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Nano-Micro Letters

, 10:50 | Cite as

Bi2Se3/C Nanocomposite as a New Sodium-Ion Battery Anode Material

  • Lixin Xie
  • Ze Yang
  • Jingying Sun
  • Haiqing Zhou
  • Xiaowei Chi
  • Hailong Chen
  • Andy X. Li
  • Yan Yao
  • Shuo Chen
Open Access
Communication

Abstract

Bi2Se3 was studied as a novel sodium-ion battery anode material because of its high theoretical capacity and high intrinsic conductivity. Integrated with carbon, Bi2Se3/C composite shows excellent cyclic performance and rate capability. For instance, the Bi2Se3/C anode delivers an initial capacity of 527 mAh g−1 at 0.1 A g−1 and maintains 89% of this capacity over 100 cycles. The phase change and sodium storage mechanism are also carefully investigated.

Keywords

Bi2Se3 Sodium-ion battery High-energy ball milling Sodium storage mechanism 

1 Highlights

  • Bi2Se3 was investigated as a novel sodium-ion battery anode material.

  • Sodiation/desodiation mechanism of Bi2Se3 has been carefully investigated.

  • Bi2Se3/C electrode demonstrates high cycling stability.

2 Introduction

Sodium-ion batteries (SIBs) have recently regained extensive research interest as alternatives to lithium-ion batteries (LIBs) for energy storage owing to the low cost and abundance of Na [1, 2, 3, 4, 5]. The lack of high energy density anode materials has impeded the progress of SIBs for a long time [6]. Developing suitable anode materials for SIBs with both high capacity and long cycle life is highly desired. Among anode materials, alloying-type materials [7] have attracted much attention. For example, Sn, Sb, and Bi can reversibly alloy with Na+ and provide high theoretical gravimetric capacities (> 300 mAh g−1), which far exceed the capacities of carbonaceous materials and Ti-based materials. The accompanying challenge for alloying-type materials is the large volume expansion when alloying with Na+. Bi displays a relatively small volume expansion (ca. 250% expansion from Bi to Na3Bi), compared to Sn (ca. 420% expansion from Sn to Na3.75Sn) and Sb (ca. 293% expansion from Sb to Na3Sb) [8], which is beneficial for a stable anode [9]. The voltage plateau is also an important criterion in evaluating an electrode material. A low operating voltage for anode materials can endow a cell with a high operation voltage. However, Na plating, dendrite formation, and electrolyte decomposition occur on the anode side when the discharge voltage approaches 0 V, as is often the case for hard carbon anodes [10, 11, 12]. The plateaus of Bi between 0.3 and 0.9 V versus Na+/Na are favorable for maintaining a high operation voltage and avoiding the aforementioned detrimental effects [13, 14].

Sulfides and selenides have been actively investigated because their conversion reactions offer high capacities for ion storage [15, 16, 17, 18]. Recently, the Bi-based compound Bi2S3 has been synthesized and displayed a high Na storage capacity [19, 20]. However, the rate capacity was unsatisfactory, limited by the low intrinsic conductivity of sulfides [15]. Bi2Se3 displays an electrical conductivity two orders of magnitude higher than that of Bi2S3 [21], which can improve the electron transport. In addition, the shuttle effect is relieved for selenides compared to sulfides [22]. Moreover, Bi2Se3 has a high density of 7.47 g cm−3 [21], permitting the opportunity to fabricate small-sized devices with high volumetric capacities (theoretically 3667 mAh cm−3). Bi2Se3 has been applied in LIBs and exhibited excellent electrochemical storage ability for Li+. Several Bi2Se3 nanostructures, such as nanosheets and microrods, have been designed for Li+ storage [23, 24]. Furthermore, high free electron densities can effectively improve the rate capability; thus, doping strategies have been employed to create S-doped and In-doped Bi2Se3 [25, 26, 27]. Despite the good electrochemical performance in Li+ storage, Bi2Se3 has not been reported as an anode material for SIBs.

Downsizing the bulk material to nanoscale and integrating carbon with it can improve the electrochemical performance, including the rate capability and cyclability, by the shorter diffusion distances, more abundant reaction sites on the large surface area, and additional space for expansion [28, 29, 30, 31]. Carbon can stabilize the nanomaterial and provide an interconnected network for electron transport as well, and the voids in the carbon can accommodate volume expansion and allow permeation of the electrolyte for fast Na+ transport [32, 33, 34].

In our study, a simple high-energy ball milling (HEBM) method was adopted to synthesize Bi2Se3 and Bi2Se3/C nanocomposite. The Bi2Se3/C nanocomposite delivers an initial reversible capacity of 527 mAh g−1 at 0.1 A g−1 with 89% retention over 100 cycles. The phase changes during cycling were investigated by ex situ X-ray diffraction (XRD) to reveal the Na storage mechanism. The rational material design combined with effective synthetic protocol is important and this work is expected to shed light on future work on developing excellent anode materials for SIBs.

3 Experimental

3.1 Synthesis Process

The synthesis of Bi2Se3 and Bi2Se3/C was performed by HEBM. Bi (Alfa Aesar, 99.999%) and Se (Alfa Aesar, 99.999%) in a molar ratio of 2:3 were sealed in an Ar-filled stainless steel jar and then ball milled for 10 h at 1200 rpm (Spex 8000 M) to form phase-pure Bi2Se3 powder. Graphite powders were milled for 48 h beforehand. Then, the milled graphite was added to Bi2Se3 powders in the weight ratio of 2:8 and ball milled for another 6 h to form the carbon-integrated Bi2Se3 nanocomposite.

