阅读说明：本技术 含有亲锂金属离子的聚合物固态电解质及制备方法与应用 (Polymer solid electrolyte containing lithium-philic metal ions, preparation method and application thereof ) 是由 慈立杰 曾振 程俊 侯广梅 于 2020-11-26 设计创作，主要内容包括：本公开提供了一种含有亲锂金属离子的聚合物固态电解质及制备方法与应用,该聚合物固态电解质以丙烯酸衍生物为聚合物的主体结构,亲锂金属丙烯酸盐中的羧基基团固定在聚合物的主链上,亲锂金属离子游离在聚合物基体中。含有亲锂性金属离子的聚合物固态电解质电导率优于单离子导体电解质,不仅能够实现电解质内部的离子调控,而且,还能够实现在锂表面的合金化,从而实现锂离子的均匀沉积,表现出优异的对锂稳定性,由此制备的全电池也实现了在大倍率下长时间的稳定循环且展现了良好的倍率性能。(The polymer solid electrolyte takes an acrylic acid derivative as a main body structure of a polymer, a carboxyl group in lithium-philic metal acrylate is fixed on a main chain of the polymer, and lithium-philic metal ions are dissociated in a polymer matrix. The polymer solid electrolyte containing lithium-philic metal ions has higher conductivity than a single-ion conductor electrolyte, can realize ion regulation in the electrolyte and alloying on the surface of lithium, thereby realizing uniform deposition of lithium ions and showing excellent stability to lithium, and the prepared full battery also realizes long-time stable circulation under high rate and shows good rate performance.)

1. A polymer solid electrolyte containing lithium-philic metal ions is characterized in that the polymer solid electrolyte takes an acrylic acid derivative as a main structure of a polymer, carboxyl groups in lithium-philic metal acrylate are fixed on a main chain of the polymer, and the lithium-philic metal ions are dissociated in a polymer matrix.

2. The solid polymer electrolyte according to claim 1, wherein the concentration of the lithium-philic metal ion in the solid electrolyte is 0 to 4.24 x 10^-4mol/g; preferably, the concentration of the lithium-philic metal ion in the polymer solid electrolyte is 2.12X 10^-4mol/g; the lithium-philic metal is at least one of aluminum, magnesium, zinc, calcium, gallium, germanium, silver, indium, platinum and gold; preferably, the lithium-philic metal is zinc.

3. The polymer solid electrolyte containing lithium-philic metal ions as claimed in claim 1, wherein the acrylic acid derivatives are any two of polyethylene glycol diacrylate, methoxypolyethylene glycol acrylate, polyethylene glycol dimethacrylate, polyethylene glycol methyl ether methacrylate, tripropylene glycol diacrylate, trimethylolpropane triacrylate, ethoxyethoxyethyl acrylate, hydroxyethyl methacrylate; preferably, the acrylic acid derivatives are polyethylene glycol diacrylate and methoxypolyethylene glycol acrylate;

further, the lithium-philic metal acrylate is selected from the group consisting of zinc acrylate, magnesium methacrylate, magnesium acrylate, zinc dimethacrylate, aluminum acrylate, aluminum methacrylate, silver acrylate; preferably, the lithium-philic metal acrylate is selected from zinc acrylate, magnesium methacrylate, magnesium acrylate or zinc dimethacrylate; still more preferably, the lithium-philic metal acrylate is zinc dimethacrylate.

4. The method of claim 1, wherein the method comprises adding the small molecule monomer, lithium salt and initiator into the organic solution, stirring, and polymerizing the stirred precursor solution under vacuum.

5. The preparation method according to claim 4, wherein the mass ratio of the small molecular monomer, the lithium salt and the initiator in the precursor solution is 2-5: 1-2: 0.005-0.02; preferably, 4:1.6: 0.01;

further, introducing a reinforcing matrix into the precursor solution, wherein the reinforcing matrix is selected from polyvinylidene fluoride-hexafluoropropylene, polyvinylidene fluoride or polyethylene oxide; preferably, in order to improve the strength of the polymer electrolyte, the reinforcing matrix is polyvinylidene fluoride-hexafluoropropylene;

further, the mass fraction of the reinforcing matrix in the precursor solution is 10-14%, preferably 12%;

further, the organic solution is selected from N-methyl pyrrolidone, N-dimethyl formamide or dimethyl sulfoxide; in order to better dissolve lithium salt, small molecule monomer and can dissolve the reinforcing matrix, preferably, the organic solution is an organic solution of N-methylpyrrolidone.

