Ionothermal Synthesis of Crystalline Nanoporous Silicon and Its Use as Anode Materials in Lithium-Ion Batteries
- 239 Downloads
Silicon has great potential as an anode material for high-performance lithium-ion batteries (LIBs). This work reports a facile, high-yield, and scalable approach to prepare nanoporous silicon, in which commercial magnesium silicide (Mg2Si) reacted with the acidic ionic liquid at 100 °C and ambient pressure. The obtained silicon consists of a crystalline, porous structure with a BET surface area of 450 m2/g and pore size of 1.27 nm. When coated with the nitrogen-doped carbon layer and applied as LIB anode, the obtained nanoporous silicon-carbon composites exhibit a high initial Coulombic efficiency of 72.9% and possess a specific capacity of 1000 mA h g−1 at 1 A g−1 after 100 cycles. This preparation method does not involve high temperature and pressure vessels and can be easily applied for mass production of nanoporous silicon materials for lithium-ion battery or for other applications.
KeywordsSilicon Anode material Nanomaterial Lithium-ion battery
Porous silicon nanoparticles
Nitrogen-doped carbon coated on porous silicon nanoparticles
Powder X-ray diffraction
Scanning electron microscopy
Transmission electron microscopy
X-ray photoelectron spectroscopy
The rapidly increasing consumption and high dependence on fossil energy in contemporary society have caused a growing sense of unease about the environment, climate, and energy supply. There is a pressing demand for developing sustainable, portable high-energy and high-power-density energy devices and systems to resolve the temporal energy source and environment mismatch for modern lifestyles . Rechargeable lithium-ion batteries (LIBs) hold remarkable promise for energy storage devices owing to their relatively high energy density and long cycle stability [2, 3]. To meet the increasing requirements of high-performance LIBs, various high-capacity electrode materials are being extensively developed, such as porous amorphous carboneous materials [4, 5], phosphorus-based composites [6, 7], silicon-based composites , and transition metal oxides [9, 10]. As a vital component, silicon (Si) is one of the most impressive anodic materials because of its large theoretical capacity (4200 mAh g−1), abundant natural sources and relatively safe Li-uptake voltage . Nevertheless, the large-scale practical commercialization of silicon anodic material is plagued by two intricate problems. On the one hand, the enormous volumetric expansion and contraction in the charge and discharge processes lead to the breakdown of the silicon active material, rapid irreversible capacity fading of the battery . On the other hand, the low intrinsic electroconductivity (1.6 × 10−3 S/m) of elemental silicon also greatly impedes electron transfer and decreases the rate capability of the electrode.
Recently, considerable efforts have been focused on circumventing the above-mentioned stability issues . A large number of nanostructured silicon materials including nanotubes , nanowires/nanorods [15, 16], and nanosheets [17, 18, 19] have been engineered to achieve improved structural integrity and cycle performance. Additionally, preparing Si-based porous composites is also considered as an effective method, because appropriate pore spaces in porous silicon composites could act as buffers to mitigate the volume expansion and thereby improve cycling performance in LIBs [20, 21]. For example, Kim et al. fabricated a three-dimensional porous silicon particles by thermal annealing and etching butyl-capped Si gels and SiO2 nanoparticles at 900 °C under an Ar atmosphere, which exhibited a stable capacity of over 2800 mA h g−1 after 100 cycles at 1 °C . An et al. reported a green, scalable, and controllable pathway to prepare nanoporous silicon (NP-Si) with excellent electrochemical properties from commercial Mg2Si alloy via high-temperature vacuum distillation . Though tremendous strides in the consummate electrochemical performance have been demonstrated, most of the preparation methods for these nanoporous structures of Si are generally too complicated to scale up.
Another effective tactic to boost the electrochemical performance of the silicon anode is coating electronically conductive carbon on nanosilicon particles to form silicon-carbon nanocomposites [19, 24], such as yolk-shell , watermelon , and hollow structures . For instance, Pan et al. designed yolk-shell–structured Si–C nanocomposites with high specific capacity and good cycling stability by a simple and low-cost method based on NaOH etching technology . Chen et al. developed a core-shell–structured Si/B4C composite with graphite coating and demonstrated that such composites possessed good long-term cycling stability . Various studies demonstrated that the conductive carbon could not only make up the low electrical conductivity of silicon, but also serve as an elastic intermediary to retard the large volume change and prevent the direct contact between silicon active materials and the electrolyte, leading to enhanced cycling stability .