3.2 Material Characterization

The phases were investigated by XRD on a Rigaku SmartLab diffractometer with a Cu Kα source at the scan rate of 5 deg. min−1. The morphology was studied under scanning electron microscopy (SEM, LEO 1525). The nanostructures and the diffraction patterns were characterized by transmission electron microscopy (TEM, JEOL 2010F, operated under 200 kV). The elemental mapping was collected by energy-dispersive X-ray spectroscopy (EDS) (attached to the TEM). X-ray photoelectron spectroscopy (XPS) measurements were performed on a PHI Quantera XPS instrument. To confirm the carbon content, the samples were heated at 10 °C min−1 from room temperature to 600 °C in thermogravimetric analysis (TGA, Q500).

3.3 Electrochemical Measurements

Coin cells (CR 2025) with Bi2Se3 or Bi2Se3/C as the active material were assembled for battery tests. A slurry was made by mixing 70 wt% active material, 20 wt% carbon black, and 10 wt% polyacrylic acid (PAA) and then coated on a Cu foil to form the working electrodes, followed by drying at 60 °C under vacuum overnight. To prepare the electrolyte, 1 mol L−1 NaClO4 was dissolved in propylene carbonate/ethylene carbonate (1:1 in volume) with 5 wt% fluoroethylene carbonate (FEC) as an additive. The loading of the active materials was 1.4 ± 0.2 mg cm−2 for the Bi2Se3/C electrode and 1.5 ± 0.3 mg cm−2 for the Bi2Se3 electrode. Homemade Na lumps and glass fibers were applied as the reference/counter electrodes and the separators, respectively. The electrochemical measurements of the cells were performed galvanostatically between 0.01 and 2.5 V versus Na/Na+ on a Land CT2001A battery tester. Cyclic voltammetry (CV) curves were swept at 0.1 mV s−1 on a BioLogic SP-200 electrochemical workstation. Electrochemical impedance spectroscopy (EIS) was measured from 100 kHz to 100 mHz with a voltage amplitude of 5 mV.

4 Results and Discussion

Figure 1 displays the structural and morphological characterization details of Bi2Se3 and Bi2Se3/C. The XRD patterns of Bi2Se3 and Bi2Se3/C are shown in Fig. 1a. The ball milled Bi2Se3 and Bi2Se3/C display the same XRD patterns, which match well with the pure rhombohedral phase (space group \( R\bar{3}m \) (166), JCPDS card No. 33-0214). After ball milling with carbon for another 6 h, the peaks of Bi2Se3/C become broader, indicating that smaller nanocrystals are produced. The crystal structure is again confirmed in the electron diffraction patterns of Fig. 1b, with the rings well indexed as the planes (0 0 6), (1 0 1), (0 1 5), (0 1 8), and (1 0 10) of rhombohedral-phase Bi2Se3. The TEM image in Fig. 1c and high-resolution TEM image in Fig. 1d show that the secondary Bi2Se3 particles are composed of well-developed nanocrystals with sizes ranging from a few nanometers to tens of nanometers. Figure 1e, f demonstrate that the Bi2Se3 nanocrystals are well encapsulated and uniformly distributed in the carbon matrix after integration with carbon. The primary nanocrystal sizes are approximately 5–20 nm, much smaller than those of as-synthesized Bi2Se3 because the carbon matrix can well separate and stabilize Bi2Se3 nanocrystals [32]. To reflect nanocrystal sizes across the samples, additional high-resolution TEM images are provided in Fig. S1. The particle sizes of the Bi2Se3/C nanocomposite also grow finer due to the separation of carbon compared to those of bare Bi2Se3, as observed in the SEM images (Fig. S2). Clear fringes of the crystal planes of Bi2Se3 can be found in Fig. 1f, indicating that the Bi2Se3 maintains good crystallinity in the carbon composite. In Fig. 1g, the uniform distribution of the elements Bi, Se, and C is confirmed by the EDS mapping. The carbon content of the composite is further confirmed to be 20.7 wt% by the TGA test (Fig. S3).
Fig. 1

a XRD patterns of as-synthesized Bi2Se3 and Bi2Se3/C. b The diffraction pattern of Bi2Se3. c Low- and d high-resolution TEM images of Bi2Se3. e Low- and f high-resolution TEM images of Bi2Se3/C. g Scanning TEM (STEM) image and its corresponding elemental (Bi, Se, and C) mappings

