electrochemical evaluation of bulk Sb2S3 was carried out with 20wt% PVdF as the binder in EC/DEC electrolyte. The constant current charge-discharge profiles are shown in Figure 2a. During first discharge, 2 plateaus were observed. The plateau at around 1.4 V is attributed to the conversion reaction of Sb2S3 to Li2S and Sb9. The lower plateau at around 0.8 V was due to alloying of Sb with Li18. In terms of capacity, 473 mAh g−1 and 938 mAh g−1 can be obtained from the material during first discharge to 1 V and 0 V, respectively. This corresponds to a transfer of about 3 electrons and 6 electrons, which is consistent with the theoretical reactions as stated in Equation 1 and 2. The formation of metallic Sb was supported by ex-situ XRD study of Sb2S3 when discharged to 1.0 V (See Supplementary Figure S1 for details). With further lithiation, the Sb peaks decreased in intensity, suggesting there was reaction between Sb and Li at lower voltage. Though, no crystalline phases could be seen at the end of discharge (to 0 V), either because Li2S and Li3Sb formed were amorphous, or too small to be detected by XRD. The result suggested that bulk Sb2S3 can undergo full conversion and alloying during first discharge. However, limitation in capacity was observed during charging: only a charge capacity of 436 mAh g−1 can be obtained when charged to 2.5 V vs. Li/Li+, corresponding to a cycle efficiency of 46.4%. Less than half of the Li can be extracted from the Sb2S3 electrode with PVdF during the charging step. We will show in a later section that the charge capacity is highly affected by the type of binder.

Figure 2: Electrochemical performance of bulk Sb2S3 with PVdF binder.
Figure 2

(a) Charge-discharge profiles of bulk Sb2S3 with PVdF binder. (b) Cycle performance of bulk Sb2S3 with PVdF binder at 250 mAg−1.

The cycle performance of the Sb2S3 electrode with 20% PVdF is shown in Figure 2b. When the electrode was cycled between 0 and 2.5 V vs. Li/Li+ with EC/DEC electrolyte, significant capacity fading was observed, with a loss of more than 50% after 50 cycles at 250 mA g−1. Three typical reasons were often cited for the capacity fading of metal sulfide materials: volume change, surface degradation and polysulfide dissolution, as shown in a schematic in Figure 3. Here, we analyzed the contribution from each factor separately by isolating their effect. This can be achieved by carefully varying the test conditions and materials. We noticed in Equation 1 and 2 that volume change from alloying mechanism only occurs below 1 V. So it is possible to avoid this contribution by limiting the test voltage range above 1 V vs. Li/Li+ (between 1 and 2.5 V in our experiment). The electrode showed a stable capacity even with PVdF binder in EC/DEC electrolyte when cycled in a higher potential range (see Figure 2b).

Figure 3: Schematic diagram of the typical causes of capacity fading in metal sulfide electrodes.
Figure 3

Since only conversion reaction with the formation of LixS occurs between 1 and 2.5 V, the result has two implications: first, polysulfide dissolution is not a major contribution to cycle degradation, at least not within the first 50 cycles because the capacity was stable despite LixS formation; second, the difference between the cycle performance of 0–2.5 V (capacity fading) and 1–2.5 V (stable capacity) is due to the utilization of the electrode below 1 V, from the reaction between Sb and Li. Therefore, the alloying reaction between Sb and Li causes much of the capacity fading in the electrode.

There are two main contributions to the capacity fading from the alloying reaction: surface reaction between the electrolyte and the active material (chemical effect) and volume expansion/contract of the particles during charge-discharge (mechanical effect). We investigated the contribution from the surface effect of the same Sb2S3 electrodes with PVdF binder by using different electrolytes. Several research groups had reported that the solid electrolyte interphase (SEI) of alloy materials such as Si and Sb anode can be strengthened by the use of fluorinated ethylene carbonate (FEC) as an additive in the electrolyte19,20,21,22,23. We expect FEC will have similar effect for the alloying process in Sb2S3. Sb2S3 electrodes with PVdF were tested with 1 M LiPF6 in FEC/DEC = 1:1 between 0 and 2.5 V, and the result is shown in Figure 2b. Capacity retention after 50 cycles was improved from 42.9% with EC/DEC to 66.7% with FEC/DEC. Since the only difference in the battery is the electrolyte, the 23.8% increase in capacity retention with FEC/DEC indicates that surface reaction is also a major factor in the cycle stability of the anode material. Further investigation of the effect of FEC on impedance of the electrode will be discussed in a later section. Even with FEC/DEC as the electrolyte, there remained a 30% drop in capacity after 50 cycles using PVdF as the binder, which suggests that there is still a large contribution from the volume change on the cycle stability of the electrode.