To date, the synthetic routes to silicon nanoparticles (Si NPs) or porous silicon (pSi) usually involve thermal decomposition of silanes , chemical etching of Si wafers, and magnesiothermic reduction of SiO2 templates [32, 33]. These preparations generally require several steps, high temperature, relatively high-cost templates, etc., which lead to high cost and difficulties to scale up . Recently, the preparation of Si NPs in solution has also been paid much attention [35, 36]. For instance, Kauzlarich et al. reported that SiCl4 reacted with NaSi or KSi in organic solvents to obtain silicon nanoparticles . Liang et al. prepared the nest-like silicon nanospheres via a solvothermal reaction, in which NaSi reacted with NH4Br in the pyridine and dimethoxyethane mixed solvent in an autoclave at 80 °C for 24 h . The reported solution synthesis generally involved highly active reducing agents such as alkaline metals, LiAlH4, and NaSi and often produced low yields or small quantities of Si NPs. In this regard, for mass fabrication of nanosilicon, a low-cost, scalable, and simple approach is still imperative. Herein, we present a convenient, high-yield preparation of porous silicon by oxidation of Mg2Si in acidic ionic liquid at 100 °C and ambient pressure. When coated with a nitrogen-doped carbon layer and served as anode of lithium-ion battery, the obtained nanoporous silicon-carbon composites exhibited a high initial Coulombic efficiency (CE) of 72.9% and delivered a specific capacity of 1000 mA h g−1 after 100 cycles at 1 A g−1.
1-Butyl-3-methylimidazolium chloride ([Bmim]Cl) was provided by Shanghai Cheng Jie Chemical Co. LTD. Aluminum chloride (AlCl3) was purchased from Sinopharm Chemical Reagent Co., Ltd. Magnesium silicide (Mg2Si) and commercial silicon powder (1–5 μm) were bought from Alfa Aesar. Battery-grade ethylene carbonate (EC), diethyl carbonate (DEC), fluoroethylene carbonate (FEC), and LiPF6 were purchased from Shenzhen Kejingstar Technology Ltd., China. All of the chemicals and reagents were used directly as received.
Synthesis of Porous Silicon Nanoparticles (pSi)
In a typical procedure, [Bmim]Cl (1.5 g) and AlCl3 (4.5 g) with a molar ratio of ~ 1:4 were mixed and loaded in a Schlenk glass tube. Subsequently, 500 mg of magnesium silicide (Mg2Si) were added into the glass tube and vigorously agitated at 100 °C for 10 h. The above procedure was conducted in a glovebox filled with Ar. After cooling down, the precipitate was collected and washed with 1 M hydrochloric acid, distilled water, and ethanol. Finally, the product (150 mg, 82% yield) was dried in vacuum for further characterization.
Synthesis of Nitrogen-Doped Carbon Coated on Porous Silicon Nanoparticles (pSi@NC)
The preparation procedure is referred to the reported literatures [39, 40]. First, 0.1 g of the obtained porous silicon nanoparticles (pSi) were dispersed into 250 mL of deionized water containing sodium dodecylbenzenesulfonate (SDBS; 5 mg) by ultrasonication for 30 min. The mixture was vigorously agitated for 1 h at room temperature. After that, 200 μL of pyrrole monomer, 0.34 g of (NH4)2S2O8, and 1.25 mL of 1 M HCl were added into the above solution. After the mixture was stirred in an ice/water bath for 24 h, the formed black powders (denoted as pSi@PPy) were gathered by filtration, washed with deionized water, and dried in vacuum. Finally, the pSi@PPy sample was heated at a ramp rate of 5 °C min−1 in a tube furnace to 700 °C for 3 h in a flowing Ar atmosphere to obtain the pSi@NC composite. The carbon content was estimated by thermogravimetric studies.
