In-Situ Plasticized LLZTO-PVDF Composite Electrolytes for High-Performance Solid-State Lithium Metal Batteries

Abstract

Solid polymer electrolytes (SPEs) are seen as the key component in the development of solid-state lithium batteries (SSLBs) by virtue of their good processability and flexibility. However, poor mechanical strength, low room-temperature lithium-ion (Li-ion) conductivity and unsatisfactory interfacial compatibility with electrodes limit their practical application. In this work, a composite electrolyte consisting of polyvinylidene fluoride and polyvinylidene carbonate with a Li_6.4La₃Zr_1.4Ta_0.6O₁₂(LLZTO) active filler (PFPC: LLZTO-SPE) is reported to achieve excellent ionic conductivity (4.25 × 10⁻⁴ S cm⁻¹ at 30 °C), a wide electrochemical window (>4.6 V), a high Li-ion transference number (t_Li⁺ = 0.49) and good interfacial compatibility with the electrode. Incorporating LLZTO as an active filler not only increases the ionic conductivity of the electrolyte, but also homogenizes Li-ion flux and stabilizes the electrode/electrolyte interface, thereby preventing lithium dendrites from piercing the electrolyte. As a result, Li/Li symmetrical cells using PFPC: LLZTO-SPEs deliver more than 800 h of cyclability at 0.1 mA cm⁻² and a high critical current density (CCD) of 2.6 mA cm⁻². The assembled Li/PFPC: LLZTO/LFP SSLBs achieve 87% capacity retention after 150 cycles at 0.2 C and 89% capacity retention for 100 cycles at 0.5 C. This work inspires new insights into designing high-performance SPEs.

1. Introduction

Lithium batteries show great application prospects in the field of energy storage due to their high energy density and low self-discharge rate [1,2]. At present, commercial Li-ion batteries based on volatile and flammable liquid electrolytes are gradually unable to fulfill the requirements of high energy density and high safety [3,4]. Solid-state lithium batteries (SSLBs) based on nonflammable solid-state electrolytes (SSEs), as the most promising choice of next-generation lithium batteries, have attracted extensive attention [5,6,7]. In addition, SSEs generally possess excellent electrochemical stability and can be used with high-voltage cathodes to produce high-energy-density batteries.