Effect of binder

Since our initial results indicated that volume change has a big effect on electrode stability, it is reasonable to see if it is possible to keep the structural integrity of the electrode by changing the binder. A flexible binder that can withstand large strain would be preferred. Instead of PVdF, which is a common electrode binder, electrodes with bulk Sb2S3 were made with CMC and polyimide binder (DB100) – CMC and polyimide binder have been demonstrated to show improved cycle performance in alloy anodes such as Sn, Si and SiO24,25,26,27,28,29,30. All the electrodes were made with 20wt% acetylene black (AB) and 20wt% binder and tested under the same conditions as described before. Because of the large amount of acetylene black and binder, reference electrodes were also made with Cu powder (Alfa Aesar 350 mesh 8–11 μm) in the same ratio of Cu:AB:binder = 6:2:2 to determine the contribution from the carbon and binder. Since Cu does not alloy with Li, the capacities from these reference electrodes reflect the Li accommodation in the carbon black and the binder. The specific capacities reported in this study for these reference electrodes were calculated with respect to the mass of Cu. Even though strictly speaking Li were not inserted into Cu but the carbon black and binder in the electrode, this allows direct comparison with the capacity of Sb2S3 electrodes because the electrode composition of 6:2:2 was the same.

Cyclic voltammetry of electrodes with PVdF, CMC and DB100 were tested and the first cycle and second cycle voltammograms are shown in Figure 4a and 4b. All three sets of electrodes with different binders show reduction reactions around 1.18 V and 0.76 V and oxidation reaction at 1.10 V during first cycle, which are typical of the conversion and alloying processes in Equation 1 and 2. There was not much difference between the peak intensities of electrodes with PVdF and CMC, indicating similar capacities from the electrode with these two binders. This was confirmed by constant-current tests at 100 mA g−1 where a charge capacity of about 450 mAh g−1 was obtained after first cycle for both electrodes (see Supplemenary Table S1). Electrodes with DB100, on the other hand, show much higher reaction currents, especially below 1 V in the CV profiles (Figure 4a and 4b). Some of the contributions in current originates from the polyimide binder, which was evident from the reference electrode with Cu:AB:DB100. Still, a large difference in intensity was observed during the second cycle with DB100 binder, indicating an enhanced electrochemical performance of Sb2S3 with the polyimide binder.

Figure 4: Cyclic voltammograms of bulk Sb2S3 and Cu with different binders at a scan rate of 0.1 mV s−1.
Figure 4

(a) 1st cycle; (b) 2nd cycle.

Constant-current charge-discharge tests were then carried out and the profiles are shown in Figure 5. The contributions from carbon black and binders can be first estimated from the Cu reference electrodes. First discharge capacities of Cu:AB:binder were 183.9, 129.9 and 488.0 mAh g−1 for PVdF, CMC and DB100, respectively. Conversely, first charge capacities were only 78.3, 56.2 and 280.6 mAh g−1 for the electrodes with the three binders. Only a small amount of capacity was obtained from reference electrodes with PVdF and CMC. DB100, on the other hand, shows some degree of Li uptake and removal.

Figure 5: Charge-discharge profiles of bulk Sb2S3 and Cu with different binders at a current rate of 100 mA g−1.
Figure 5

(a) 1st cycle; (b) 2nd cycle.

