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Solid-State Lithium Batteries with Cathode-Supported Composite Solid Electrolytes Enabling High Rate Capability and Excellent Cyclic Performance

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29 August 2023

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30 August 2023

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Abstract
In this study, robust composite solid electrolytes were developed and employed them to enhance the performance of Li-metal batteries significantly. The robust composite solid electrolytes are composed of a soft polymer, poly(ethylene oxide), a Li salt, bis(trifluoromethanesulfonyl)imide (LiTFSI), and super ionic conductive ceramic fillers such as Li1.5Al0.5Ti1.5(PO4)3 (LATP), and Li6.4La3Zr1.4Ta0.6O12 (LLZTO). The main goal of this study is to enhance the electrochemical stability and ionic conductivity. The ionic conductivities of the composite solid electrolytes were found to be 2.08 × 10-4 and 1.64 × 10-4 S cm-1 with the introduction of LATP and LLZTO fillers, respectively. The results prove that the fabricated solid electrolyte was electrochemical stable at voltage exceeding 4.25 V vs. Li/Li+. The internal resistance of the solid electrolyte significantly reduced as compare to gel electrolyte. This reduction can be attributed owing to the alleviation of bulk electrolyte, charge-transfer, and interfacial electrolyte/electrode impedance. When LiFePO4 cathode sheets are coated with a composite solid electrolyte containing LATP powders, the resulting Li-metal battery displays high capacity at 5 C (with a capacity retention of 65.2% compared to the original capacity at 0.2 C) as well as superior cyclic stability and excellent Coulombic efficiency (> 99.5%, over 200 cycles). These results confirm that the composite solid electrolyte acts as a protective layer which have ability to prevent the growth of Li dendrites. Consequently, the fabricated electrolyte configuration can be engineered to enable high energy/power density and electrochemical stable cyclability in Li-metal batteries.
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1. Introduction