The half-cell of Bi2Se3/C was cycled at a scan rate of 0.1 mV s−1 within 0.01–2.5 V versus Na+/Na and the IV curves are shown in Fig. 2a. Three cathodic peaks at 1.04, 0.52, and 0.27 V and four anodic peaks at 1.88, 1.7, 0.79, and 0.67 V are depicted in the first cycle. The peak positions are analogous to those in Bi2S3 anode because of the similar properties between S and Se as chalcogens [14, 19, 20]. In the cathodic scan, Bi and Na2Se form at 1.04 V [19, 20], followed by the sodiation of Bi at lower voltages of 0.52 and 0.27 V [14]. In the reverse scan, desodiation of the Na–Bi alloy occurs at 0.67 and 0.79 V [14], then NaBiSe2 is formed at 1.7 and 1.88 V [19, 20, 35]. The peak at 1.04 V in the first cycle is slightly shifted to 1.14 V in the following cycle. Other than this shift, the CV curves overlap very well, which indicates a highly reversible Na storage kinetics. Figure S4 also displays the CV curve of Bi2Se3. The same characteristics are observed in the CV curves of Bi2Se3 and Bi2Se3/C, which indicate that integrating carbon does not affect the sodiation process of Bi2Se3. However, integrating carbon does improve the stability of the electrode, which is evidenced by the obvious decrease in the peak intensities of bare Bi2Se3 over CV cycling.
Fig. 2

Studies of electrochemical properties of the Bi2Se3/C anode for SIBs. a CV curves of the Bi2Se3/C anode at 0.1 mV s−1. b Cyclic performance of Bi2Se3/C and Bi2Se3 anodes at 0.1 A g−1 and the related Coulombic efficiency of Bi2Se3/C anode. c Discharge/charge profiles and d rate performance of Bi2Se3/C anode at different current densities

The cyclic performances of Bi2Se3 and Bi2Se3/C at 0.1 A g−1 and the related Coulombic efficiency of the Bi2Se3/C anode are shown in Fig. 2b. Alloying and conversion anodes often show lower Coulombic efficiencies than intercalation anodes. At the first cycle, the Bi2Se3 and Bi2Se3/C anodes both display reasonably high Coulombic efficiencies (> 75%), indicating higher utilization of Na+ than most alloying anodes. With carbon integrated, the reversible capacity of Bi2Se3/C anode (527 mAh g−1) is somewhat comprised compared to the capacity of 557 mAh g−1 for the Bi2Se3 anode at the first cycle. In the following cycles, however, the Bi2Se3/C anode exhibits much improved stability, reaching a steady value of 510 mAh g−1 within five cycles and retaining 89% of the initial capacity over 100 cycles, while the Bi2Se3 anode displays a fast decay in capacity to below 200 mAh g−1 within 20 cycles. At a higher current density of 0.5 A g−1, the Bi2Se3/C anode still shows high stability with an initial capacity of 445 mAh g−1 after the first two cycles at 0.1 A g−1 and that of 383 mAh g−1 over 180 cycles (Fig. S5). The cyclic performance of Bi2Se3/C is superior to those of other Bi-based materials and competitive with many typical anode materials (Table S1) [36, 37, 38, 39, 40, 41]. Although the initial capacity of Bi2Se3/C is not extremely high compared to those of similar materials reported, the unique advantage of this composite is its stability in long-term cycling. For example, at 0.1 A g−1, the capacity of 470 mAh g−1 for Bi2Se3/C composite at the 100th cycle is more than triple that of Bi@C microspheres [42] and ca. 50% higher than that of Bi2S3 nanorods at the 40th cycle [19]. Figure 2c shows the voltage profiles of the Bi2Se3/C anode for a wide range of discharge/charge rates between 0.01 and 2.5 V versus Na+/Na. At the low current density of 0.1 A g−1, the plateaus can be clearly identified with three discharge plateaus and four charge plateaus, corresponding to the peaks in the CV curves. The discharge/charge profiles maintain analogous shapes and plateaus even at very high current densities, indicating the fast reaction kinetics of the Na storage process. The details of the fast reaction kinetics may be ascribed to the fast capacitive contribution, as discussed later. Figure 2d shows the excellent rate capability of Bi2Se3/C as an anode material for SIBs. Remarkably, it delivers the high capacities of 500, 445, 415, 384, 332, 298, 255, and 186 mAh g−1 at 0.1, 0.3, 0.5, 1, 3, 5, 7, and 10 A g−1, respectively. To confirm the high reversibility, 0.1 A g−1 is applied again after cycling at 10 A g−1, and the capacity returns to its previous level as expected. The rate capacities of Bi2Se3/C are competitive with those of typical anode materials listed in Table S2 and the performance is better at high current densities. The volumetric capacity is also an important consideration for practical application; that of the Bi2Se3/C electrode reaches 1064 mAh cm−3, calculated by multiplying the volumetric density of Bi2Se3/C (2.02 g cm−3) with the gravimetric capacity (527 mAh g−1) at 0.1 A g−1.

To explore the insights of sodiation/desodiation mechanism of Bi2Se3, ex situ XRD was conducted. After charging/discharging, the electrodes were removed from the cells in a glove box and covered with Kapton tapes to avoid oxidation. The sampling points were chosen in reference to the dQ/dV curves in Fig. 3a. When the anode is sodiated to 0.86 V from the open-circuit voltage, the Bi2Se3 characteristic peak disappears while Bi peaks appear with Na2Se [14]. The XRD patterns of Bi and Na2Se are maintained when the material is discharged to a low voltage of 0.47 V. In this process, the intercalation of Na+ into Bi may occur. The phase of NaBi appears at 0.01 V, indicating that alloying reaction occurs at the complete sodiation state [8, 43]. In the desodiation process, Bi dealloys with Na+, evidenced by the appearance of the Bi phase at 0.88 V. However, even at the highest potential of 2.5 V, the Bi2Se3 phase does not recover; instead, NaBiSe2 with Bi phases are formed [19]. The irreversible Bi2Se3 change can also explain the peak shifting from 1.04 V in the first cycle to 1.14 V in the following cycles in the IV curves of Fig. 2a. When the electrode is again sodiated to 1.05 V at the second cycle, diffraction patterns corresponding to Bi and Na2Se appear again. In summary, the phase changes during cycling can be listed as the following four steps:
Fig. 3

a

dQ/dV plots for the first two cycles and b ex-situ XRD results of the Bi2Se3/C anode