6. The process according to claim 4, wherein a plasticizer selected from the group consisting of diethyl carbonate, dimethyl carbonate, ethyl methyl carbonate, dioxolane, dimethyl polyethylene glycol, succinonitrile and ionic liquids is optionally added to the precursor solution; preferably, the plasticizer is diethyl carbonate;

further, the small molecule monomer is selected from any two of polyethylene glycol diacrylate, methoxy polyethylene glycol acrylate, polyethylene glycol dimethacrylate, polyethylene glycol methyl ether methacrylate, tripropylene glycol diacrylate, trimethylolpropane triacrylate, ethoxyethoxyethyl acrylate and hydroxyethyl methacrylate; preferably, the small molecule monomer is polyethylene glycol diacrylate and methoxy polyethylene glycol acrylate;

further, the lithium salt is selected from lithium bistrifluoromethanesulfonylimide (LiTFSI), lithium difluorooxalato borate, lithium perchlorate, lithium hexafluorophosphate or lithium bis (fluorosulfonyl) imide; preferably, the lithium salt is lithium bistrifluoromethanesulfonylimide (LiTFSI).

7. The method according to claim 4, wherein the polymerization is carried out by a method selected from the group consisting of radical thermal polymerization, ultraviolet polymerization, anionic polymerization and cationic polymerization; preferably, the polymerization mode is free radical thermal polymerization;

further, the initiator comprises a thermal initiator and a photoinitiator, wherein the thermal initiator is selected from azobisisobutyronitrile or benzoyl peroxide; preferably, the initiator is azobisisobutyronitrile; the photoinitiator is selected from methyl benzoylformate, 2-dimethoxy-2-phenylacetophenone, 2-dimethoxy-2-phenylacetophenone, 4-methylbenzophenone, benzophenone or 2-hydroxy-2-methyl propiophenone, preferably, the photoinitiator is 2-hydroxy-2-methyl propiophenone;

further, the polymerization conditions are:

when the initiator is a thermal initiator, pouring the stirred precursor solution on a glass plate, carrying out blade coating by using a scraper to form a film, and polymerizing the film for 1-24 hours under the vacuum drying condition of 50-90 ℃; preferably, the temperature of vacuum drying is 80 ℃; preferably, the time of polymerization is 12 hours;

or, when the initiator is a photoinitiator, pouring the stirred precursor solution on a glass plate, carrying out blade coating with a scraper to form a film, and irradiating with ultraviolet light for 5-20min, preferably, the ultraviolet light irradiation time is 15 min;

further, after the polymerization is finished, the mixture is continuously dried for 8 to 12 hours under the vacuum drying condition of 50 to 90 ℃; preferably, the vacuum drying temperature is 80 ℃; preferably, the drying time is 10 hours.

8. A solid-state lithium ion battery comprising a positive electrode, a lithium metal negative electrode and an electrolyte, wherein the electrolyte is the polymer solid-state electrolyte containing lithium-philic metal ions according to any one of claims 1 to 3 and/or the polymer solid-state electrolyte obtained by the method according to any one of claims 4 to 7.

9. The solid state lithium ion battery of claim 8, wherein the positive electrode material comprises lithium iron phosphate, lithium cobaltate, ternary positive electrode; preferably, it is lithium iron phosphate.

10. Use of the polymer solid electrolyte containing lithium-philic metal ions according to any one of claims 1 to 3 and/or the solid-state lithium-ion battery according to claim 8 in the field of flexible devices.

Technical Field

The invention relates to the technical field of preparation of lithium ion batteries, in particular to a polymer solid electrolyte containing lithium-philic metal ions, a preparation method and application thereof.

Background

The information in this background section is only for enhancement of understanding of the general background of the invention and is not necessarily to be construed as an admission or any form of suggestion that this information forms the prior art that is already known to a person of ordinary skill in the art.

The all-solid-state lithium metal battery formed by matching the solid electrolyte with the lithium metal battery has extremely high energy density and good safety, and is an important development direction of future energy storage devices. Solid electrolytes can be broadly classified into inorganic solid electrolytes and polymer solid electrolytes. The rigid nature of the inorganic solid electrolyte makes poor contact with the lithium negative electrode, severely affecting the transport of lithium ions at the interface. Compared with inorganic solid electrolytes, polymer solid electrolytes have a series of incomparable advantages, but the application of the polymer solid electrolytes in all-solid-state lithium metal batteries also faces many challenges, and the polymers have low ionic conductivity, narrow electrochemical window and low mechanical strength. What is more troublesome is that the interface between the polymer electrolyte and the lithium negative electrode continues to deteriorate during cycling, resulting in low battery efficiency and severe capacity degradation. The interfacial problems mainly include persistent interfacial side reactions and the growing of lithium dendrites, which are caused by the properties of the lithium metal itself and non-uniform lithium deposition/exfoliation during battery cycling.

