High capacity and stable all-solid-state Li ion battery using SnO2-embedded nanoporous carbon.

Extensive research efforts are devoted to development of high performance all-solid-state lithium ion batteries owing to their potential in not only improving safety but also achieving high stability and high capacity. However, conventional approaches based on a fabrication of highly dense electrode and solid electrolyte layers and their close contact interface is not always applicable to high capacity alloy- and/or conversion-based active materials such as SnO2 accompanied with large volume change in charging-discharging. The present work demonstrates that SnO2-embedded nanoporous carbons without solid electrolyte inside the nanopores are a promising candidate for high capacity and stable anode material of all-solid-state battery, in which the volume change reactions are restricted in the nanopores to keep the constant electrode volume. A prototype all-solid-state full cell consisting of the SnO2-based anode and a LiNi1/3Co1/3Mn1/3O2-based cathode shows a good performance of 2040 Wh/kg at 268.6 W/kg based on the anode material weight.

Introduction

All-solid-state lithium ion batteries (ASS−LIBs) with nonflammable solid electrolyte have attracted growing interest because of the safety precaution required for widespread use of Li ion batteries (LIBs) in power-grid applications, electric vehicles and so on[1,2]. Although the low ionic conductivity of solid electrolyte (SE) has limited so far the development of ASS−LIB to a thin film-type cell[3-5], the recent discovery of highly ionic conductive SE such as sulfide-based compounds, of which conductivity was over 10−3 S cm−1 (refs[6-10]), prompt us to develop a bulk-type cell composed of active materials and SE powders. This is expected to lead high capacity ASS-LIBs instead of LIBs using organic liquid electrolytes (OLE−LIBs).

Conventional researches on ASS−LIBs have focused on fabrication of highly dense electrode layer and SE layer as well as their close contact interface to yield enough Li ion conducting paths[11-14], which is quite different from OLE−LIBs. However, large capacity active materials such as Si, Sn, P, SnO2 and so on, which are accompanied with large volume change in their Li−alloying/dealloying and metal oxide to metal conversion reactions, are difficult to apply to the present ASS−LIB system. The close contact at the SE/electrode interface and densely packing in the electrode are not maintained for such active materials due to the formation of crack and void with the volume change during charge-discharge cycling. It was reported that an increase in compressive pressure of ASS-cell using silicon and Li electrodes to keep the interface contact improved the cycle performance, but the capacity was decreased due to the limitation of reactions[15,16].

Here, we report on the first attempt of applying active material-embedded porous carbon electrode materials to ASS−LIBs. The novel strategy of this study is as follows; (1) the porous carbon framework is used as a three-dimensional electron conducting path in the electrode, (2) the carbon nanopores play an important role of a buffer space for the volume change during charge−discharge reactions to keep the constant electrode volume and then a stable contact of SE/electrode interface. Porous materials as a battery electrode are considered to have disadvantage of low volumetric capacity, but this is not the case for the present study because the pore space provided in advance is compensated by the inevitable volume expansion of lithiated active materials. Here we found out that a SnO2−embedded nanoporous carbon fulfills their functions as the active electrode material in ASS system and surprisingly shows high capacity and good cycle stability superior to those in OLE system. One more fascinating discovery of this study is that Li ion conduction occurs successfully in the carbon nanospace without SE beyond expectation. The approach is applicable to other alloy- and conversion-based active materials with large volume change in principle, thus the present study will open the door for the development of high performance ASS-LIBs with high capacity and high stability.

Results

Preparation and characterization of SnO2–embedded nanoporous carbons

Embedding of SnO2 nanocrystallites into nanopores of porous carbons was carried out by introducing SnCl2 vapor into the carbon nanopores, a subsequent hydrolysis and dryness according to the previous report[17,18]. A porous carbon with an average pore diameter of 45 or 140 nm, which was obtained by a silica opal template process[19], was used here for the above syntheses. In the following, the porous carbon and the SnO2-embedded carbon nanocomposites are denoted as CX and SnO2/CX[Y], where X and Y indicate the average pore diameter of porous carbon and the loading amount of SnO2, respectively. Powder X-ray diffraction (XRD) measurements confirmed that SnO2 nanocrystallites with the primary crystallite size around 3 nm, which was estimated from the full width at half-maximum of (110) XRD peak using the Scherrer equation, were produced in the composite samples (Supplementary Fig. 1). It was observed by scanning electron microscopy (SEM) and transmission electron microscopy (TEM) that SnO2 nanocrystallites with the size around 3 nm, which was consistent with the primary crystallite size estimated from XRD, were deposited preferentially in the carbon nanopores (Fig. 1). As shown in Fig. 1f, the SnO2 nanocrystallites were closely accumulated on the surface of carbon pore wall for the high SnO2-loading sample of SnO2/C140[75]. Table 1 shows structural parameters of SnO2 contents, specific surface areas (Sa) and specific pore volumes (Vp) of samples, as well as weighted average values of Sa (Sa,w) and Vp (Vp,w) which are calculated under the assumption of a simple mixing of CX and SnO2 nanocrystallites with the primary crystallite size. The Sa and Vp values were decreased with increasing the loading amount of SnO2 and they were much smaller than the weighted average values. In addition, the pore size distribution was shifted toward smaller pore size range with the increase in SnO2 loading amount (Supplementary Fig. 2). These results demonstrated almost perfect embedding of SnO2 nanocrystallites in carbon nanopores of CX.