Sodiation process:
$$ {\text{conversion}}\;{\text{reaction: Bi}}_{2} {\text{Se}}_{3} + \, 6{\text{Na}}^{ + } + \, 6{\text{e}}^{ - } \to 2{\text{Bi}} + 3{\text{Na}}_{2} {\text{Se }}\left( {\text{irreversible}} \right) $$
(1)
$$ {\text{alloying}}\;{\text{reaction}}{:}{\text{ Bi}} + x{\text{Na}}^{ + } + \, x{\text{e}}^{ - } \to {\text{Na}}_{x} {\text{Bi}} $$
(2)
Desodiation process
$$ {\text{dealloying}}\;{\text{reaction}}{:}{\text{ Na}}_{x} {\text{Bi}} \to {\text{Bi }} + \, x{\text{Na}}^{ + } + \, x{\text{e}}^{ - } $$
(3)
$$ {\text{conversion}}\;{\text{ reaction}}{:}{\text{ Bi}} + 2{\text{Na}}_{2} {\text{Se}} \to {\text{NaBiSe}}_{2} + 3{\text{Na}}^{ + } + \, 3{\text{e}}^{ - } $$
(4)
In addition to XRD analysis, XPS was also applied to provide a more comprehensive understanding of the materials and the electrochemical process, because XPS is sensitive to the surface within the depth of ca. 5 nm. Figure S7 displays the XPS survey spectrum and high-resolution spectra of Bi 4f and Se 3d for Bi2Se3/C electrode. The peaks at 163.7 and 158.4 eV are assigned to Bi 4f5/2 and Bi 4f7/2, respectively. The peaks at 54.3 and 53.5 eV correspond to Se 3d3/2 and Se 3d5/2 in Bi2Se3, respectively, confirming the successful synthesis of Bi2Se3 [44]. In addition, the peaks related to BiO x and SeO x are also found, indicating oxidation happens at the surface [44]. The solid electrolyte interface (SEI) compositions were also investigated by comparing the electrode before and after one cycle. Figure 4 indicates significant changes in the C 1s and F 1s spectra. The pristine electrode has a strong signal at 284.6 eV related to the carbon bonds of graphite or carbon black, and the small peaks at 285.3, 285.9, and 288.8 eV correspond to –CH2–, –CH–COONa, and R–COONa of the PAA binder [9, 45]. After one cycle, several new peaks are formed in the higher binding energy region and the strong signal at 284.6 eV related to graphite and carbon black disappears, indicating the formation of the SEI film on the surface. The signals from 286.0 to 289.5 eV are assigned to the –C–O– and –C=O– species of the SEI film and the peak at 291.1 eV arises from Na2CO3 of the SEI film [9, 46]. The signal related to F 1s appears after one cycle, indicating that the SEI film contains F from the decomposition of FEC.
Fig. 4

High-resolution XPS spectra a C 1s and b F 1s of the Bi2Se3/C electrode before and after one cycle

The reaction kinetics can be revealed by EIS and the EIS spectra of Bi2Se3/C electrode and Bi2Se3 electrode are displayed in Fig. 5a. The intercept with the Zreal axis at high frequency represents the electrolyte and contact resistance (Rs), while the semicircles at medium frequency are related to the SEI resistance (Rf) and electrolyte/electrode charge transfer resistance (Rct) [47]. The equivalent circuit model for the fitting is shown in the inset of Fig. 5a with the fitting results listed in Table S3. Rct of the Bi2Se3/C electrode decreases significantly from 661.4 to 81.4 Ω after cycling benefited from the reconstructed porous structure with close connections, as seen under SEM (Fig. S8) [48]. On the contrary, the EIS spectra of Bi2Se3 display a large Rct increase after cycling due to the contact loss. For the Bi2Se3 electrode after cycling, large aggregates are formed with rough surfaces and loose contact between particles. In addition, the Rf increase of 19.9 Ω for the Bi2Se3 electrode is more significant than that of 6.8 Ω for the Bi2Se3/C electrode, caused by the fracture and the continuous growth of a thick SEI layer in the Bi2Se3 electrode.
Fig. 5

a EIS spectra for Bi2Se3 and Bi2Se3/C anodes before and after five cycles. b CV curves of the Bi2Se3/C anode at different scan rates. c, d b-value fitted by the relationship of the logarithm peak currents and logarithm scan rates

For nanomaterials with large surface areas, surface-induced capacitive processes can have significant effects and improve the charge/discharge capability [49, 50, 51]. The b value is often used as an index to estimate the surface-induced capacitive contribution. According to i = aν b , where i is the current response at the scan rate ν, the b value can be readily fitted by log(i) − log(ν) linear plots. The b value can vary from 0.5 to 1. The capacitive process dominates when the b value is close to 1, while diffusion-controlled processes dominate when the b value approaches 0.5. Figure 5b shows the IV curves at different scan rates for the Bi2Se3/C electrode; the relations of log(i) and log(ν) at the corresponding peaks derived from the IV curves are shown in Fig. 5c, d. The fitted b values are 0.71, 0.82, 0.78, and 0.74 for the R1, R2–1, R2–2, R3 peaks and 0.85, 0.85, 0.98, and 0.86 for O1–1, O1–2, O2, and O3 peaks. These values are much higher than 0.5, which indicates that fast capacitive process occurs during Na storage, contributing to the high rate capacity for the Bi2Se3/C electrode. The current and scan rate relations are not shown for Bi2Se3 electrode because of the significant changes of the CV curves over cycling.