Common SSEs are mainly divided into inorganic solid electrolytes and organic solid polymer electrolytes. The inorganic SSEs possess the advantage of high room-temperature Li-ion conductivity and high mechanical strength, but significant hardness and brittleness induce large interfacial resistance with electrodes, which limits their practical applications [8,9,10]. Solid polymer electrolytes (SPEs) show high flexibility and good interfacial contact with electrodes, but relatively low room-temperature Li-ion conductivity makes them fail to meet the demand of high-energy-density lithium batteries [11,12,13]. Inorganic solid electrolyte powders such as Li₇La₃Zr₂O₁₂ (LLZO), Li_0.33La_0.56TiO_3−x (LLTO) and Li_1.4Al_0.4Ti_1.6(PO₄)₃ (LATP) are introduced as active fillers, while the segmental motion of polymer chains is promoted by reducing the crystallinity of polymers through the interaction between the polymer and the inorganic material surface electrolyte. Thus, the resistance to Li dendrites is enhanced, and the conductivity of Li ions and the mechanical properties of the electrolyte are improved [14,15,16,17]. In addition, some functional groups can help dissociate lithium salts based on Lewis acid-base interactions and increase Li-ion transfer. Up to now, significant efforts have been devoted to developing composite electrolytes composed of a polyethylene oxide (PEO) matrix and nano-sized inorganic solid electrolyte filler to achieve improved overall performance, and certain progress has been made [18]. However, the PEO matrix can be oxidized and decomposed at about 4 V (vs. Li/Li⁺), which restricts the application of PEO-based composite electrolytes in high-voltage scenarios [19]. Compared with PEO, poly(vinylidene fluoride) (PVDF) shows a wide electrochemical window to match high-voltage cathodes [20,21,22]. However, PVDF-based SPE film consists of a large number of micro-sized spherical particles due to solvent evaporation, thus creating voids inside the electrolyte film. These internal voids reduce the mechanical strength of the electrolyte and induce the uneven internal transport of Li ions, leading to lithium dendrite growth and puncturing of the electrolyte film [23]. Moreover, the presence of solvent molecules in the free state in the PVDF-based SPEs will result in interfacial deterioration due to side reactions with lithium metal [24]. Although high-temperature drying can remove the residual solvent and reduce the gap between PVDF polymer particles, it will also damage the structure of solvated Li ions, resulting in a sharp decrease in Li-ion conductivity [23,25]. In situ polymerization is an effective way to solve the existing problems of PVDF-based SPEs, such as low conductivity and interfacial instability [26,27,28]. First, the liquid polymerization precursor can penetrate between the electrode and the PVDF-based SPE, which effectively improves the solid-solid interfacial contact. In addition, an electrolyte constructed via in situ polymerization is relatively dense, which can produce uniform and dense ion transport paths [29,30,31]. In recent years, electrolytes based on in-situ solidification of vinylene carbonate (VC) monomers have been widely utilized [32]. For instance, Cui et al. designed a PVCA SPE supported by a cellulose matrix, which obtained an ionic conductivity of 9.82 × 10⁻⁵ S cm⁻¹ at 50 °C [33]. Chen et al. reported a PVC-based SPE via in situ polymerization, achieving a superior ionic conductivity of 1.2 × 10⁻⁴ S cm⁻¹ at 25 ℃ and good interfacial compatibility with electrodes [34]. However, the Li-ion transport in in-situ-polymerized pure PVC electrolytes relies on chain segments with a low degree of polymerization, which leads to unsatisfactory lithium dendrite resistance and a low Li-ion transference number. Moreover, inert supports such as glass fibers and polyolefins are unable to participate in Li-ion transport, resulting in a non-uniform distribution of Li-ion flux in the composite electrolytes [30,35,36]. Using a PVDF inorganic filler composite electrolyte as the substrate and incorporating an in-situ-polymerized PVC electrolyte is an effective but rarely reported method to solve the above problems and obtain a high-performance composite electrolyte [37,38,39].

Herein, we designed a composite solid polymer electrolyte with a PVDF/LLZTO composite electrolyte as the active substrate and PVC/LLZTO as the in-situ plasticizer to achieve superior comprehensive performance. In this design, the LLZTO particles as active fillers compounded with PVDF construct organic-inorganic interfaces to obtain rich ion transport paths, so that the PVDF polymer substrates effectively participate in Li-ion transport. Meanwhile, the LLZTO particle compounded with an in-situ-polymerized PVC electrolyte not only promotes the movement of polymer chains to improve Li-ion conductivity, but the electrochemical potential difference between the PVC and LLZTO also causes the migration of Li ions in the LLZTO lattice from the surface of LLZTO to the PVC, resulting in the formation of abundant lithium vacancies for rapid Li-ion transport. The LLZTO filler provides abundant Lewis’s acid sites to adsorb anionic groups in the electrolyte, thereby increasing the Li-ion transference number. The resulting PVDF/PVC/LLZTO solid polymer electrolyte (PFPC: LLZTO-SPE) achieves a high Li-ion conductivity of 5.0 × 10⁻⁴ S cm⁻¹ at room temperature, a broad electrochemical window of more than 4.6 V and a high Li-ion transference number of ~0.5. Moreover, the introduction of LLZTO ceramic additives effectively improves the comprehensive mechanical properties of the composite electrolyte, thereby inhibiting the penetration of lithium dendrites. As a result, the Li/Li symmetrical cells assembled with the PFPC: LLZTO-SPEs exhibit stable cycling for more than 800 h at 0.1 mA cm⁻² and a high critical current density (CCD) of 2.6 mA cm⁻². The Li/LFP cells show stable cycling performance (capacity retention of more than 87% at 0.2 C for 150 cycles) and excellent rate capability (specific capacity of 103 mAh g⁻¹ at 2.0 C). This work explores the application of active fillers in composite electrolytes, which is an important guidance for large-scale synthesis of high-performance solid lithium batteries.