The electrochemical properties of porous silicon nanoparticles were studied by using a half CR2032 coin cell, in which lithium metal foils served as counter electrodes and reference electrode, the as-prepared pSi@NC as working electrode, polypropylene macroporous films (Celgard 2400) as separators, and 1.0 M LiPF6 in 1:1 (v/v) mixture of ethylene carbonate (EC)/diethyl carbonate (DEC) as the electrolyte. The CR2032 cells were assembled in a glovebox with argon atmosphere (oxygen and water contents less than 0.1 ppm). The working anode electrodes were prepared by mixing the obtained pSi@NC composite, super P carbon, and sodium alginate in a weight ratio of 70:20:10 in deionized water to form a homogeneous slurry. Next, the slurry was coated onto Cu foil and dried under vacuum condition at 80 °C for 12 h. The total loading mass of the active materials on the electrode was approximately 0.5 mg cm−2. The charge-discharge cycles of the half-cells were performed on a Neware battery tester (Shenzhen, China) at a constant current mode over the range of 0.01–1.5 V. Cyclic voltammetry (CV) of the as-prepared anodes was measured on a CHI650d electrochemical workstation (Shanghai Chenhua Instruments Inc., China), using a three-electrode cell with the voltage sweep rate of 0.2 mV s−1 at room temperature. The specific capacity was calculated based on the total mass of the pSi@NC composites.
Power X-ray diffraction (PXRD) measurements were carried out on a Bruker D8 ADVANCE X-ray diffractometer (Cu Kα radiation, 40 kV, 40 mA, λ = 1.5418 Å). The morphology and microstructure of the samples were obtained by scanning electron microscopy (Hitachi field-emission scanning electron microscope, S-4800), and the energy-dispersive X-ray spectroscopy was used to analyze the elemental distribution. Transmission electron microscopy (TEM) and high-resolution TEM images were recorded on a JEM-2100 equipment. The porous parameters were determined using a Micromeritics ASAP 2020 analyzer at 77 K after degassing of the sample at 150 °C for 10 h. The specific surface area was calculated using the multiple-point Brunauer−Emmett−Teller (BET) method, and the pore size distribution was analyzed by the density functional theory (DFT) method based on the adsorption data. Raman spectroscopy (LabRAM Aramis, Horiba, equipped with a 633-nm wavelength laser) was used to investigate the structure of nanoporous silicon, which was first calibrated with a Si wafer (520 cm−1). PHI 5000 VersaProbe spectrometer was used for X-ray photoelectron spectroscopy (XPS) measurements. Thermogravimetric analysis (TGA) was conducted on a simultaneous STA449F3 (Netzche) thermal analyzer under air atmosphere at 10 °C min−1 from 30 to 800 °C in air flowing. Cyclic voltammetry (CV) tests were performed on a CHI650d electrochemical station (Shanghai Chenhua Instruments Inc., China).
Results and Discussion
Figure 4b illustrates the first two discharge–charge curves of the pSi@NC composite anodes cycling at a current density of 0.1 A g−1. The pSi@NC composite had a long and flat discharge terrace around 0.1 V during the first discharge, which is in accordance with the characteristic terrace of the Li insertions of crystalline Si. The well-crystallized silicon turned amorphous and showed the representative charge/discharge profiles of amorphous silicon in subsequent cycles. The other potential plateaus which appeared around 0.6 V during the first lithiation process resulted from the SEI formation . The results were in good agreement with the CV curves. The initial discharge and charge capacities were 2790 and 2036 mA h g−1, delivering a high initial Coulombic efficiency (CE) of 72.9%. The lower charge capacity could partly be due to the constraining effect of the oxide layer SiOx, which served as buffers to limit the volume expansion and extent of lithiation [58, 59]. Importantly, no obvious capacity decay was observed in the subsequent cycles, and the Coulombic efficiency was maintained nearly constant at around 100%.