5 Conclusions

The application of Bi2Se3 was explored as an anode material for SIBs. Benefiting from the high theoretical capacity and high intrinsic conductivity of Bi2Se3, the positive effects of carbon, and the effective HEBM method, a high-performance anode material was achieved. The Bi2Se3/C electrode showed a high reversible capacity of 527 mAh g−1 and retains 89% of this capacity over 100 cycles at 0.1 A g−1. To obtain insights regarding the electrochemical process of Na storage, the phase changes were revealed by ex situ XRD.

Notes

Acknowledgements

The authors thank the support from TcSUH as the TcSUH Robert A. Welch Professorships on High Temperature Superconducting (HTSg) and Chemical Materials (E-0001). H.C. acknowledges the support from the National Science Foundation under grant number DMR-1410936.

Supplementary material

40820_2018_201_MOESM1_ESM.pdf (827 kb)
Supplementary material 1 (PDF 828 kb)

References

  1. 1.
    V. Palomares, P. Serras, I. Villaluenga, K.B. Hueso, J. Carretero-González, T. Rojo, Na-ion batteries, recent advances and present challenges to become low cost energy storage systems. Energy Environ. Sci. 5(3), 5884–5901 (2012).  https://doi.org/10.1039/c2ee02781j CrossRefGoogle Scholar
  2. 2.
    H. Kim, H. Kim, Z. Ding, M.H. Lee, K. Lim, G. Yoon, K. Kang, Recent progress in electrode materials for sodium-ion batteries. Adv. Energy Mater. 6(19), 1600943 (2016).  https://doi.org/10.1002/aenm.201600943 CrossRefGoogle Scholar
  3. 3.
    S. Chu, Y. Cui, N. Liu, The path towards sustainable energy. Nat. Mater. 16(1), 16–22 (2016).  https://doi.org/10.1038/nmat4834 CrossRefGoogle Scholar
  4. 4.
    Z. Yang, Y. Jiang, L. Deng, T. Wang, S. Chen, Y. Huang, A high-voltage honeycomb-layered Na4NiTeO6 as cathode material for Na-ion batteries. J. Power Sources 360, 319–323 (2017).  https://doi.org/10.1016/j.jpowsour.2017.06.014 CrossRefGoogle Scholar
  5. 5.
    C.P. Grey, J.M. Tarascon, Sustainability and in situ monitoring in battery development. Nat. Mater. 16(1), 45–56 (2016).  https://doi.org/10.1038/nmat4777 CrossRefGoogle Scholar
  6. 6.
    N. Yabuuchi, K. Kubota, M. Dahbi, S. Komaba, Research development on sodium-ion batteries. Chem. Rev. 114(23), 11636–11682 (2014).  https://doi.org/10.1021/cr500192f CrossRefGoogle Scholar
  7. 7.
    M. Lao, Y. Zhang, W. Luo, Q. Yan, W. Sun, S.X. Dou, Alloy-based anode materials toward advanced sodium-ion batteries. Adv. Mater. 29(48), 1700622 (2017).  https://doi.org/10.1002/adma.201700622 CrossRefGoogle Scholar
  8. 8.
    L.D. Ellis, B.N. Wilkes, T.D. Hatchard, M.N. Obrovac, In situ XRD study of silicon, lead and bismuth negative electrodes in nonaqueous sodium cells. J. Electrochem. Soc. 161(3), A416–A421 (2014).  https://doi.org/10.1149/2.080403jes CrossRefGoogle Scholar
  9. 9.
    C. Wang, L. Wang, F. Li, F. Cheng, J. Chen, Bulk bismuth as a high-capacity and ultralong cycle-life anode for sodium-ion batteries by coupling with glyme-based electrolytes. Adv. Mater. 29(35), 1702212 (2017).  https://doi.org/10.1002/adma.201702212 CrossRefGoogle Scholar
  10. 10.
    M.M. Doeff, Y. Ma, S.J. Visco, L.C.D. Jonghe, Electrochemical insertion of sodium into carbon. J. Electrochem. Soc. 140(12), 169–170 (1993).  https://doi.org/10.1149/1.2221153 CrossRefGoogle Scholar
  11. 11.
    S. Komaba, W. Murata, T. Ishikawa, N. Yabuuchi, T. Ozeki, T. Nakayama, A. Ogata, K. Gotoh, K. Fujiwara, Electrochemical Na insertion and solid electrolyte interphase for hard-carbon electrodes and application to Na-ion batteries. Adv. Funct. Mater. 21(20), 3859–3867 (2011).  https://doi.org/10.1002/adfm.201100854 CrossRefGoogle Scholar
  12. 12.
    Y. Li, Y.-S. Hu, M.-M. Titirici, L. Chen, X. Huang, Hard carbon microtubes made from renewable cotton as high-performance anode material for sodium-ion batteries. Adv. Energy Mater. 6(18), 1600659 (2016).  https://doi.org/10.1002/aenm.201600659 CrossRefGoogle Scholar