After systematic analyzing the effect from AB and binder, the results from the Sb2S3 electrodes become clearer. Sb2S3 electrodes with PVdF and CMC showed a first discharge capacity of around 930 mAh g−1, out of which AB and binder accounts for about 130–180 mAh g−1. (See Supplementary Table S1) So the actual amount of capacity uptake by Sb2S3 material was about 750–800 mAh g−1. On the other hand, Sb2S3 electrode with DB100 showed a first discharge capacity of 1358.5 mAh g−1, which was above the theoretical capacity of Sb2S3. This was in fact reasonable because 488.0 mAh g−1 of the electrode capacity originates from AB and DB100. Figure 5a also shows that the main difference between the discharge curves of Sb2S3 electrode with CMC and DB100 was the increase in capacity below 1 V, which is due to the Li accommodation in the polyimide binder. During charging, a much higher capacity could be obtained from Sb2S3 electrode with DB100 than those with PVdF and CMC. The increase in capacity by changing binder in the Sb2S3 electrode from CMC to DB100 was about 430 mAh g−1, which was higher than the amount of Li that can be removed from the polyimide binder. Thus, polyimide binder also enhanced the charge-discharge performance of the Sb2S3 material in the electrode. This was evident in the second charge profile in Figure 5b – increased capacity from the Sb2S3 electrode with DB100 was observed at both the 1 V plateau (alloying reaction) as well as around 2 V (conversion reaction). The higher utilization of Sb2S3 with DB100 binder was probably due to better binding of the particles within the electrode.

The three types of electrodes were then subjected to cycling at 250 mA g−1 between 0 and 2.5 V with EC/DEC electrolyte. Lines with solid markers in Figure 6 correspond to the cells tested in EC/DEC. Electrodes with PVdF or CMC start with similar initial capacity of about 400 mAh g−1, but the capacity retention after 50 cycles was higher with CMC binder, which clearly indicate the importance of binder in the cycle performance. On the other hand, electrode with DB100 gave an initial capacity of 750 mAh g−1, but capacity faded after cycling. By changing the electrolyte to FEC/DEC, cycle stability of all the electrodes were improved (lines with open markers in Figure 6). In particularly, the capacity retention after 50 cycles for the electrode with polyimide binder improved from 66.2% to 92.5% with FEC/DEC. This indicates that the use of FEC can effectively suppress capacity fading due to surface effect from the electrode with DB100. Our results showed that by changing the binder and electrolyte composition, high capacity with good stability can be obtained. Further work is in progress to clarify the origin of the remaining capacity loss, which can be due to the capacity loss from Li reaction with the polyimide binder and/or a small amount of polysulfide dissolution from the electrode during cycling.

Figure 6: Cycle performance of bulk Sb2S3 with different binders at 250 mAg−1.
Figure 6

Solid – cells with EC/DEC; open – cells with FEC/DEC.

The charge-discharge profiles of bulk Sb2S3 with DB100 binder tested in EC/DEC and FEC/DEC are shown in Supplementary Figure S2. The decrease in capacity for both the conversion and alloying reactions (both 1.4 V and 0.8 V plateaus) can be suppressed by the use of FEC. In order to further understand the role of FEC electrolyte, impedance measurements at different cycle number were carried out with 10 mV amplitude between 500 kHz and 5 mHz. The cells were first discharged partially to 1.0 V and held at 1.0 V for 2 hours before impedance measurement. Figure 7 shows the Nyquist plots of the cell with EC/DEC and FEC/DEC after 5th and 50th cycles. After 5 cycles, both electrodes with EC/DEC and FEC/DEC showed similar charge-transfer resistance (solid lines in Figure 7). After 50 cycles, charge-transfer resistance for the cell tested with FEC/DEC remains the same. On the other hand, the cell tested with EC/DEC showed large increase in impedance. Our result indicated that the use of FEC suppresses the increase in surface resistance of the electrode, leading to better cycle stability.

Figure 7: Nyquist plots of Sb2S3 half cells with DB100 binder.
Figure 7

Electrode tested in EC/DEC (thick red line) and FEC/DEC (thin black line) electrolyte after 5th and 50th cycles.

Effect of particle size on electrochemical performance

In the previous section, we observed that bulk Sb2S3 exhibited high capacity and good cycle stability with a suitable binder and electrolyte composition. Still one question remains: does reduction of particle size give additional benefit? To answer this, Sb2S3 wires with a width of about 1 μm were synthesized through a co-precipitation and hydrothermal process for comparison. Figure 1c shows the morphology of the wires. The Sb2S3 wires were made into electrodes with DB100 as the binder and tested with FEC/DEC electrolyte, the same as the one with bulk Sb2S3.