Liquid organic electrolyte (LOE) based lithium-ion batteries (LIBs) have gained a lot of attention since many years and utilized variety of applications owing to their outstanding combination of high-power density and energy. They are ideal for use in electric vehicles, portable electronic devices, and other industries [1,2]. However, LOE is a volatile and flammable electrolyte, which elevates major problems for LIBs development. The risk of thermal runaway and potential explosion or catastrophic fires associated with these electrolytes has severely impacted their progress [3,4]. Thus, solid-state LIBs are regarded as the most promising next-generation lithium batteries. Solid-state electrolytes are preferred over liquid electrolytes because they eliminate safety concerns and allow for higher energy density by using high-capacity electrodes like high-voltage cathodes, Li metal anodes, and conversion-type sulphur and oxygen electrodes [5,6,7,8]. Usually in solid state batteries, a separator was introduced to avoid direct contact between two electrodes, while enabling ion flow between them. The ion movements are the crucial for a battery performance, as it produces electrical energy. But, solid-state electrolytes act as a both separator and electrolyte. Like liquid electrolyte, separator can conduct ions as well as separate the electrolytes, which simplify the battery fabrication process. Additionally, separator can provide battery safety, stability, and credibility. Moreover, solid state electrolyte has no chance to leakage and short circuit during its uses, unlikely liquid electrolyte [9]. Therefore, solid state electrolyte is safer option to use in batteries as electrolyte. Overall, the use of solid-state electrolytes as both an electrolyte and a separator simplify the battery fabrication process, while improving its safety and reliability. This is an important development in the field of battery technology, as it can help to reduce the cost and complexity of manufacturing batteries while also improving their performance and safety.
Solid-state batteries must have solid-state electrolytes to achieve high electrochemical and mechanical stability. This electrolyte not only enhance the performance of the batteries but also provides high compatible interface between two electrodes. Therefore, selecting the appropriate type of solid electrolyte and developing the right composition are critical factors for the battery’s performance. The most essential component i.e., solid state electrolyte, can be broadly categorized into two types such as solid polymer electrolytes and inorganic (i.e., ceramics) electrolytes [10,11,12]. There are numerous studies of solid inorganic electrolyte such as Li1.5Al0.5Ti1.5(PO4)3 (LATP) and Li6.4La3Zr1.4Ta0.6O12 (LLZTO) owing to their wide electrochemical window, high conductivity i.e., ~10-4 S cm-1 at ambident temperature, and strong electrochemical stability [13,14]. However, its practical applications are hindered due to great interfacial resistance between brittle ceramic electrodes and electrolytes [15,16,17]. In contrary, polymer-based composite solid electrolytes (which are incorporate with Li salts and diverse functional fillers have garnered significant interest due to their favorable attributes for commercial applications. These include their ease of processing and flexibility [18,19,20,21]. However, poly(ethylene oxide) (PEO)-based composite solid electrolytes possessed low ionic conductivity (< 10-5 S cm-1) and the narrow electrochemical window (< 3.9 V) at ambident temperature, which hindered its practical uses [14,15]. Based on the above deduction, one strategy is to offer a synergistic effect on the novel design of “ceramic-in-polymer” or “polymer-in-ceramic” electrolytes that combines highly ionic conductive ceramics (e.g., LATP and LLZTO) and highly flexible and processible polymers (e.g., PEO), capable of offering a feasibility for high-performance solid-state Li-metal batteries [22,23]. Such a design can provide a feasible approach for developing high-performance solid-state Li-metal batteries. To enhance the electrochemical performance of solid state batteries, the development of solid composite electrolytes (i.e., "ceramic-in-polymer" or "polymer-in-ceramic" electrolytes) has been explored, such as PEO + LLZTO [24] and poly(vinylidene fluoride-co-hexafluoropropene) + LATP [12,25]. However, even though ionic conductivity has improved significantly in recent years, Li dendrites and the possibility of penetration through “ceramic-in-polymer” electrolytes can lead to short circuits in solid-state batteries, severely limiting their practical use.
The development of composite solid electrolytes has shown promise in enhancing the cyclic stability of solid-state batteries, which is important in the context of the issues experienced by solid-state batteries. However, issues such as Li dendrite formation and short circuits still hinder their practical applications. This study aims to address these issues and unlock the full potential of solid-state batteries as a reliable and sustainable energy storage solution. To achieve this goal, this work proposes depositing “ceramic-in-polymer” electrolytes on the cathode side to create conductive and stable interfaces, minimizing interfacial resistance and mechanical stress during extended cycling. Two types of composite solid electrolytes, PEO + LLZTO + LiTFSI and PEO + LATP + LiTFSI, are coated on the LiFePO4 (LFP) cathode to create high-performance Li-metal batteries. This research aids in the design of high-performance solid-state batteries by providing insight into the applicability of composite solid electrolytes for usage on both the LFP cathode and Li anode side. High energy/power density and stable cyclability could be achieved with these composite solid electrolytes because of their high compatibility with the cathode and anode and their ability to inhibit Li dendrite growth.

2. Experimental

2.1. Fabrication of composite solid electrolytes

In this work, poly(ethylene oxide) (PEO, formula: (-CH2CH2O-)n, molar mass = 3 × 105 g mol-1, melting point: 65 °C, Aladdin) and lithium bis(trifluoromethanesulfonyl)imide (LiTFSI, formula: LiC2NO4F6S2, molar mass: 287.1 g mol-1, Sigma-Aldrich, 99.95 %) were dried at 80 °C for 12 h under vacuum prior the fabrication of composite solid electrolytes. 1-methyl-2-pyrrolidone (NMP, Sinopharm) and acetonitrile (ACN, Aladdin) were used as received.
Two types of composite gel electrolytes were prepared using different ratios of PEO and LiTFSI in weight/weight (w/w). The first ratio was 2/1 (PEO/LiTFSI), and the second ratio was 3/1 (PEO/LiTFSI). The gel electrolytes were prepared by dissolving the PEO/LiTFSI mixtures in 15 mL of ACN under continuous stirring at 30 °C for 6 h. The resulting slurries were used for fabricating gel electrolytes supported by LFP cathode sheets. The samples with the PEO/LiTFSI ratio of 2/1 and 3/1 were denoted as PL21 and PL31, respectively. Subsequently, the PL slurries were mixed with 20 wt.% ceramic powders, namely, lithium aluminum titanium phosphate (LATP) and lithium lanthanum zirconium tantalum oxide (LLZTO), with stirring at 50 °C for 6 h to achieve a homogeneous electrolyte slurry. The samples mixed with LATP and LLZTO powders were labeled as PL31-LATP and PL31-LLZTO, respectively. Both slurries were then used for fabricating composite solid electrolytes supported by LFP cathode.