  13. 13.
    M. Dahbi, N. Yabuuchi, K. Kubota, K. Tokiwa, S. Komaba, Negative electrodes for Na-ion batteries. Phys. Chem. Chem. Phys. 16(29), 15007–15028 (2014).  https://doi.org/10.1039/c4cp00826j CrossRefGoogle Scholar
  14. 14.
    D. Su, S. Dou, G. Wang, Bismuth: a new anode for the Na-ion battery. Nano Energy 12, 88–95 (2015).  https://doi.org/10.1016/j.nanoen.2014.12.012 CrossRefGoogle Scholar
  15. 15.
    Z. Hu, Q. Liu, S.-L. Chou, S.-X. Dou, Advances and challenges in metal sulfides/selenides for next-generation rechargeable sodium-ion batteries. Adv. Mater. 29(48), 1700606 (2017).  https://doi.org/10.1002/adma.201700606 CrossRefGoogle Scholar
  16. 16.
    Z. Liu, T. Lu, T. Song, X.-Y. Yu, X.W. Lou, U. Paik, Structure-designed synthesis of FeS2@C yolk–shell nanoboxes as a high-performance anode for sodium-ion batteries. Energy Environ. Sci. 10(7), 1576–1580 (2017).  https://doi.org/10.1039/c7ee01100h CrossRefGoogle Scholar
  17. 17.
    Y. Kim, Y. Kim, Y. Park, Y.N. Jo, Y.J. Kim, N.S. Choi, K.T. Lee, SnSe alloy as a promising anode material for Na-ion batteries. Chem. Commun. 51(1), 50–53 (2015).  https://doi.org/10.1039/c4cc06106c CrossRefGoogle Scholar
  18. 18.
    X. Duan, J. Xu, Z. Wei, J. Ma, S. Guo, H. Liu, S. Dou, Atomically thin transition-metal dichalcogenides for electrocatalysis and energy storage. Small Methods 1(11), 1700156 (2017).  https://doi.org/10.1002/smtd.201700156 CrossRefGoogle Scholar
  19. 19.
    W. Sun, X. Rui, D. Zhang, Y. Jiang, Z. Sun, H. Liu, S. Dou, Bismuth sulfide: a high-capacity anode for sodium-ion batteries. J. Power Sources 309, 135–140 (2016).  https://doi.org/10.1016/j.jpowsour.2016.01.092 CrossRefGoogle Scholar
  20. 20.
    W. Yang, H. Wang, T. Liu, L. Gao, A Bi2S3@CNT nanocomposite as anode material for sodium ion batteries. Mater. Lett. 167, 102–105 (2016).  https://doi.org/10.1016/j.matlet.2015.12.108 CrossRefGoogle Scholar
  21. 21.
    W. Liu, K.C. Lukas, K. McEnaney, S. Lee, Q. Zhang, C.P. Opeil, G. Chen, Z. Ren, Studies on the Bi2Te3–Bi2Se3–Bi2S3 system for mid-temperature thermoelectric energy conversion. Energy Environ. Sci. 6(2), 552–560 (2013).  https://doi.org/10.1039/c2ee23549h CrossRefGoogle Scholar
  22. 22.
    Y. Lu, P. Zhou, K. Lei, Q. Zhao, Z. Tao, J. Chen, Selenium phosphide (Se4P4) as a new and promising anode material for sodium-ion batteries. Adv. Energy Mater. 7(7), 1601973 (2017).  https://doi.org/10.1002/aenm.201601973 CrossRefGoogle Scholar
  23. 23.
    H. Xu, G. Chen, R. Jin, J. Pei, Y. Wang, D. Chen, Hierarchical Bi2Se3 microrods: microwave-assisted synthesis, growth mechanism and their related properties. CrystEngComm 15(8), 1618–1625 (2013).  https://doi.org/10.1039/c2ce26678d CrossRefGoogle Scholar
  24. 24.
    Z. Ali, C. Cao, J. Li, Y. Wang, T. Cao, M. Tanveer, M. Tahir, F. Idrees, F.K. Butt, Effect of synthesis technique on electrochemical performance of bismuth selenide. J. Power Sources 229, 216–222 (2013).  https://doi.org/10.1016/j.jpowsour.2012.11.120 CrossRefGoogle Scholar
  25. 25.
    F. Mao, J. Guo, S. Zhang, F. Yang, Q. Sun, J. Ma, Z. Li, Solvothermal synthesis and electrochemical properties of S-doped Bi2Se3 hierarchical microstructure assembled by stacked nanosheets. RSC Adv. 6(44), 38228–38232 (2016).  https://doi.org/10.1039/c6ra01301e CrossRefGoogle Scholar
  26. 26.
    R. Jin, J. Liu, Y. Xu, G. Li, G. Chen, L. Yang, Hierarchical Bi2Se3–xSx microarchitectures assembled from ultrathin polycrystalline nanosheets: solvothermal synthesis and good electrochemical performance. J. Mater. Chem. A 1(36), 10942 (2013).  https://doi.org/10.1039/c3ta12030a CrossRefGoogle Scholar
  27. 27.
    G. Han, Z.-G. Chen, D. Ye, L. Yang, L. Wang, J. Drennan, J. Zou, In-doped Bi2Se3 hierarchical nanostructures as anode materials for Li-ion batteries. J. Mater. Chem. A 2(19), 7109–7116 (2014).  https://doi.org/10.1039/c4ta00045e CrossRefGoogle Scholar