2. Materials and Methods

2.1. Materials for Experiment

Lithium difluoroxalate (LiDFOB, 99%, Aladdin, Shanghai, China), vinylene carbonate (VC, 98%, Aladdin), azodiisobutyronitrile (AIBN, 98%, Aladdin), LiOH∙H₂O (99%, Aladdin), La(OH)₃ (99.99%, Aladdin), ZrO₂ (99.99%, Aladdin), Ta₂O₅ (99.99%, Aladdin), N-Methylpyrrolidone (NMP, 99.5%, Aladdin) and N,N-Dimethylformamide (DMF, 99.5%, Aladdin) were purchased and used without further purification. Polyvinylidene fluoride (PVDF, M_W = 500,000, Suweil 5130), lithium iron phosphate (LFP, Betri, Lyon, France), lithium metal foils and Super P carbon black were supplied by MTI Corporation.

2.2. Preparation of Electrolyte Support System

Based on previous work, the Li_6.4La₃Zr_1.4Ta_0.6O₁₂ (LLZTO) electrolyte powders were synthesized using the solid phase method. [27,40] The average particle size of the LLZTO obtained was about 500 nm. The preparation of electrolytes was carried out in an ultra-dry chamber with a dew point of −60 °C. Firstly, 0.12 g of LLZTO particles were dispersed in 8 mL DMF, which was evenly dispersed in DMF after ultrasonic and stirring. Then, 1 g of PVDF and 0.5 g of LiDFOB were dissolved in an LLZTO/DMF dispersion solution and stirred for 12 h to get a uniform slurry. Finally, the slurry was coated onto the glass plate using the solution pouring method, put in the vacuum oven and dried at 80 °C for 24 h to get a PVDF/LiDFOB/LLZTO SPE substrate. For comparison, the PVDF/LiDFOB SPE substrate without LLZTO was prepared using the same method.

2.3. Preparation of Polymerization Precursors

Firstly, different amounts (1, 3, or 5 wt%) of LLZTO were added to 1 mL VC solution, and the LLZTO powder was dispersed evenly under ultrasonic and stirring. Then, 0.144 g of LiDFOB and 0.005 g of AIBN were added and stirred for 1 h to obtain the polymeric precursor solution. In comparison, a VC polymeric precursor solution without LLZTO powder was also prepared. The precursor solution was added to the PVDF:LLZTO SPEs. These SPE membranes after polymerization were referred to as PFPC: 1 wt% LLZTO, PFPC: 3 wt% LLZTO and PFPC: 5 wt% LLZTO, respectively.

2.4. Preparation of Batteries

A lithium symmetrical CR 2032 battery was assembled through dropping 10 μL precursor solution on both sides of a 19 mm diameter SPE membrane support and a lithium foil. For a full battery, lithium iron phosphate was chosen as the positive terminal. The LFP positive electrode was prepared via solution casting. 80 wt% LFP, 10 wt% Super-P and 10 wt% polyvinylidene fluoride (PVDF) were added to the NMP and stirred for 12 h to achieve a uniform slurry. The mass loading of the LFP was 5 ± 0.2 mg cm⁻². Further drying at 80 °C for 12 h was conducted. Lithium metal was used as the negative electrode. The prepared cell was heated in the oven at 60 °C for 24 h to complete the polymerization of the VC. All cells were assembled in a glove box filled with argon gas. Other electrochemical testing cells use the same method to replace the electrodes with stainless steel or lithium metal.

2.5. Electrochemical Test

SS/electrolyte/SS cells were assembled using stainless steel plates as blocking electrodes. Electrochemical impedance spectroscopy (EIS) was tested using an electrochemical workstation (Princeton, NJ, USA). The test frequency was 1 MHz~0.1 Hz, and the temperature range was 30~60 °C. The calculation formula for ionic conductivity is:

$$\sigma =\frac{L}{R·S}$$

(1)

where L is the thickness of electrolyte film, R is the EIS measurement result of the SS/ electrolyte/SS cell, and S is the area of the SS electrode.