Metallic lithium has extremely strong reduction characteristics, and can react with most of electrolytes and lithium salts to generate an electronic insulating and ionic conducting solid electrolyte interface layer (SEI) at an electrolyte/lithium interface. The SEI formation results in loss of electrode material and electrolyte, reducing coulombic efficiency, and blocks the lithium negative electrode from the electrolyte, preventing further reaction between the two.

Non-uniform lithium deposition/exfoliation induced by non-uniform electric field and ion distribution at the interface is yet another important cause of interface problems. The deposition/stripping of lithium is accompanied by a huge volume change of a lithium metal electrode material, and the local excessive lithium deposition/stripping can cause continuous fracture of an SEI film and continuous renewal of an interface, thereby causing continuous occurrence of interface reactions and continuous increase of interface resistance; in addition, the uneven deposition of lithium ions induces the generation of lithium dendrites, and the overall mechanical strength of the polymer solid electrolyte is insufficient to effectively hinder the growth of lithium dendrites, thus risking short circuits. In addition, lithium atoms at the root of the lithium dendrites preferentially lose electrons during the subsequent stripping process to form dead lithium, which additionally reduces the coulombic efficiency of the battery. Therefore, the key to solve the problem of the interface between the polymer solid electrolyte and the lithium cathode is to regulate and control the ion distribution at the interface and realize uniform deposition and stripping of lithium ions.

In order to solve the above problems, single ion conductor polymer electrolytes and surface alloying treatments have been used for extensive research. However, the inventors found that the single ion conductor polymer electrolyte has disadvantages in that it has low ionic conductivity, it is difficult to achieve high specific capacity cycling of the battery at a large rate, and the anion groups completely anchored on the polymer main chain limit migration of lithium ions in the polymer matrix to some extent due to strong electrostatic attraction between the anion groups and lithium ions. The surface alloying treatment usually involves chemical treatment of the lithium metal surface or modification of one side of a corresponding electrolyte, the operation is complicated, and some measures aiming at the surface treatment of the inorganic solid electrolyte, such as magnetron sputtering, atomic deposition and the like, are difficult to be carried out due to the property difference of the polymer solid electrolyte and the inorganic solid electrolyte. At present, surface alloying treatment means are mostly applied to liquid lithium metal batteries and inorganic solid lithium metal battery systems. Therefore, the current polymer solid electrolyte still cannot meet the requirements of the all-solid-state lithium metal battery, and the technical problem that researchers need to overcome how to solve the defects of the current polymer solid electrolyte is solved.

Disclosure of Invention

In order to solve the defects of the prior art, the purpose of the present disclosure is to provide a polymer solid electrolyte containing lithium-philic metal ions, and a preparation method and an application thereof, wherein the polymer solid electrolyte containing lithium-philic metal ions has a conductivity superior to that of a single-ion conductor electrolyte, and not only can realize ion regulation inside the electrolyte, but also can realize alloying on the surface of lithium, so as to realize uniform deposition of lithium ions and show excellent stability to lithium, and thus, the prepared full cell also realizes stable cycling under a large rate for a long time and shows good rate performance.

Specifically, the technical scheme of the present disclosure is as follows:

in a first aspect of the present disclosure, the present disclosure provides a polymer solid electrolyte containing lithium-philic metal ions, the polymer solid electrolyte uses an acrylic acid derivative as a main structure of a polymer, carboxyl groups in a lithium-philic metal acrylate are fixed on a main chain of the polymer, and the lithium-philic metal ions are free in a polymer matrix.

In a second aspect of the present disclosure, the present disclosure provides a method for preparing a polymer solid electrolyte containing lithium-philic metal ions, which includes adding a small molecule monomer, a lithium salt and an initiator into an organic solution, stirring, and polymerizing the stirred precursor solution under vacuum conditions.

In a third aspect of the present disclosure, the present disclosure provides a solid-state lithium metal battery comprising a positive electrode, a lithium metal negative electrode, and an electrolyte, which is a polymer solid-state electrolyte containing lithium-philic metal ions and/or a polymer solid-state electrolyte obtained by the above-described method.