Figure 8a shows the 2nd cycle voltammograms of the Sb2S3 wires and bulk Sb2S3. Both electrodes showed similar charge-discharge peaks for alloying and conversion reactions of Sb2S3. Electrode with Sb2S3 wire showed additional peaks at 1.9 and 2.35 V during charging and 1.7 V during discharging. This may be due to trace amount of elemental S in the material. Other than the additional peaks in electrode with Sb2S3 wire, both electrodes showed similar peak currents, indicating similar charge-discharge capacities. Constant-current tests of the electrodes were carried out and the cycle performance is shown in Figure 8b. Sb2S3 wire showed slightly higher capacity than bulk Sb2S3 at a rate of 250 mA g−1, but the difference is not significant.

Figure 8: Comparison of Sb2S3 wire and bulk Sb2S3 with DB100 binder and FEC/DEC electrolyte.
Figure 8

(a) 2nd cycle voltammograms, (b) cycle and rate performance, (c) charge-discharge profiles at different rates.

Both electrodes gave good cycle performance because the polyimide binder provides mechanical stability to the electrodes and FEC suppresses surface reaction. The electrodes were also tested up to 2000 mA g−1 (see insert in Figure 8b). Surprisingly, the same rate performances were observed for both Sb2S3 wire and bulk Sb2S3. This indicates that no additional benefits were observed by reducing the particle size, and the reduction of particle size is not necessary for obtaining high rate and high capacity in these materials.

The charge-discharge profiles of bulk Sb2S3 tested at different current rates are shown in Figure 8c. At a current rate of 2000 mA g−1, a charge capacity of 580 mAh g−1 could be obtained. This corresponds to a charge or discharge time of 17 minutes. This is significant because it is the highest rate capability ever reported for bulk 10–20 μm materials. The ability to use bulk materials to get high capacity and high rate makes them one step closer to commercialization.


Capacity and cycle performance of electrode materials are highly dependent on electrode configuration and electrolyte composition. Systematic investigations were carried out to analyse the factors affecting cycle performance. In the case of Sb2S3, volume change and surface reactions were identified as the major factors affecting the electrode stability. Polysulfide dissolution is not a main factor for short-term stability (Figure 3). The use of polyimide binder allows higher utilization of the Sb2S3 active material and provides good mechanical stability in the electrodes. In fact, some polyimide binders are active with Li and can lead to additional capacity in the electrode. Surface degradation and impedance change is suppressed by the use of FEC in the electrolyte. After judicial choosing the binder and electrolyte, electrodes with bulk Sb2S3 gives a charge capacity of close to 800 mAh g−1 with stable cycle stability. Particle size effect is not found to be crucial once the electrode configuration and electrolyte is optimized. Nano-particles, which are difficult to handle and synthesize in large-scale, are not necessary to provide good electrochemical performances. Even electrodes with bulk Sb2S3 can give up to 580 mAh g−1 at a rate of 2000 mA g−1, which is the highest ever recorded for materials with 10–20 μm size.


Sample preparation and characterization

Two different types of Sb2S3 samples were evaluated in this study: (1) Bulk crystalline Sb2S3 was obtained from Sigma Aldrich and used as it is (denoted as “Sb2S3” in the paper). (2) Crystalline Sb2S3 wire were made by an aqueous precipitation between SbCl3 in acetone and sodium thiosulfate (Na2S2O3) followed by a hydrothermal annealing at 150°C for 4 hours, adopted from procedure of Li et al.31.

Structure of the materials was studied by powder X-ray diffraction (XRD) with a Cu K_alpha (Bruker). Morphology and particle size of the tested materials were studied by field emission scanning electron microscope (SEM) with a JOEL JSM-7600F.

Electrochemical evaluation

The Sb2S3 active material was mixed with acetylene black (Alfa Aesar) and binder in a weight ratio of 6:2:2. 20wt% carbon was added to ensure sufficient electrical conductivity within the electrode. For binder, polyvinylidene fluoride (PVdF from Kynar HSV900), carboxymethyl cellulose sodium salt (CMC from Sigma Alrich) and polyimide binder (DB100 – Dreambond 100 from ISTUSA) were used. The materials were mixed in either 1-methyl-2-pyrrolidone (NMP) for PVdF and DB100 or de-ionized water for CMC to form a slurry. The slurry is then coated on roughened copper foil as a current collector using a doctor blade. The electrode was then dried at 80°C and compressed with a roll press. The electrodes were cut into 16 mm diameter discs and further dried at 110°C in vacuum for 4 hours before transferring into an Ar-filled glove box. An additional annealing step at 300°C for 5 hours in vacuum was performed on electrodes with DB100 to polymerize the binder before testing. Typical electrode thickness is between 20–30 μm with a packing density of about 1.0 g cm−3. The electrodes were assembled with Li metal as counter electrodes in a 2016 coin cell. 1 M lithium hexafluorophosphate (LiPF6) in ethylene carbonate (EC) to diethyl carbonate (DEC) of 1:1 is the typical electrolyte used in the cell. Electrolyte with fluoroethylene carbonate 4-fluoro-1,3-dioxolan-2-one (FEC) (1 M LiPF6 in FEC/DEC = 1:1) is also used to study how the stability of the electrodes with cycling can be improved chemically.

