Functionalized gel polymer electrolyte membrane for high performance Li metal batteries
Graphical abstract
Introduction
Rechargeable lithium-ion batteries (LIBs) with increased energy density are widely used in electric vehicles and portable electronic devices [[1], [2], [3], [4], [5]]. However, commercial LIBs suffer from a major safety problem due to the organic liquid electrolytes [[6], [7], [8], [9]], which have obviously irresolvable disadvantages, such as the leakage, flammability [2,10], corrosivity and thermal instability [11], significantly limiting their prevailing applications. Hence, solid-state LIBs return back again to the center stage of developing better LIBs. Replacing liquid electrolytes with solid-state electrolytes (SSEs) is considered an effective strategy to achieve the practical solid-state Li-metal batteries free of the aforementioned issues [[11], [12], [13], [14]]. In terms of SSEs, their good chemical/electrochemical stabilities make solid state batteries feasible working in high voltages with desired high energy density, long cycling life, and good reliability [12]. Moreover, with the rigid solid electrolytes, the utility of Li metal with the most negative electrochemical potential (−3.040 V vs. SHE) [15] becomes highly likely to promote the battery energy density, which renders an ultra-high theoretical capacity (3860 vs. 372 mAhg−1 of graphite anode).
There are mainly two families of SSEs, namely the polymer and inorganic electrolytes [16] employed at present to fabricate solid batteries. Inorganic solid electrolytes have advantages of excellent ionic conductivity and high electrochemical windows at room temperature, such as the 0.1–1 mS cm−1 of NASICON type SSEs at 25 °C [14,17,18] and the much-anticipated Garnet type SSEs with the ionic conductivity of >1 mS cm−1 at 25 °C, comparable to organic electrolytes. Of special interest is that Garnet SSEs are thought to be chemical stable with Li anode and their electrochemical window of ~9 V (vs. Li/Li+) [19] is experimentally reached, which is significantly higher than that of liquid electrolytes (usually lower than 4.5 V). However, the Garnet SSEs suffer from the poor interface compatibility with electrolytes and high interface resistance [[20], [21], [22], [23], [24]] that makes it difficult in fast charging owing to their fragility and brittleness [8,22,25]. While polymer-based electrolytes demonstrate the enough flexibility to improve the interface compatibility in solid LIBs [26], although they have some drawbacks including the poor Li conductivity of 10−6 to 10−8 S cm−1 at room temperature [27,28], small ionic transference number (t+ < 0.5), and lower thermal and electrochemical stabilities as well [29]. Apparently, the combination of Garnet and polymer electrolytes, as the “ceramic in polymer” strategy, could play a multiple role in making full advantages of both polymer and inorganic electrolytes to build a consecutive and stable SSE-electrode interface, as well as transport the Li ions and electrons quickly enough [[30], [31], [32], [33], [34], [35], [36], [37], [38], [39]].
In polymer electrolytes, the polyvinylidene fluoride-hexafluoropropylene (PVDF-HFP) demonstrates better thermal stability [40], lower crystallinity and higher ionic conductivity with respect to other polyethylene oxide (PEO) based electrolytes, which has drawn increasingly more attention [41] in battery applications. However, the intrinsic inferior mechanical strength of PVDF-HFP electrolyte restricts their further applications because they fail to sustain the stresses generated by the electrode materials during cycling [42]. As a result, such a combination of PVDF-HFP polymer and inorganic electrolytes as gel polymer electrolytes (GPEs) is somewhat compromise, but effective way in utilizing the high ionic conductivity of inorganic electrolytes and good flexibility of polymer electrolytes [43] for the promising solid LIBs. In this “ceramic in polymer” electrolyte, the PVDF-HFP has good thermoplasticity and easily become colloid as the structural skeleton. To increase the ionic conductivity, inorganic electrolyte can be supplemented into the polymer matrix by many methods, such as the cross-linking, forming block copolymer, adding plasticizers, and introducing ceramic fillers [28,44]. Among these attempts, dispersing ceramic fillers in polymer matrix has attracted great interest because it can enhance the ionic conductivity efficiently, as well as the mechanical strength and thermal stability of polymer electrolytes [45], such as the recent result by Huo et al. using Garnet or Al doped LiGe2(PO4)3 SSEs to enhance the ionic conductivity [46].