2.2. Fabrication of LFP-supported composite solid electrolytes

In order to produce the LFP cathode, olivine-type LFP powders (particle size around 500 nm) were combined with a polyvinylidene fluoride binder) (PVDF), and a conducting medium (Super-P, Taiwan Maxwave Co., Taiwan) in NMP solvent. The ratio of the above components was 90:7:3 (w/w/w), respectively, resulting for the formation of an LFP slurry. Then the slurry was mixed for 2 h using a 3D mixer with Zr balls to ensure uniformity. The aforementioned slurry was applied to Al foil using a doctor blade. The above produced LFP cathode sheets were dried overnight in a vacuum oven at 110 °C, compacted, and then cut into the proper form for battery assembly. The fabrication process for LFP-supported composite solid electrolytes involved four configurations (PL21, PL31, PL31-LATP, and PL31-LLZTO). The electrolyte slurries were deposited onto the LFP cathode, and the thickness of each composite layer was precisely controlled using a doctor blade. To maintain good adhesion, all samples were kept in a vacuum oven at 140 °C for overnight.

2.3. Materials and electrochemical characterization

The morphology of the LFP-supported composite solid electrolytes was investigated through field-emission scanning electron microscopy (FE-SEM, JEOL JSM-6700F). The X-ray diffraction (XRD) patterns of composite solid electrolytes were obtained using diffractometer (Brucker D2) equipped with a copper (Cu) target. To determine the maximum potential of each composite solid electrolyte in symmetric cells with Li metal, linear scanning voltammetry was employed. Electrochemical impedance spectroscopy (EIS) was used to evaluate the polarization of coin cells constructed with different LFP-supported composite electrolytes in the 100 kHz to 10 mHz frequency range. EIS measurement were done by utilizing a CH Instruments 608C instrument.
For electrochemical performance measurements of the LFP-supported composite solid electrolytes, coin cells (CR2032 type) were utilized. The fabricated LFP-supported composite electrolytes were inserted into the coin-cell kits, and Li-metal batteries were assembled within a glove box. The charge/discharge cycle tests used to evaluate the real-time performance of the LFP-supported composite electrolytes ranged from 0.2 to 5 C within the voltage range of 2.4-4.0 V at room temperature. The cyclic performance of Li-metal batteries was tested over 200 cycles at 0.2 C (charging) and 0.5 C (discharging).