Figure 1

Porous composite structure of SnO2/CX[Y]. (a,b) SEM images of SnO2/C45[73]; (b) is an enlarge image. (c) TEM image of SnO2/C45[73]. (d) SEM image of SnO2/C140[75]. (e) TEM image of SnO2/C140[75]. (f) Enlarged image of the yellow frame area in e.

Table 1

Structural parameters of SnO2/CX[Y].

Sample	Y (wt%)	Sa (m2/g)	Sa,w (m2/g)	Vp (cm3/g)	Vp,w (cm3/g)
SnO2/C140[Y]	06170	1073326279	1073594523	2.000.560.38	2.000.780.60
SnO2/C45[Y]	0566872	1093548223220	1093604518489	4.421.820.920.90	4.421.941.411.24

Y: SnO2 content, Sa: Specific surface area, Vp: specific pore volume, Sa,w and Vp,w: calculated values of Sa and Vp under the assumption of a simple mixing of CX and SnO2.

Charge-discharge properties of SnO2–embedded nanoporous carbons

The charge-discharge measurements were carried out on an ASS half-cell, which was composed of a working electrode (WE) layer of mixture of SnO2/CX[Y] and LiI-Li2S-P2S5 (SE), the SE layer and a Li foil (see experimental section). Figure 2a shows an SEM image of a cross section of SE layer and working electrode layer using SnO2/C140[62] of a disassembled ASS half-cell. Since the sample was peeled off from the current collector for the observation, there were some cracks in the WE layer. SE and SnO2/C140[62] domains were existed in the WE layer (Fig. 2b), and some of SnO2/C140[62] domains were covered by stretched SE, which was deformed from as-prepared SE particles during the milling and pressing processes for the cell construction (Supplementary Fig. 3). It was confirmed that the porous structure of SnO2/C140[62] was maintained without filling SE in nanopores even after the cell construction (Fig. 2c,d and e). Sight signals of S and Sn remained in the black area out of SnO2/C140[62] and SE domains in Fig. 2d,e, respectively, are due to inevitable background signals caused by continuous X-ray. No existence of the solid electrolyte inside the nanopores was also confirmed by STEM-EELS-EDX analysis (Supplementary Fig. 4).

Figure 2

Cross-sectional morphology of SnO2/C140[62]-electrode layer and SE layer in disassembled ASS half-cell. (a) SEM image of the interface of these layers. (b) SEM image of the electrode layer part in a; the darker areas with smooth surface correspond to particulate and/or stretched SE. Rough and porous surface areas are of SnO2/C140[62] domains. The dotted yellow circle areas indicate representative SE-covered SnO2/C140[62] domains. (c) Enlarged SEM image of the interface between SE and SnO2/C140[62] large domain. (d,e) EDX elementary mapping of sulfur (d) and tin (e) in c. Here EDX data were taken on the large domain to avoid the additional signals behind domains.

In Fig. 3, the initial charge-discharge curves of SnO2/C45[72] are shown as a representative example and are compared with those measured in an organic liquid electrolyte (OLE) half-cell. The initial discharge process on the ASS system included irreversible capacity, but it was much smaller than that in the OLE due to the solid electrolyte interface formation. The ASS system surprisingly showed higher charge capacity than the OLE system and clear dQ/dV peaks of dealloying reaction of LixSn around 0.5 V and conversion reaction of Sn to SnOy above 0.9 V, of which potentials are consistent with those in the OLE system and the previous reported. It was also confirmed that the potential of dQ/dV peaks was consistent with that of anodic peaks in CV curve (Supplementary Fig. 5). The initial charge capacity in the ASS system was 750 mAh/g based on the composite weight, which was corresponding to 1042 mAh/g based on SnO2 weight because the capacity due to C45 was negligibly small. The high capacity over the theoretical capacity of either Sn-Li alloying-dealloying reaction (781 mAh/g) or SnO2-Sn conversion reaction (711 mAh/g), indicating the contribution of both reactions on the charging-discharging. It can be concluded that the SnO2-embedded porous carbon functions successfully as a high capacity electrode active material in ASS system.