Figure 4c shows the cycling performance of the pSi@NC composites anodes, which were conducted at a current density of 0.1 A g−1 for 100 cycles and at a current density of 1 A g−1 for subsequent 100 cycles. The pSi@NC nanocomposite anodes showed a capacity of 1720 mA h g−1 after 110 cycles at a current density of 0.1 A g−1, corresponding to a 79% capacity retention. Furthermore, the pSi@NC composite electrodes delivered a reversible capacity of 1010 mA h g−1 at 1 A g−1 after subsequent 110 cycles, with a capacity decay rate of 0.2% per cycle from 101 to 210th cycle. Figure 4d shows the rate performance of the pSi@NC electrode. The pSi@NC electrode achieved discharge capacities of 2360, 1690, 1570, 1470, 1320, and 850 mA h g−1 at the current density of 0.1, 0.3, 0.5, 1.0, 2.0, and 5.0 A g−1, respectively. The discharge capacity could be recovered to approximately 2160 mA h g−1 when the current density was returned back to 0.1 A g−1, proving that the pSi@NC composite anode had an outstanding electrochemical reversibility. In comparison, commercial silicon powder (Fig. 4e) coated with the conducting nitrogen-doped carbon as an anode reached a high initial discharge capacity of 3230 mA h g−1, but suffered severe capacity deterioration to 110 mA h g− 1 after 100 cycles at 0.1 A g−1. These result suggested that the conducting nitrogen-doped carbon layer and the porous structure in pSi@NC could provide the fast ion/electron transport pathways and maintained the structural stability, thus endowing the pSi@NC composite anode with good rate performance and excellent reversibility [21, 39, 60]. In addition, surface oxidation in pSi might also contribute to improve the cycling efficiency of lithium-ion batteries, which limited the volume expansion of the silicon particles and avoided some side reactions according to the previous studies .
In summary, we developed a new method to prepare nanoporous silicon in high yields based on the reaction of magnesium silicide (Mg2Si) in acidic ionic liquid. When coated with the nitrogen-doped carbon layer and applied as an anode of lithium-ion battery, the obtained silicon-carbon composites exhibited high reversible capacity, long-term cycling stability, and high initial Columbic efficiency. The N-doped carbon-coating layer supplied the efficient conductive pathways for fast lithium-ion transportation and electron transfer, which is beneficial for enhancing the electrochemical properties of silicon particles. Since the reaction condition is relatively mild, and the yield of the products is over 82%, this preparation method could be extended to the mass production of silicon anode materials.
This work was supported by the National Natural Science Foundation of China (21471075 and 21673115).
Availability of Data and Materials
FW carried out this study. BZ and WZ contributed to the data analysis. HD contributed to the manuscript revision and polishing. All authors discussed the results and approved the final manuscript.
The authors declare that they have no competing interests.
Springer Nature remains neutral with regard to jurisdictional claims in published maps and institutional affiliations.
- 9.Zhu GY, Wang L, Lin HN, Ma LB, Zhao PY, Hu Y, Chen T, Chen RP, Wang YR, Tie ZX, Liu J, Jin Z (2018) Walnut-like multicore–shell MnO encapsulated nitrogen rich carbon nanocapsules as anode material for long cycling and soft-packed lithium-ion batteries. Adv Funct Mater 28:180003CrossRefGoogle Scholar
- 10.Karunakaran G, Kundu M, Maduraiveeran G, Kolesnikov E, Gorshenkov MV, Balasingam SK, Kumari S, Sasidharan M, Kuznetsov D (2018) Hollow mesoporous heterostructures negative electrode comprised of CoFe2O4@Fe3O4 for next generation lithium ion batteries. Microporous Mesoporous Mater 272:1–7CrossRefGoogle Scholar
- 12.Ko M, Chae S, Cho J (2015) Challenges in accommodating volume change of Si anodes for Li-ion batteries. Chem Electro Chem 2:1645–1651Google Scholar
- 31.Li YZ, Yan K, Lee HW, Lu ZD, Liu N, Cui Y (2016) Growth of conformal graphene cages on micrometre-sized silicon particles as stable battery anodes. Nat Energy 1:15029Google Scholar
- 47.Childres I, Jauregui LA, Park W, Cao H, Chen YP (2013) Raman spectroscopy of graphene and related materials. In: Jang JI (ed), New developments in photon and materials research. Nova Science Publishers, New YorkGoogle Scholar
- 50.Xu C, Lindgren F, Philippe B, Gorgoi M, Björefors F, Edström K, Gustafsson T (2015) Improved performance of the silicon anode for Li-ion batteries: understanding the surface modification mechanism of fluoroethylene carbonate as an effective electrolyte additive. Chem Mater 27:2591–2599CrossRefGoogle Scholar
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.