3. Results and discussion

Figure 1 displays the FESEM images (Top- and cross-sectional) of the PL31-LATP and PL31-LLZTO electrolytes. The top-view images reveal a roughened surface consisting of numerous ceramic particles embedded in flexible PEO polymer. The cross-sectional views demonstrate that the composite solid electrolytes are tightly attached to the LFP cathode sheets, with a thickness of approximately 25‒30 μm for both solid electrolytes. There is no visible distinction observed at the interface between the composite solid electrolytes and the LFP cathode sheets, which are covered by a smooth coating of composite solid electrolytes. These findings led to the conclusion that the “ceramic-in-polymer” electrolytes are very cohesive and highly flexible.
The XRD patterns of PL31-LATP and PL31-LLZTO samples on LFP cathode sheets are displayed in Figure 2. The LFP sample exhibited various diffraction peaks which are well matched with the standard orthorhombic olivine phase of LFP (JCPDS Card No.: 83-2092: a = 10.334 Å, b = 6.010 Å, and c = 4.693 Å) [26], confirming highly crystalline in nature of the LFP powders [27]. The XRD patterns also show two diffractions peak at 19.2 and 23.6°, which can be assigned to the (120) and (112) crystalline planes of PEO crystals, respectively [28]. The weak diffraction peaks are attributed to the ceramics (i.e., LATP and LLZTO) inserted into the PEO network, which reduces the crystalline degree of PEO polymers [29]. The XRD pattern of LATP powder for the PL31-LATP sample matches the typical NASICON-type structure with rhombohedral lattice (Card No.: ICDD 00-035-0754). The XRD peaks are positioned at 24.5, 29.7, and 36.5°, which are corresponding to (104), (113), and (116), respectively [30,31]. However, the PL31-LLZTO sample's diffraction peaks closely correspond to the typical pattern of cubic-LLZTO (ICSD Card No.: 45-109), confirming the existence of a cubic phase LLZTO [32,33]. Overall, the XRD patterns of both PL31-LATP and PL31-LLZTO samples confirm the solid composite nature of the materials, consisting of olivine-type LFP, amorphous PEO, and crystalline ceramics (LATP and LLZTO crystals) without any impurity.
LSV is an important technique used to study the electrochemical behavior materials by sweeping the potential applied to an electrode or electrolyte at a constant rate. In the context of characterizing composite solid electrolytes, LSV was employed to determine the breakdown potential of each electrolyte sample. This was done by subjecting the electrolyte at a scan rate of 0.1 mV s-1, as illustrated Figure 3(a). The following experiment's LSV profiles demonstrated composite electrolytes' electrochemical stability. The results revealed that composite electrolytes possessed high breakdown potentials exceeding 4.25 V compared to the Li/Li+ reference electrode. This finding is crucial because it indicates that these solid electrolytes can withstand high potentials without undergoing significant degradation or decomposition. The tendency of solid electrolytes to maintain stability at high potentials implies that they may efficiently assist the operation of high-voltage cathodes, allowing the development of new energy storage systems with enhanced performance and energy density. Figure 3(b) and Figure 4(c) demonstrate the Nyquist plots of LFP-supported composite electrolytes before and after cycling test (50 cycles), respectively. Over the frequency range, Nyquist plots show one charge-transfer impedance depressed semicircle comprising the electrode/electrolyte contact across the frequency range [34]. Accordingly, one equivalent circuit model (see Figure 3(d)) can be proposed with the combination of components including R1 (the resistance of bulk electrolyte), R2 (the interfacial impedance of the electrolyte/electrode interface, i.e., the resistance of solid electrolyte interphase (SEI) layer)), R3 (the interfacial impedance of charge transfer resistance), and CPE (the constant phase elements for double layer capacitance) [35]. Z-view software was used to investigate the EIS spectra of LFP-supported composite solid electrolytes. The experimental impedance spectra and model predictions were within 10% throughout the frequency range. The equivalent series resistance (ESR = R1 + R2 + R3) could be calculated from Figure 4(a) to estimate the cells' total internal resistance [36]. Accordingly, before cycling, the ESR values of PL21, PL31, PL31-LATP, and PL31-LLZTO samples are found to be 726, 536, 141, and 162 Ω, respectively. After cycling, the ESR values are decreased to 199, 192, 87, and 113 Ω for PL21, PL31, PL31-LATP, and PL31-LLZTO samples, respectively. The reduced magnitude in ESR measurements when compared to before cycling may be ascribed to the formation of an ionically conductive electrolyte. This result reveals that the ESR value (i.e., the overall inner resistance) is significantly decreased by the robust design of composite solid electrolytes (i.e., PL31-LATP and PL31-LLZTO) as compared to gel electrolyte, attributed to the fact that the bulk electrolyte, interfacial electrolyte/electrode impedance, and charge-transfer is substantially alleviated. Overall, the analysis of Nyquist plots and ESR values provides valuable information regarding the internal resistance and electrochemical behavior of composite solid electrolytes, which is critical for designing high-performance energy storage devices. Further, ionic conductivity (σ) was evaluated using EIS plots using this formula σ = l / (R1 A), where ‘l’ is the thickness of the film in the electrolyte, and ‘A’ is the projected active area [37,38]. The σ values follows the following order: PL31-LATP (2.08 × 10-4 S cm-1) > PL31-LLZTO (1.64 × 10-4 S cm-1) > PL31 (8.58 × 10-5 S cm-1) > PL21 (5.10 × 10-5 S cm-1) and are presented in Figure 4(b). The PL31-LATP and PL31-LLZTO samples have better ionic conductivities than the PL21 and PL31 samples owing to the formation of a 3D ionic conductive network structure. PEO polymer matrixes and ceramic particles construct this 3D network. Solid electrolytes for Li-metal batteries provide the aforesaid high ionic conductivity. The crystalline degree of PEO polymers reduce due to introduction of moderate amounts of LATP and LLZTO fillers. The ionic segmental motion is enhanced due to reduction of crystalline in composite electrolytes. This enhanced segmental motion promotes ion mobility inside the composite electrolyte, resulting in greater ionic conductivity. Moreover, percolation behavior phenomenon was observed at the interface between LATP/LLZTO particles and PEO polymer matrix [39,40]. This percolation behavior further enhances the movement of Li+ ions, facilitating faster ionic conduction and contributing to enhanced ionic conductivity [41,42]. Accordingly, the quantification of ionic conductivity using EIS analysis reveals that the design of composite solid electrolytes, particularly those incorporating LATP and LLZTO fillers, significantly enhances the ionic conductivity in Li-metal batteries. The 3D ionic conductive network formed within the composite electrolyte, along with the reduced crystalline degree of the polymer and percolation behavior at the interface, collectively contribute to the improved ionic conductivity and have the potential for developing high-performance energy storage technology.