Figure 3

Initial charge-discharge properties of SnO2/CX[Y] versus Li/Li+ in all-solid state (ASS) and organic liquid electrolyte (OLE) systems. (a) Initial charge-discharge and dQ/dV curves of SnO2/C45[72]. (b) Initial charge capacity as a function of SnO2-loading amount of SnO2/C140[Y] (brown) and SnO2/C45[Y] (blue and gray).

Although Li ions in OLE system can easily access to SnO2 in SnO2/CX[Y] composites via the penetration of liquid electrolyte into the carbon nanopore space, it is not the case for ASS system because the SE is located outside of carbon nanopores. Therefore, the higher capacity of SnO2/C45[72] in ASS system than that in OLE system suggests that any Li ions conduction path exists throughout the SnO2-embedded carbon nanospace. Considering this point, the effect of loading amount of SnO2 (Y) on the capacity was investigated on the ASS system. As shown in Fig. 3b, the capacity was increased with increasing the Y value and especially SnO2-loading at Y > 65 was effective to yield high capacity. The tendency is quite different from that in OLE system, which was previously reported that the capacity is almost constant at Y < 65 and it drops at Y > 65 (ref.[18]). Highly SnO2-loading at Y > 65 in carbon nanopores is necessary to have an effective Li-ion conducting path in the SnO2/CX[Y] composite from the outside SE for the ASS system, which may be formed through the phases such as LixSn, Sn and LixO produced by the reaction of SnO2 nanoparticles with Li ions. A detailed investigation on the Li-ion conduction mechanism is now in progress.

Prototype full cell performance

The charge-discharge properties during 30 cycling were investigated at room temperature on a prototype ASS full-cell using SnO2/C45[72] and LiNbO3-coated LiNi1/3Co1/3Mn1/3O2 as active anode and cathode materials, respectively (Fig. 4). The initial charge-discharge capacities based on anode material weight were comparable to those observed on the ASS half-cell taking into account that the anode/cathode capacity ratio was set at 1.2 for the cell assembly. The capacities after a few cycles were almost constant around 600 mAh/g-anode. The coulombic efficiency was above 95% after the 2nd cycle and the discharge capacity retention was above 86% even after 30 cycles. The cycle performance in the ASS system was superior to that in the OLE system, of which capacity retention was 50% at the 30th cycle as previously reported[18]. The average operating voltage of the ASS full-cell is 3.4 V, thus the specific energy density is considered to be 2040 Wh/kg at the specific power density of 268.6 W/kg based on the anode material weight. The prototype cell shows an even better performance than a liquid electrolyte-type cell.

Figure 4

Performance of the prototype all-solid-state full cell. (a) Charge-discharge curves at 0.1 C and room temperature. (b) Cycle performance of capacity in the range of 2.0–4.5 V. (c) Coulombic efficiency versus cycle number. (d) Discharge capacity retention.

Discussion

In the present study, we disclosed that SnO2-embedded porous carbons are a promising candidate for stable and high capacity anode materials in ASS–LIB system. The high capacity is achieved on the samples with high SnO2-loading amount over 65 wt%, which is considered to be caused by a formation of effective Li ion conducting path in the SnO2-embedded carbon nanopores. Here we discuss the SnO2-loading amount-dependent property from simple calculations. When spherical nanoparticles of SnO2 with the diameter of 3 nm, which was confirmed by the TEM observation, are closely packed and form a single nanoparticulate layer on the surface of mesopores and macropores of original porous carbon, the coverage ratio of SnO2-related layer against the carbon pore surface is calculated to be 28–30% for the as-prepared SnO2/C45[72] and SnO2/C140[70] by using the specific mesopore and macropore surface areas of C45 (682 m2/g) and C140 (660 m2/g) determined by GCMC method. The coverage value is too low to carry Li ions via the loaded SnO2 throughout nanopores in SnO2/CX[Y] without filling SE inside unless all of SnO2 nanoparticles are located around the pore mouths contacted with outside SE. However, the coverage value is calculated to be 71–76% after the full reaction of SnO2 with Li ions, which is accompanied with the 2.12 time volume expansion for the conversion of SnO2 to Sn and Li2O as well as the 3.57 time volume expansion of Li4.4Sn against Sn, that is totally 4.05 time volume expansion based on SnO2 (Supplementary calculations). This means that effective Li ion conduction paths are formed in SnO2/CX[Y] from the outside SE probably through the phases such as LixSn, Sn and LixO produced by the reaction of Li ions with SnO2 nanoparticles, thus the highly SnO2-loading is necessary to yield high capacity.