The cells were then tested with a battery tester between 0 to 2.5 V vs. Li/Li+. Typical charge-discharge rate was 100 mA g−1 during the first five cycles and 250 mA g−1 in subsequent cycles. Cyclic voltammetry profiles were taken at a scan rate of 0.1 mVs−1 between 0.005 V and 3 V vs. Li/Li+. Impedance measurements were carried with a potentiostat (Biologic VMP3) between 500 kHz and 5 mHz.


  1. 1.

    Materials science principles related to alloys of potential use in rechargeable lithium cells. J. Power Sources 26, 109–120 (1989).

  2. 2.

    , , & Sub-Microcrystalline Sn and Sn-SnSb Powders as Lithium Storage Materials for Lithium-Ion Batteries. Electrochem. Solid-State Lett. 2, 161–163 (1999).

  3. 3.

    , & Nano- and bulk-silicon-based insertion anodes for lithium-ion secondary cells. J. Power Sources 163, 1003–1039 (2007).

  4. 4.

    , , & Beyond Intercalation-Based Li-Ion Batteries: The State of the Art and Challenges of Electrode Materials Reacting Through Conversion Reactions. Adv. Mater. 22, E170–E192 (2010).

  5. 5.

    , , & Reactivity of transition metal (Co, Ni, Cu) sulphides versus lithium: The intriguing case of the copper sulphide. Solid State Sci. 8, 640–651 (2006).

  6. 6.

    , , , & Novel SnS2-nanosheet anodes for lithium-ion batteries. J. Power Sources 167, 529–535 (2007).

  7. 7.

    et al. Direct growth of high-rate capability and high capacity copper sulfide nanowire array cathodes for lithium-ion batteries. J. Mater. Chem. 20, 6638–6645 (2010).

  8. 8.

    & Sn-based nanomaterials converted from SnS nanobelts: Facile synthesis, characterizations, optical properties and energy storage performances. Electrochim. Acta 56, 243–250 (2010).

  9. 9.

    , , & Stibnite (Sb2S3) and its amorphous composite as dual electrodes for rechargeable lithium batteries. J. Mater. Chem. 20, 1097–1102 (2010).

  10. 10.

    , & MoS2 Nanoplates Consisting of Disordered Graphene-like Layers for High Rate Lithium Battery Anode Materials. Nano Lett. 11, 4826–4830 (2011).

  11. 11.

    et al. Few-layer SnS2/graphene hybrid with exceptional electrochemical performance as lithium-ion battery anode. J. Power Sources 201, 259–266 (2012).

  12. 12.

    , & Metal sulfide nanostructures: synthesis, properties and applications in energy conversion and storage. J. Mater. Chem. 22, 19–30 (2012).

  13. 13.

    , & Microwave synthesis of nanocrystalline Sb2S3 and its electrochemical properties. Mater. Res. Bull. 42, 1357–1363 (2007).

  14. 14.

    et al. Preparation of rod-like Sb2S3 dendrites processed in conventional hydrothermal. Mater. Lett. 63, 1258–1261 (2009).

  15. 15.

    et al. Conversion of hydroperoxoantimonate coated graphenes to Sb2S3@graphene for a superior lithium battery anode. Chem. Mater. 24, 4750–4757 (2012).

  16. 16.

    et al. High-capacity antimony sulphide nanoparticle-decorated graphene composite as anode for sodium-ion batteries. Nature Comm. 4, 2922; 10.1038/ncomms3922 (2013).

  17. 17.

    et al. Sb2S3 with Various Nanostructures: Controllable Synthesis, Formation Mechanism, and Electrochemical Performance toward Lithium Storage. Chem. a Eur. J. 16, 13210–13217 (2010).

  18. 18.

    , & The nanocomposites of carbon nanotube with Sb and SnSb0.5 as Li-ion battery anodes. Carbon 41, 959–966 (2003).