The transfer number of Li ions (t_Li⁺) was measured using the DC polarization method of a Li/Li symmetrical cell with voltage polarization of 10 mV. t_Li⁺ is calculated according to the formula:

$$t_{{Li}^{+}}=\frac{I_s(∆V-I_i{R}_i)}{I_i(∆V-I_s{R}_s)}$$

(2)

where I_s and R_s represent the current and resistance of the Li/Li symmetric cell at the steady state, I_i and R_i represent the current and resistance of the Li/Li symmetric cell at the initial state and ∆V represents the voltage polarization applied. An SS/electrolyte/Li cell was assembled using a stainless steel sheet as the working electrode and lithium metal as the reference electrode. Electrochemical stability was tested via linear sweep voltammetry (LSV) using a Li/electrolyte/SS cell from 0 to 6 V.

2.6. Materials Characterization

The crystal structure of LLZTO was analyzed via X-ray diffraction (XRD) (Bruker D2 phaser, Cu Kα radiates in the 2θ range of 10~80° and a step size of 0.1°). The morphology of the electrolyte was measured using emission scanning electron microscopy (SEM) (FESU4800, Hitachi, Tokyo, Japan). Fourier transform infrared spectroscopy was performed using the Spectra Tech Collector II attachment in diffuse reflection mode with the Bruker Vertex V70 spectrometer. A gel permeation chromatography (GPC) investigation was performed using a Waters 1515 HPLC with three Styragel columns (HT3, HT4 and HT5) and 2414 differential refractive index detector. The eluant was Tetrahydrofuran (1 mL min⁻¹). Polystyrene standards were employed for the GPC calibration curve.

3. Results

3.1. Preparation and Physical Characterization of Electrolytes

Figure 1a shows the schematic preparation process of PFPC-based SPEs. Typically, a homogeneous precursor consisting of VC, LLZTO, lithium salt (LiDFOB) and azobisisobutyronitrile (AIBN) was dropped onto the PVDF-based polymer film, followed by heating at 60 °C to trigger the polymerization of the VC monomer and thus obtain the integrated composite solid polymer electrolyte (denoted as PFPC: LLZTO SPE). The PVDF/PVC solid polymer electrolyte (PFPC SPE) was synthesized for contrast using the same method, except that no LLZTO powder was added during the preparation process. As shown in Figure 1b, both VC and VC-LLZTO are in a liquid state in the initial stage, but are polymerized into a solid state after being heated at 60 °C. The results of the Fourier transform infrared (FTIR) spectroscopy (Figure 1c and Figure S1) show that the intensity of the absorption peaks located at about 3160 and 1560 cm⁻¹, corresponding to the C=C-H and C=C bonds, in the PVC and PVC: 3 wt% LLZTO is significantly weaker than that of the VC and VC: 3 wt% LLZTO, which indicates the successful polymerization of the VC monomers. The results of the gel permeation chromatography (GPC) test show the average molecular weight (Mn = 178,949) and the average molar mass (Mw = 405,818) of the PVC after polymerization, which further indicate that the PVC had a high degree of polymerization (Figure S2).

The particle size of fillers has a great influence on the performance of composite electrolytes [18,40]. The nanoscale inorganic fillers in the composite electrolyte build fast ion transport paths, and the larger the specific surface area of the particles, the stronger the interaction between the polymer-free matrix or lithium salt and the more interfaces for ion migration, thus improving the Li-ion conductivity of the electrolyte. Nanoscale inorganic fillers in composite electrolytes build increased interfaces with fast ion transport paths, which improve the Li-ion conductivity of electrolytes [41,42]. The size distribution test (Figure 2a) shows that the D₁₀, D₅₀ and D₉₀ sizes of LLZTO fillers are 0.166 μm, 0.518 μm and 1.106 μm, respectively. The scanning electron microscope (SEM) measurements presented in Figure 2b and Figure S3 further demonstrate that the LLZTO particles are evenly dispersed, with the diameter concentrating at approximately 500 nm. The X-ray diffraction (XRD) pattern indicates that the LLZTO fillers present a cubic-phase structure with high ionic conductivity. The XRD pattern of the PFPC SPE obtained via in situ polymerization is similar to that of the pure PVDF (PF) film, and no characteristic peaks corresponding to lithium salts can be observed, indicating that the lithium salts are fully dissociated in the SPEs. Moreover, the characteristic peaks of LLZTO appear in the XRD pattern of the PFPC: 3 wt% LLZTO, indicating the successful introduction of the LLZTO fillers into the SPEs (Figure 2c). As shown in Figure S4, the PVDF SPEs without LLZTO have more voids than PVDF: LLZTO SPEs. It can be observed in Figure 2d,e that compared to the loose structure of PVDF: LLZTO SPEs, the pores of PFPC: LLZTO SPEs are filled by the in-situ-polymerized PVC: LLZTO to form a continuous texture. The loose structure limits the improvement of ionic conductivity and interface compatibility, and the compact structure is expected to solve these problems. Figure S5 shows that the PVDF: LLZTO SPE film exhibits excellent flexibility, which enables it to be folded at any angle. This property remains unchanged after in situ polymerization to form the PFPC: 3 wt% LLZTO SPE (as shown in Figure 2f). Figure 2g and Figure S6 show that the thickness of the PFPC: 3 wt% LLZTO SPE is ~50 µm and the EDS mapping shows the uniform distribution of C, F, O and Zr elements, indicating the LLZTO and LiDFOB are uniformly distributed in the PFPC: 3 wt% LLZTO SPE. These excellent structural properties of the composite electrolyte lay the foundation for the improvement of electrochemical performance.