In summary, the use of the SnO2-embedded porous carbons was demonstrated as an effective strategy for developing stable and high capacity all-solid-state Li ion batteries. At the present, the prototype cell using SnO2/C45[72] showed a specific energy density of 2040 Wh/kg at the specific power density of 268.6 W/kg based on the anode material weight which is even better performance than a liquid electrolyte-type cell. On the other hand, development of Si-, SiOx- and Ge-embedded porous carbons as a high capacity and stable electrode in OLE system was reported recently[20-22]. By optimization of the composite structure and exploiting the compositional versatility using Si, SiOx, Ge and so on, therefore, we could further extend the possible sets of electrodes for advanced all-solid-state batteries.

Methods

Synthesis of SnO2/nanoporous carbon composites

A nanoporous carbon with an average pore diameter (X nm) of 140 nm or 45 nm, which was denoted as CX, was obtained by a silica opal template process according to the previous report[19]. A mixture of SnCl2 (Kishida Chemical Co. Ltd.) and CX was heated in a sealed tube at 593 K for 24 h. The CX used was preheated at 393 K for 2 h under vacuum to remove adsorbed water. 400 mg of the mixed sample obtained above was dispersed in 600 mL of pure water and was filtered off to remove unreacted SnCl2, and then was dried in vacuo for overnight. The obtained composite is referred to as SnO2/CX[Y], where Y indicates wt% of the SnO2 content.

Structural Characterization

Powder X-ray diffraction (XRD) patterns of samples were obtained on a Rigaku RINT-2200 diffractometer using CuKα radiation. The SnO2 content in samples was estimated by thermogravimetric analysis (TGA, SEIKO Instrument Inc, TG/DTA7300). The specific surface areas were determined by αs-plot analysis[23,24] from the N2 adsorption isotherm at 77 K (MicrotracBEL Co. Ltd. BELSORP-max). Pore size distribution and pore volume of samples were analyzed by Grand Canonical Monte Carlo (GCMC) method[25]. The morphology of samples was observed by scanning electron microscope (SEM, JEOL JSM-7500FAM) and high-resolution scanning transmission electron microscope (HR-STEM; ARM-200CF, JEOL Ltd.). The SEM image and EDX analysis data of a cross-section of solid electrolyte/anode were taken on the material peeled off from the current collector sheet in an Ar-filled glove box after a half-cell construction described below.

Electrochemical Measurements

A two electrode all-solid-state cell was used to investigate electrochemical properties of SnO2/CX[Y]. A glassy solid electrolyte (SE) was prepared by mechanical milling of a 10:90 mixture by weight% of LiI (Aldrich, 99.999%) and 75Li2S-25P2S5 (mol%) at 370 rpm for 40 hours with a planetary ball-milling apparatus (Fritsch Japan Co. Ltd, P-7), which was followed by heating at 583 K for 2 hours in vacuum. The 75Li2S-25P2S5 was obtained according to the previous paper[26]. For the working electrode, the SE and SnO2/CX[Y] with the volume ratio of 50:50 were dispersed in heptane by using a homogenizer, and then dried on a hot plate in an Ar atmosphere. A typical cell was fabricated in an Ar-filled glove box using a macol cylinder with 1.0 cm2 cross-section area as follows. The SnO2/CX[Y] and SE composite (16.8 mg) was pressed on a stainless-steel sheet at 1 ton/cm2 in the cylinder, and subsequently a SE layer (100 mg) was formed by pressing at 40 ton/cm2. Then a Li foil was placed on the surface of SE side of the bilayer to construct a half-cell. Cycling test was carried out by using a prototype full-cell which was fabricated by utilizing the SnO2/CX[Y] and SE composite as an anode and a 50:48:2 mixture by volume% of LiNbO3-coated LiNi1/3Co1/3Mn1/3O2 (Nb-LNCM), the SE and vapor grown carbon fiber (VGCF, Showa Denko K.K.) as a cathode. The Nb-LNCM was prepared according to the procedure previously reported[14]. The cell construction was carried out by the same manner as that for the half cell. The cathode and anode were assembled so that the capacity ratio of cathode/anode was 1.2.

Electrochemical charge-discharge curves were measured on an electrochemical analyzer (Hokuto Denko, HJ-SM8) at 25 °C. A charging-discharging at a constant current (CC) mode was carried out for the half-cell of ASS system at the current density of 0.1 C in the potential range of 0.01–2.5 V vs. Li/Li+ after the initial discharging from open circuit voltage to 0.01 V. The 0.1 C corresponds to the current density of 79 mA g−1 based on the weight of SnO2/CX[Y]. The full-cell test was performed by using a constant current and constant voltage (CC−CV) mode in the potential range of 4.5–2.0 V at the cut-off current 0.01 C. Electrochemical properties of SnO2/CX[Y] in an organic liquid electrolyte was also investigated according to the previous report[18] using a Li counter electrode and a 1.0 mol dm−3 LiPF6 in ethylene carbonate/dimethyl carbonate (1/1 by volume).

Supporting Information