To evaluate the high-rate capability, galvanostatic charge-discharge profiles of solid electrolytes were recorded, which is equipped with Li-metal batteries and presented in Figures 5(a)‒5(d). The Li-metal batteries were cycled through voltages of 2.4 to 4.0 V (vs. Li/Li+) at charge and discharge rates of 0.2, 0.5, 1, 2, and 5 C. At 0.2 C, all batteries showed a distinct flat plateau, suggesting a two-phase reversible process: LiFePO4 ↔ (1−x)LiFePO4 + xFePO4 + xLi+ + xe−. The estimated specific capacity for this reaction is around 170 mAh g-1, and measured at Ca. 3.2−3.6 V vs. Li/Li+ [43]. All battery discharge capacities attained approximately 160 mAh g-1, which is close to the estimated capacity. Furthermore, symmetry was observed in the 0.2 C charge/discharge curves, indicating Li ions in the olivine-type LFP crystals.
Electrode polarization (represented by the potential difference between charging and discharging plateaus, ΔE) was significantly influenced by the electrolyte type, particularly at high-rate capacities such as 2 C and 5 C. With higher C rates, the ΔE increased due to the apparent polarization resulting from ionic diffusion and charge transfer resistance in the Li-metal batteries. As shown by the discharge capacity vs C rate plot, the Li-metal battery fabricated using the PL31-LATP electrolyte displayed improved rate capability across the entire 0.2-5 C rate range (see Figure 6(a)). The capacity retentions were 96.2 % (0.5 C), 83.9 % (1 C), 75.8 % (2 C), and 65.2 % (5 C) compared to the discharge capacity at 0.2 C, confirming its high-rate capabilities. After the rate capability test, all Li-metal batteries recovered to their original capacity at 0.2 C, indicating excellent Li+ reversibility through the robust design of the hierarchical composite solid layer, even after high-rate cycling experiments. In contrast, both PL21 and PL31 samples displayed poor high-rate capability at 5 C, indicating significant electrode polarization. The enhanced rate capacity compared to the PL31-LATP sample underlined the relevance of LATP fillers in the construction of composite solid electrolytes.
Figures 6(b)‒6(d) demonstrate galvanostatic cycles of Li symmetric cells using several solid-state electrolytes (PL31, PL31-LATP, and PL31-LLZTO samples) at a current density of 0.2 mA cm-2 to evaluate the durability. This analysis was done evaluating the electrochemical stability of the composite electrolytes in the presence of Li metal. The whole galvanostatic cycling analysis was done at ambient temperature. According to the findings, Li symmetric cells equipped with composite electrolytes that contained soft PEO electrolytes without LLZTO fillers (PL31) displayed unstable Li plating/stripping cycling for about 60 h before incurring a short circuit. Notably, the Li-dendrite-suppression capability of the composite electrolyte gradually improved with the incorporation of LATP and LLZTO fillers. Particularly noteworthy, the Li symmetric cells fabricated with PL31-LATP and PL31-LLZTO electrolytes demonstrated stable cycling without short circuits for 60 h. These results suggest the potential of these batteries for enhanced safety and improved electrochemical stability in Li metal. This enhancement is due to the high amount of LLZTO ceramic, which has a shear modulus of up to 55 GPa, significantly more than the minimal value (8.5 GPa), necessary to inhibit Li dendrite growth [44]. As per the previous finding, LATP powders modulus of elasticity and hardness values are vary from 107–150 GPa and 5.5–10.0 GPa, respectively [45]. Therefore, it is necessary to introduce highly conductive ceramics as fillers into composite electrolytes in order to increase the mechanical strength, which acts as a physical barrier to suppress Li dendrites [46].
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Figure 6. (a) Variation of discharge capacity with C rate for different Li-metal batteries, and galvanostatic cycles of Li symmetric cells using different solid electrolytes: (b) PL31, (c) PL31-LATP, and (d) PL31-LLZTP at 0.2 mA cm-2.
Figure 6. (a) Variation of discharge capacity with C rate for different Li-metal batteries, and galvanostatic cycles of Li symmetric cells using different solid electrolytes: (b) PL31, (c) PL31-LATP, and (d) PL31-LLZTP at 0.2 mA cm-2.
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The typical charge-discharge curves of Li-metal batteries fabricated with LFP-supported solid-state electrolytes (PL31-LATP and PL31-LLZTO) are presented in Figures 7(a) and 7(b). Charge/discharge analysis of the Li-metal batteries was conducted under ambient temperature with potential window 2.4–4.0 V vs. Li/Li+. The batteries were charged at rate of 0.2 C and discharged at a rate of 0.5 C. Significantly, both Li-metal batteries exhibit a stable reversible capacity spanning from 153 to 160 mAh g-1 after 200 cycles, which represents over 90 % energy storage within the olivine LFP lattices. In addition, the charge/discharge curves exhibit symmetry at 0.2 C/0.5 C, indicating that Li+ intercalation and de-intercalation are reversible. Figures 7(c) and 7(d) display the capacity retention and Coulombic efficiency as a function of cycle number for both Li-metal batteries fabricated with LFP-supported solid-state electrolytes in order to evaluate their cyclic performance. Coulombic efficiency and capacity retention are commonly electrochemical parameters of an energy device, which are used to assess the cyclic stability of composite solid electrolytes during charge/discharge cycling. Remarkably, after 200 cycles, both Li-metal batteries demonstrate superior cyclic performance with excellent Coulombic efficiency (> 99.5%). This satisfactory result confirms that the composite solid electrolyte consisting of PEO, ceramics (LATP and LLZTO), and LiTFSI offers a protective layer against Li dendrite growth. Consequently, it induces desirable cyclic stability and superior rate capability, ensuring the long-term performance of the batteries.
To facilitate the practical applications, a pouch cell was assembled using an LFP-supported dual composite solid electrolyte (PL31-LATP) and a graphite anode, as shown in the inset of Figure 7(c). The digital photograph image demonstrates that the pouch cell successfully powers a light-emitting diode. The pouch cell configuration, comprising LFP cathodes, graphite anodes, and composite solid electrolytes with a thickness around 30 μm, achieves an energy density of around 116 Wh kg-1. Energy density, cyclic stability, and high-rate capacity are all significantly increased thanks to the cathode-supported hierarchical electrolyte's architecture. An improved ionic conductivity and lower interfacial electrolyte/electrode resistance are the results of this ideal design for composite solid electrolytes. This provides a potentially useful approach to improving energy density, cycle stability, and rate capability in real-world battery applications.
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Figure 7. Typical charge-discharge curves of different Li-metal batteries using (a) PL31-LATP and (b) PL31-LLZTO electrolytes at 0.2 C (charging) and 0.5 C (discharging). Cyclic performance of different Li-metal batteries using (c) PL31-LATP and (d) PL31-LLZTO electrolytes at 0.2 C (charging) and 0.5 C (discharging). The inset shows the photographs of Li-metal batteries using PL31-LATP electrolytes reaching to ca. 3.51 V) and light-emitting diode lighted on by the solid-state battery.
Figure 7. Typical charge-discharge curves of different Li-metal batteries using (a) PL31-LATP and (b) PL31-LLZTO electrolytes at 0.2 C (charging) and 0.5 C (discharging). Cyclic performance of different Li-metal batteries using (c) PL31-LATP and (d) PL31-LLZTO electrolytes at 0.2 C (charging) and 0.5 C (discharging). The inset shows the photographs of Li-metal batteries using PL31-LATP electrolytes reaching to ca. 3.51 V) and light-emitting diode lighted on by the solid-state battery.
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4. Conclusions