  28. 28.
    Y. Liu, N. Zhang, L. Jiao, Z. Tao, J. Chen, Ultrasmall Sn nanoparticles embedded in carbon as high-performance anode for sodium-ion batteries. Adv. Funct. Mater. 25(2), 214–220 (2015).  https://doi.org/10.1002/adfm.201402943 CrossRefGoogle Scholar
  29. 29.
    Y. Kim, Y. Kim, A. Choi, S. Woo, D. Mok et al., Tin phosphide as a promising anode material for Na-ion batteries. Adv. Mater. 26(24), 4139–4144 (2014).  https://doi.org/10.1002/adma.201305638 CrossRefGoogle Scholar
  30. 30.
    J. Duan, W. Zhang, C. Wu, Q. Fan, W. Zhang, X. Hu, Y. Huang, Self-wrapped Sb/C nanocomposite as anode material for high-performance sodium-ion batteries. Nano Energy 16, 479–487 (2015).  https://doi.org/10.1016/j.nanoen.2015.07.021 CrossRefGoogle Scholar
  31. 31.
    Y.N. Ko, Y.C. Kang, Electrochemical properties of ultrafine Sb nanocrystals embedded in carbon microspheres for use as Na-ion battery anode materials. Chem. Commun. 50(82), 12322–12324 (2014).  https://doi.org/10.1039/c4cc05275g CrossRefGoogle Scholar
  32. 32.
    Z. Yang, J. Sun, Y. Ni, Z. Zhao, J. Bao, S. Chen, Facile synthesis and in situ transmission electron microscopy investigation of a highly stable Sb2Te3/C nanocomposite for sodium-ion batteries. Energy Storage Mater. 9, 214–220 (2017).  https://doi.org/10.1016/j.ensm.2017.07.010 CrossRefGoogle Scholar
  33. 33.
    S. Ni, J. Ma, J. Zhang, X. Yang, L. Zhang, Electrochemical performance of cobalt vanadium oxide/natural graphite as anode for lithium ion batteries. J. Power Sources 282, 65–69 (2015).  https://doi.org/10.1016/j.jpowsour.2015.01.187 CrossRefGoogle Scholar
  34. 34.
    J. Ma, S. Ni, J. Zhang, X. Yang, L. Zhang, The charge/discharge mechanism and electrochemical performance of CuV2O6 as a new anode material for Li-ion batteries. Phys. Chem. Chem. Phys. 17(33), 21442–21447 (2015).  https://doi.org/10.1039/c5cp03435c CrossRefGoogle Scholar
  35. 35.
    Q. Wang, W. Zhang, C. Guo, Y. Liu, C. Wang, Z. Guo, In situ construction of 3D interconnected FeS@Fe3C@graphitic carbon networks for high-performance sodium-ion batteries. Adv. Funct. Mater. 27(41), 1703390 (2017).  https://doi.org/10.1002/adfm.201703390 CrossRefGoogle Scholar
  36. 36.
    Q. Wang, C. Guo, Y. Zhu, J. He, H. Wang, Reduced graphene oxide-wrapped FeS2 composite as anode for high-performance sodium-ion batteries. Nano-Micro Lett. 10, 30 (2018).  https://doi.org/10.1007/s40820-017-0183-z CrossRefGoogle Scholar
  37. 37.
    J. Liang, X. Gao, J. Guo, C. Chen, K. Fan, J. Ma, Electrospun MoO2@NC nanofibers with excellent Li+/Na+ storage for dual applications. Sci. China Mater. 61(1), 30–38 (2017).  https://doi.org/10.1007/s40843-017-9119-2 CrossRefGoogle Scholar
  38. 38.
    J. Liang, C. Yuan, H. Li, K. Fan, Z. Wei, H. Sun, J. Ma, Growth of SnO2 nanoflowers on N-doped carbon nanofibers as anode for Li- and Na-ion batteries. Nano-Micro Lett. 10(2), 21 (2018).  https://doi.org/10.1007/s40820-017-0172-2 CrossRefGoogle Scholar
  39. 39.
    Y. Zhou, W. Sun, X. Rui, Y. Zhou, W.J. Ng, Q. Yan, E. Fong, Biochemistry-derived porous carbon-encapsulated metal oxide nanocrystals for enhanced sodium storage. Nano Energy 21, 71–79 (2016).  https://doi.org/10.1016/j.nanoen.2015.12.003 CrossRefGoogle Scholar
  40. 40.
    X. Zhang, Y. Zhou, B. Luo, H. Zhu, W. Chu, K. Huang, Microwave-assisted synthesis of NiCo2O4 double-shelled hollow spheres for high-performance sodium Ion batteries. Nano-Micro Lett. 10(1), 13 (2017).  https://doi.org/10.1007/s40820-017-0164-2 CrossRefGoogle Scholar
  41. 41.
    M. Mao, C. Cui, M. Wu, M. Zhang, T. Gao et al., Flexible ReS2 nanosheets/N-doped carbon nanofibers-based paper as a universal anode for alkali (Li, Na, K) ion battery. Nano Energy 45, 346–352 (2018).  https://doi.org/10.1016/j.nanoen.2018.01.001 CrossRefGoogle Scholar