3.2. Electrochemical Performance of Electrolytes

Using stainless steel sheets as blocking electrodes to assemble symmetrical cells, an electrochemical impedance spectroscopy (EIS) test was carried out through the electrochemical workstation. Based on the EIS spectra in Figure 3a, the resistance value of PFPC: 3 wt% LLZTO SPE is 6.16 Ω at 30 °C and the unit area resistance is 3.22 Ω cm⁻². The Li-ion conductivity can be calculated to be 4.25 × 10⁻⁴ S cm⁻¹ via referring to Formula 1. As shown in Figure 3b, the Li-ion conductivity of the PFPC SPE without LLZTO is 1.82 × 10⁻⁴ S cm⁻¹ at 30 °C and can be significantly improved via adding an LLZTO active filler, among which the PFPC: 3 wt% LLZTO SPE shows the highest Li-ion conductivity of 4.25 × 10⁻⁴ S cm⁻¹. This is attributed to the fact that PVC with LLZTO fills the internal pores of PVDF and forms a new fast ion transport channel at the interface between PVC and LLZTO after the addition of LLZTO fillers. The inherent polarity of PVDF is weak, which results in its poor ability to dissociate lithium salts. As a result, a pure PVDF−lithium salt system is unable to conduct Li ions. In PVDF-based SPEs, lithium ions are transported through the interactions between the [solvent-Li⁺] complex (solvated Li ion) and the polymer [22,43]. When LLZTO is introduced into the PVDF-based SPE, a new interface is formed between PVDF and LLZTO, which enables fast transport of solvated Li ions. For the PVC: LLZTO SPEs, the electrochemical potential difference between the PVC and LLZTO causes the migration of Li ions in the LLZTO lattice from the surface of the LLZTO to the PVC, resulting in the formation of a large number of lithium vacancies for rapid lithium-ion transport [18,44]. However, high LLZTO content may lead to particle agglomeration and hinder ion transport, resulting in reduced ionic conductivity. PFPC: 3 wt% LLZTO SPE was used in the subsequent tests. The ionic transference in the electrolyte was divided into cation (Li⁺ in this case) and anion (DFOB^- in this case) transference, where the effective ionic transference is the transference of Li ions. A high Li-ion transference number is beneficial for improving the effective Li-ion conductivity of the electrolyte. The Li-ion transference number (t_Li⁺) of the PFPC: 3 wt% LLZTO calculated from the Bruce-Vincent-Evans equation is 0.49 (Figure 3d), higher than that of the PFPC (t_Li⁺ = 0.16, Figure 3c), which is due to the introduction of LLZTO [16]. The LLZTO filler dissociates lithium salts through using Lewis acid-base interaction on the surface, adsorbs the anion group and improves the efficiency of Li-ion transport at the same time. Linear scanning voltammetry (LSV) was used to test the electrochemical stability of the electrolyte. As shown in Figure S7, the PFPC SPE starts oxidative decomposition at 3.0 V, which can be attributed to the oxidation of the unpolymerized VC [45]. The electrochemical window was raised to 4.6 V after the introduction of LLZTO particles in PVDF and PVC. After adding LLZTO nanoparticles, the internal specific surface area of the electrolyte increased, leading to a uniform electric field [21]. A uniform electric field can increase the stability of the composite electrolyte under high voltage. This result indicates that the PFPC: 3 wt% LLZTO SPE possesses the capability to match the high-voltage cathode.