In this context, a new GPE membrane is prepared as the PVDF-HFP-LLZTO-LiFSI (PLxL-GPE, x corresponds the mass ratio of LLZTO vs. PVDF-HFP) composite, in which the Li6.4La3Zr1.4Ta0.6O12 (LLZTO) and LiFSI are filled as the ion-conductive agents to improve the ionic conductivity of porous PVDF-HFP electrolyte. The PLxL-GPE membrane exhibited superior electrochemical performance, thermal stability, and mechanical strength of 9.42 MPa. With a higher transference number of 0.62 in Li metal battery tests, both symmetric Li/PL30L-GPE/Li and the LiFePO4|PL30L-GPE|Li cells exhibit excellent electrochemical performance, especially the rate capability (118 mAh g−1 for LiFePO4 at 2C) which rewards from the construction of stable electrolyte/electrolyte interfaces.
Section snippets
Materials
Garnet type Li6.4La3Zr1.4Ta0.6O12 (LLZTO) solid electrolyte was purchased from Hefei Kejing Materials Technology Co. Ltd. (4 N, 99.99%). Polyvinylidene fluoride-hexafluoropropylene (PVDF-HFP) was bought from Sigma-Aldrich Co. (average Mw ~ 455,000, average Mn ~110,000, pellets). Lithium bis(fluorosulfonyl)imide (LiFSI) was from Aladdin Industrial Co., Ltd. (AR, 98%). Acetone and ethanol were from Beijing Chemical Factory (AR, 98%). 1-Methyl-2-pyrrolidinone (NMP) was from Shanghai Aladdin
Results and discussion
The color changes of PVDF-HFP-LLZTO-LiFSI gel polymer electrolyte (GPE) (PLxL-GPE, x corresponds the mass ratio of LLZTO vs. PVDF-HFP) membranes with the Li6.4La3Zr1.4Ta0.6O12 (LLZTO) content are shown in Fig. S1 of Supporting Information (SI). Fig. 1a demonstrates the XRD patterns of the as-prepared PLxL-GPE membranes with the referenced patterns of commercial LLZTO and PVDF-HFP materials. The diffraction peaks match well with the cubic phase LLZTO and no detectable impurities can be observed
Conclusion
In summary, we have developed a gel polymer electrolyte as PVDF-HFP-LLZTO-LiFSI (PLxL-GPE, x corresponds the mass ratio of LLZTO vs. PVDF-HFP) membrane, which combines the high ionic conductivity of garnet type solid state electrolytes and good flexibility of polymer electrolytes. The PLxL-GPE membrane with x = 30% (PL30L-GPE) shows a highest ionic conductivity of 3.57 × 10−4 S cm−1, largest Li-ion transference number of 0.62 and wide electrochemical window of 4.27 V. Moreover, the PL30L-GPE
New concepts
In solid battery, of special interest is that the use of liquid electrolyte, even with very small amount, plays an important role in forming the interphase and activating the ionic transport trajectory, which are inevitable processes at present battery systems to overcome the unresolvable poor interface compatibility. Hence, the side reactions are always not doing harm to the battery performance. Balancing the amounts of side products, even utilizing them in interface is probably a key
Declaration of Competing Interest
The authors have no conflicts of interest to declare. All co-authors have seen and agree with the contents of the manuscript and there is no financial interest to report. We certify that the submission is original work and is not under review at any other publication.
Acknowledgements
The authors thank the funding supports from National Key Research and Development Program of China (No. 2019YFA0705702), National Natural Science Foundation of China (No. 22075328), the Hundreds of Talents program of Sun Yat-sen University, Fundamental Research Funds for the Central Universities (19lgzd05), 21C Innovation Laboratory, Contemporary Amperex Technology Ltd. (No. 21C-OP-202007) and Guangdong Provincial Key Laboratory of Energy Materials for Electric Power (No. 2018B030322001).
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