  42. 42.
    F. Yang, F. Yu, Z. Zhang, K. Zhang, Y. Lai, J. Li, Bismuth nanoparticles embedded in carbon spheres as anode materials for sodium/lithium-ion batteries. Chem.-Eur. J. 22(7), 2333–2338 (2016).  https://doi.org/10.1002/chem.201503272 CrossRefGoogle Scholar
  43. 43.
    J. Sottmann, M. Herrmann, P. Vajeeston, Y. Hu, A. Ruud, C. Drathen, H. Emerich, H. Fjellvåg, D.S. Wragg, How crystallite size controls the reaction path in nonaqueous metal ion batteries: the example of sodium bismuth alloying. Chem. Mater. 28(8), 2750–2756 (2016).  https://doi.org/10.1021/acs.chemmater.6b00491 CrossRefGoogle Scholar
  44. 44.
    D. Kong, J.J. Cha, K. Lai, H. Peng, J.G.A.S. Meister et al., Rapid surface oxidation as a source of surface degradation factor for Bi2Se3. ACS Nano 5(6), 4698–4703 (2011).  https://doi.org/10.1021/nn200556h CrossRefGoogle Scholar
  45. 45.
    S.R. Leadley, J.F. Watts, The use of XPS to examine the interaction of poly(acrylic acid) with oxidised metal substrates. J. Electron Spectrosc. 85(1–2), 107–121 (1997).  https://doi.org/10.1016/S0368-2048(97)00028-5 CrossRefGoogle Scholar
  46. 46.
    F.A. Soto, P. Yan, M.H. Engelhard, A. Marzouk, C. Wang et al., Tuning the solid electrolyte interphase for selective Li- and Na-ion storage in hard carbon. Adv. Mater. 29(18), 1606860 (2017).  https://doi.org/10.1002/adma.201606860 CrossRefGoogle Scholar
  47. 47.
    S. Ni, J. Zhang, J. Ma, X. Yang, L. Zhang, X. Li, H. Zeng, Approaching the theoretical capacity of Li3VO4 via electrochemical reconstruction. Adv. Mater. Interfaces 3(1), 1500340 (2016).  https://doi.org/10.1002/admi.201500340 CrossRefGoogle Scholar
  48. 48.
    S. Ni, J. Ma, J. Zhang, X. Yang, L. Zhang, Excellent electrochemical performance of NiV3O8/natural graphite anodes via novel in situ electrochemical reconstruction. Chem. Commun. 51(27), 5880–5882 (2015).  https://doi.org/10.1039/c5cc00486a CrossRefGoogle Scholar
  49. 49.
    J. Wang, J. Polleux, J. Lim, B. Dunn, Pseudocapacitive contributions to electrochemical energy storage in TiO2 (anatase) nanoparticles. J. Phys. Chem. C 111(40), 14925–14931 (2007).  https://doi.org/10.1021/jp074464w CrossRefGoogle Scholar
  50. 50.
    C. Chen, Y. Wen, X. Hu, X. Ji, M. Yan, L. Mai, P. Hu, B. Shan, Y. Huang, Na+ intercalation pseudocapacitance in graphene-coupled titanium oxide enabling ultra-fast sodium storage and long-term cycling. Nat. Commun. 6, 6929 (2015).  https://doi.org/10.1038/ncomms7929 CrossRefGoogle Scholar
  51. 51.
    X. Deng, Z. Wei, C. Cui, Q. Liu, C. Wang, J. Ma, Oxygen-deficient anatase TiO2@C nanospindles with pseudocapacitive contribution for enhancing lithium storage. J. Mater. Chem. A 6(9), 4013–4022 (2018).  https://doi.org/10.1039/c7ta11301c CrossRefGoogle Scholar

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© The Author(s) 2018

Open AccessThis article is distributed under the terms of the Creative Commons Attribution 4.0 International License (http://creativecommons.org/licenses/by/4.0/), which permits unrestricted use, distribution, and reproduction in any medium, provided you give appropriate credit to the original author(s) and the source, provide a link to the Creative Commons license, and indicate if changes were made.

Authors and Affiliations

  • Lixin Xie
    • 1
  • Ze Yang
    • 1
  • Jingying Sun
    • 1
  • Haiqing Zhou
    • 1
  • Xiaowei Chi
    • 2
  • Hailong Chen
    • 3
  • Andy X. Li
    • 4
  • Yan Yao
    • 2
  • Shuo Chen
    • 1
  1. 1.Department of Physics and TcSUHUniversity of HoustonHoustonUSA
  2. 2.Department of Electrical and Computer Engineering and Materials Science and Engineering ProgramUniversity of HoustonHoustonUSA
  3. 3.The Woodruff School of Mechanical EngineeringGeorgia Institute of TechnologyAtlantaUSA
  4. 4.Clements High SchoolSugar LandUSA

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