3.3. Stability against Electrolytes for Lithium Metal

The stability of the Li/electrolyte interface is the key to an SSLB’s cycle performance. The Li/electrolyte interface was evaluated through assembling Li/Li symmetrical cells. As shown in Figure 4a, the polarization voltage of the PFPC: 3 wt% LLZTO SPE is significantly lower than that of the PFPC SPE at the same current density. The Li/PFPC: 3 wt% LLZTO/Li symmetrical cell cycles stably for 800 h at 30 °C under 0.1 mA cm⁻², while the Li/PFPC/Li symmetrical cell short-circuits after only 100 h. The interface resistance can directly reflect the interface stability. The EIS of the Li/Li symmetric cells before and after cycling is shown in Figure 4b,c. The semicircle can be simulated via the inset model circuit in Figure 4b,c. Both spectra consist of a tiny semicircle which can be ascribed to the overall resistance of the electrolyte (bulk resistance) at high frequencies (R1), and a large semicircle which can be resolved to the interface resistance between lithium metal and the electrolyte film (R2) as well as the interface resistance between the internal components (PVDF substrate and the PVC: LLZTO) of the electrolyte (R3) [46,47]. After 100 cycles, the initial interface resistance of the Li/PFPC/Li cell is 263 Ω (337 Ω cm⁻²), which is impossible to measure using a reasonable EIS, indicating that a short circuit occurs in the Li/PFPC/Li cell. By contrast, the interface resistance of the Li/PFPC: 3 wt% LLZTO/Li cell only increases from 127 Ω (163 Ω cm⁻²) to 194 Ω (248 Ω cm⁻²) after 100 cycles. During the initial stages of cycling, the increase in impedance can be attributed to the formation of an SEI at the interface between the lithium metal and the electrolyte. After long-term cycling, the increase in impedance is caused by the interfacial side reaction between the polymer components in the electrolyte and the lithium metal electrodes. This indicates that the introduction of LLZTO improves the stability of the electrolyte against lithium metal. The Li/PFPC: 3 wt% LLZTO/Li cell cycles stably for more than 600 h when the current density is increased to 0.2 mA cm⁻² (Figure 4d). Figure 4e shows the rate performance of symmetric cells at various current densities. The Li/PFPC/Li cell suffers a short circuit at 1.6 mA cm⁻². This is due to the rapid growth of lithium dendrites under high current density, which results in the short circuit of the cell and a sharp voltage drop [27]. In comparison, Li/PFPC: 3 wt% LLZTO/Li delivers a much smaller voltage hysteresis at various current densities, and the cell maintains stable cycling under 2.3 mA cm⁻².

Excellent stability against lithium depends on the uniform deposition of lithium. Lithium deposition behavior is closely related to the transport process of Li ions. The main Li-ion transport path in the PFPC SPE is the PVC gel electrolyte in the PVDF pores, so the lithium dendrites grow in the PVDF pores (Figure 5a). When LLZTO nanoparticles are introduced into the polymer matrix, the electrochemical potential difference between the PVC and the LLZTO causes the migration of Li ions in the LLZTO lattice from the surface of the LLZTO to the PVC, resulting in the formation of a large number of lithium vacancies for rapid lithium-ion transport. During this process, a space charge layer is formed at the interface between the polymer substrate and the LLZTO. The space charge layer at the interface of LLZTO and PVC can be used as a three-dimensional ion migration path to redistribute Li ions at the interface of the PFPC: 3 wt% LLZTO SPE and lithium metal anode, so as to achieve uniform lithium deposition on the surface of the lithium metal (Figure 5c) [48,49,50,51]. As shown in Figure 5b,d, after cycling for 100 h, the surface of the electrode in the Li/PFPC/Li cell becomes rough. In contrast, the surface of the electrode in the Li/PFPC: 3 wt% LLZTO/Li cell is still smooth and flat after 100 h of cycling. The excellent interfacial contact and stability between the Li metal and the PFPC: 3 wt% LLZTO SPE facilitates long-term cycling in cells.