This research illustrates the efficacy of a strong composite solid electrolyte design for high-performance Li-metal batteries using LFP cathode sheets, soft polymer (PEO), and Li salt (LiTFSI). The designed solid electrolytes showed superior electrochemical stability above 4.25 V vs. Li/Li+. The ESR value exhibits a noteworthy reduction as compare to gel electrolytes, owing to the resilient architecture of composite solid electrolytes containing LATP and LLZTO fillers. The observed reduction can be ascribed to the mitigation of bulk electrolyte, charge-transfer, and interfacial electrolyte/electrode impedance. Based on the analysis of EIS measurements, the ionic conductivities of PL31-LATP and PL31-LLZTO electrolytes reach high values of 2.08 × 10-4 and 1.64 × 10-4 S cm-1, respectively, at ambient temperature. The Li-metal battery equipped with LFP-supported PL31-LATP electrolyte exhibits not only high-rate capability at 5 C (with a capacity retention of 65.2 % compared to the original capacity at 0.2 C), but also superior cyclic stability with excellent Coulombic efficiency (> 99.5%) over 200 cycles. These results confirm that the fabricated composite solid electrolyte, composed of PEO, ceramics (LATP and LLZTO), and LiTFSI, acts as a protective layer against the growth of Li dendrites during extended cycling tests, leading to enhanced cyclic stability and desirable rate capability. The composite solid electrolytes developed in this study offer a promising solution for the design of high-performance solid-state electrolytes utilizing LATP ceramic particles.