  19. 19.

    , & Performance Enhancing Electrolyte Additives for Lithium Ion Batteries with Silicon Anodes. J. Electrochem. Soc. 159, A642–A646 (2012).

  20. 20.

    et al. Effect of Fluoroethylene Carbonate (FEC) on the Performance and Surface Chemistry of Si-Nanowire Li-Ion Battery Anodes. Langmuir 28, 965–976 (2011).

  21. 21.

    et al. High performance silicon nanoparticle anode in fluoroethylene carbonate-based electrolyte for Li-ion batteries. Chem. Commun. 48, 7268–7270 (2012).

  22. 22.

    , , , & Significant electrochemical performance improvement of TiSnSb as anode material for Li-ion batteries with composite electrode formulation and the use of VC and FEC electrolyte additives. Electrochem. Commun. 24, 89–92 (2012).

  23. 23.

    , , , & Silicon Solid Electrolyte Interphase (SEI) of Lithium Ion Battery Characterized by Microscopy and Spectroscopy. J. Phys. Chem. C 117, 13403–13412 (2013).

  24. 24.

    , & Sodium Carboxymethyl Cellulose: A Potential Binder for Si Negative Electrodes for Li-Ion Batteries. Electrochem. Solid-State Lett 10, A17–A20 (2007).

  25. 25.

    , , , & On the binding mechanism of CMC in Si negative electrodes for Li-ion batteries. Electrochem. Commun. 9, 2801–2806 (2007).

  26. 26.

    et al. Improvement of cyclability of Si as anode for Li-ion batteries. J. Power Sources 192, 644–651 (2009).

  27. 27.

    , , & Silicon Composite Electrode with High Capacity and Long Cycle Life. Electrochem. Solid-State Lett. 12, A215–A218 (2009).

  28. 28.

    et al. SiOx–graphite as negative for high energy Li-ion batteries. J. Power Sources 196, 5667–5673 (2011).

  29. 29.

    et al. A Highly Cross-Linked Polymeric Binder for High-Performance Silicon Negative Electrodes in Lithium Ion Batteries. Ang. Chem. Inter. Ed 51, 8762–8767 (2012).

  30. 30.

    et al. Effect of polyimide binder on electrochemical characteristics of surface-modified silicon anode for lithium ion batteries. J. Power Sources 244, 521–526 (2013).

  31. 31.

    , , , & Growth of crystalline Sb2S3 nanorods by hydrothermal method. J. of Cryst. Growth 255, 342–347 (2003).

Download references


This study was supported by the National Research Foundation of Singapore under the TUM CREATE Centre for Electromobility and the Energy Research Institute at Nanyang Technological University, Singapore.

Author information


  1. School of Energy and Environment, City University of Hong Kong, Tat Chee Avenue, Kowloon, Hong Kong SAR

    • Denis Y. W. Yu
  2. TUM CREATE, #10-02 CREATE Tower, Singapore 138602, Singapore

    • Denis Y. W. Yu
    •  & Harry E. Hoster
  3. Energy Research Institute @ NTU, Nanyang Technological University, 50 Nanyang Avenue, Singapore 639798, Singapore

    • Denis Y. W. Yu
    •  & Sudip K. Batabyal


  1. Search for Denis Y. W. Yu in:

  2. Search for Harry E. Hoster in:

  3. Search for Sudip K. Batabyal in:


D.Y.W.Y. designed and carried out the electrochemical experiment and wrote the paper. H.E.H. supervised the work. S.K.B. performed material synthesis and characterization and co-wrote the paper.

Competing interests

The authors declare no competing financial interests.

Corresponding authors

Correspondence to Denis Y. W. Yu or Sudip K. Batabyal.

Supplementary information

Word documents

  1. 1.

    Supplementary Information

    Supplementary Information


By submitting a comment you agree to abide by our Terms and Community Guidelines. If you find something abusive or that does not comply with our terms or guidelines please flag it as inappropriate.

Creative Commons BY-NC-NDThis work is licensed under a Creative Commons Attribution-NonCommercial-NoDerivs 3.0 Unported License. The images in this article are included in the article's Creative Commons license, unless indicated otherwise in the image credit; if the image is not included under the Creative Commons license, users will need to obtain permission from the license holder in order to reproduce the image. To view a copy of this license, visit