3.4. Solid-State Battery Performance

In order to verify the application of electrolytes in practice, Li/LFP cells were assembled. The cells were subjected to cyclic voltammetry (CV) testing. Figure 6a shows the initial CV curves of the Li/PFPC: 3 wt% LLZTO/LFP cell; these five curves basically coincide. The peaks of the curve correspond to the Li-ion insertion and extraction behavior of LFP material, indicating good cycling performance of Li ions during the cycle and almost no loss during the cycle. Further, the cells were subjected to charge and discharge cycles between 2.5 and 3.8 V at room temperature to verify the application of the electrolyte. The rate performance of the Li/LFP cells is shown in Figure 6b,c. It can be seen that the capacity of the Li/PFPC: 3 wt% LLZTO/LFP cell is 156, 151, 140, 127 and 103 mAh g⁻¹ at 0.1, 0.2, 0.5, 1.0 and 2.0 C, respectively. When the current returns to 0.1 C, the capacity is restored to 154 mAh g⁻¹. The excellent rate capability benefits from the fast Li-ion transfer kinetics of PFPC: 3 wt% LLZTO SPEs. The smooth charge/discharge curves of the Li/PFPC: 3 wt% LLZTO/LFP cell at cycles of various rates indicate that no side reactions occur during the cell cycle. However, the polarization voltage of the cell increases slightly as the cycle rate increases, while the specific capacity decreases slightly. In contrast, the specific capacity of the Li/PFPC/LFP cell is 140 mAh g⁻¹ at 0.1 C. As the current density increases, the specific capacity decreases significantly to 23 mAh g⁻¹ at 2.0 C, and the charge/discharge curve shows that polarization of the cell increases significantly as the cycle rate increases (Figure S8). As shown in Figure 6d,e, the Li/PFPC: 3 wt% LLZTO/LFP cell cycles stably for more than 150 cycles at 0.2 C (0.13 mA cm⁻²) with a capacity retention rate of about 87% and an average coulomb efficiency of 99.5%. In contrast, the specific capacity of the LFP/PFPC/Li cell is only 27 mAh g⁻¹ after 150 cycles at 0.2 C (0.15 mA cm⁻²), and the charge/discharge curve of the cell shows that the polarization voltage of the cell increases significantly after cycling, which is caused by the side reactions between the Li metal and PVC at the interface (Figure S9). Further verifying the cycling performance of the Li/PFPC: 3 wt% LLZTO/LFP cell at a high rate, the stable cycling at 0.5 C (0.61 mA cm⁻²) for more than 100 cycles results in a capacity retention rate of about 89% and a coulomb efficiency of 99.5% (Figure 6f,g). The much-improved electrochemical performance of the Li/PFPC: 3 wt% LLZTO/LFP cell benefits from the fast Li-ion transport of the electrolyte and the good interface contact between the electrolyte and the electrode, demonstrating the prospect of practical applications of the PFPC: 3 wt% LLZTO SPE.

4. Conclusions

In this work, a novel PFPC: 3 wt% LLZTO SPE was fabricated via in situ polymerization. The introduction of VC and LLZTO not only filled the holes in the PVDF SPE, but also homogenized Li-ion flux and stabilized the electrode/electrolyte interface, thereby preventing lithium dendrites from piercing the electrolyte. This hybrid PFPC: 3 wt% LLZTO SPE exhibits improved ionic conductivity (4.25 × 10⁻⁴ S cm⁻¹ at 30 °C), a broad electrochemical window (>4.6 V) and a high Li-ion transference number (t_Li⁺ = 0.49). The integrated Li/PFPC: LLZTO-SPE/LFP cells exhibit much-improved capacity retention and long cycling life. This work provides a promising strategy for composite electrolytes and offers prospects and directions for solid lithium metal batteries.