CRediT authorship contribution statement

Kang-Feng Chang: Data curation, Methodology, Visualization, Investigation Chien-Te Hsieh: Methodology, Validation, Funding acquisition, Supervision, Writing - original draft, Writing - review & editing. Pradeep Kumar Panda: Validation, Writing - review & editing. Po-Chih Yang: Validation, Writing - original draft, Writing - review & editing. Navish Kataria: Data curation, Inspection. Kuan Shiong Khoo: Methodology, Validation, Writing - review & editing.

Acknowledgements

The authors gratefully acknowledge the support of the Ministry of Science and Technology in Taiwan, provided through grant numbers NSTC 112-2221-E-155-005-MY3. Additionally, the authors express their appreciation for the equipment support received from Gold Carbon Inc. (Taoyuan, Taiwan).

Declaration of competing interest

The authors declare that they have no known competing financial interests or personal relationships that could have appeared to influence the work reported in this paper.

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Figure 1. Top and cross-sectional views of FE-SEM images: (a, b) PL31-LATP and (c, d) PL31-LLZTO sample on LFP cathode sheets.
Figure 1. Top and cross-sectional views of FE-SEM images: (a, b) PL31-LATP and (c, d) PL31-LLZTO sample on LFP cathode sheets.
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Figure 2. Typical XRD patterns of (a) PL31-LATP and (b) PL31-LLZTO sample on LFP cathode sheets.
Figure 2. Typical XRD patterns of (a) PL31-LATP and (b) PL31-LLZTO sample on LFP cathode sheets.
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Figure 3. (a) LSV curves of different SSE samples, Nyquist plots of symmetric cells using different SSE samples (b) before and (c) after cycling test, and (d) the proposed equivalent circuit, consisting of electrolyte resistance, interfacial resistance, charge-transfer resistance, and two constant phase elements.
Figure 3. (a) LSV curves of different SSE samples, Nyquist plots of symmetric cells using different SSE samples (b) before and (c) after cycling test, and (d) the proposed equivalent circuit, consisting of electrolyte resistance, interfacial resistance, charge-transfer resistance, and two constant phase elements.
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Figure 4. (a) ESR and (b) ionic conductivity as function of Typical XRD patterns of (a) PL31-LATP and (b) PL31-LLZTO sample on LFP cathode sheets.
Figure 4. (a) ESR and (b) ionic conductivity as function of Typical XRD patterns of (a) PL31-LATP and (b) PL31-LLZTO sample on LFP cathode sheets.
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Figure 5. Typical charge-discharge curves of Li-metal batteries equipped with (a) PL21, (b) PL31, (c) PL31-LATP, and (d) PL31-LLZTO electrolytes at various rates.
Figure 5. Typical charge-discharge curves of Li-metal batteries equipped with (a) PL21, (b) PL31, (c) PL31-LATP, and (d) PL31-LLZTO electrolytes at various rates.
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