In a fourth aspect of the present disclosure, the present disclosure provides a use of a polymer solid electrolyte containing lithium-philic metal ions and/or a solid-state lithium-ion battery in the field of flexible devices.

One or more technical schemes in the disclosure have the following beneficial effects:

(1) in order to promote the uniform deposition of lithium ions and achieve the purposes of regulating ion current and slowing down the growth of lithium dendrites, the lithium-philic metal acrylate is polymerized with other small molecular free radicals to introduce the lithium-philic metal ions and fix carboxylic acid groups on a polymer main chain at the same time, so that the ionic polymer solid electrolyte is obtained and plays a role in regulating and controlling ion distribution. During the battery cycle, the carboxylic acid group fixed on the main chain can inhibit concentration polarization caused by the reverse movement of anions, and is beneficial to the uniform distribution of lithium ions in the electrolyte, thereby promoting the uniform deposition of the lithium ions and slowing down the growth of lithium dendrites.

(2) In order to slow down the local excessive Li on the surface of the lithium cathode⁺And a sharp volume change due to deposition/peeling, thereby slowing the renewal rate of the SEI film and reducing the occurrence of side reactions, and also helping to inhibit the growth of lithium dendrites, wherein after lithium-philic metal ions are introduced into an ionic polymer solid electrolyte, which is assembled into a battery, the lithium-philic metal ions in the electrolyte can migrate to the surface of a lithium metal electrode and be reduced to zero-valent lithium-philic metal under the driving of an applied electric field during battery cycling. The zero-valent lithium-philic metal can further generate alloying reaction with lithium so as to form an alloy layer on the surface of the lithium metal. Due to Li of the alloy⁺The diffusion rate is higher than that of lithium metal, Li⁺Can migrate more rapidly inside the alloy layer while Li between the lithium metal substrate below the alloy layer and the alloy layer⁺The transfer rate will also increase. Alloy layer for Li⁺The promotion effect of the migration can relieve the violent volume change of the surface of the lithium negative electrode, thereby reducing the occurrence of side reactions and inhibiting the growth of lithium dendrites.

(3) The solid lithium ion battery assembled by the polymer solid electrolyte containing the lithium-philic metal ions has good cycle stability and is 0.5C (1C is 170mAh g)^-1) Under the condition of (1), the discharge capacity after the circulation of 400 circles is 144mA h g^-1The capacity retention rate reaches 93.4% and the coulombic efficiency is 99.91%. Magnification at 1CNext, LFP/SPE-5Zn/Li cycles 200 cycles before maintaining 113.5mA h g^-1The reversible capacity of (2) was 88.8% in capacity retention rate and 99.91% in coulombic efficiency.

Drawings

The accompanying drawings, which are included to provide a further understanding of the disclosure, illustrate embodiments of the disclosure and together with the description serve to explain the disclosure and are not to limit the disclosure.

Embodiments of the present disclosure are described in detail below with reference to the attached drawing figures, wherein:

FIG. 1 is a schematic view showing the chemical structures of the monomers polymerized and the molecular structure of the polymerization product in example 1;

FIG. 2 is a plot of the logarithm of the conductivity versus the reciprocal Kelvin temperature for each sample of example 1;

FIG. 3 shows the cell density at 0.1mA cm for the symmetrical cell of example 5^-1(a) And 0.2mA cm^-1(c) The cycle curves under (a) - (d); the appearance (e) of the surface of the lithium negative electrode after Li/SPE-0Zn/Li circulation; the shape (f) and Zn element distribution (g) of the surface of the lithium cathode after Li/SPE-5Zn/Li circulation of the symmetric battery;

FIG. 4 is the electrochemical impedance spectra before and after cycling for the symmetrical cell of example 5: (a) Li/SPE-0 Zn/Li; (b) Li/SPE-5 Zn/Li;

FIG. 5 shows the PEO-based solid polymer symmetric cell of example 5 at 0.2mA cm^-1The lower cycle curve;

FIG. 6 is an X-ray photoelectron spectrum of Zn element on the surface of a lithium negative electrode after Li/SPE-5Zn/Li cycling of the symmetric cell in example 5;

FIG. 7 is the cycle performance and (C) rate performance of the full cell LFP// Li of example 5 at (a)0.5C and (b) 1C;

fig. 8 is cycle performance at 0.5C for the PEO-based solid polymer full cell of example 5;

fig. 9 is a capacity-voltage curve of the full cell of example 5 at various cycle numbers at 0.5C: (a) Li/SPE-0 Zn/Li; (b) Li/SPE-5 Zn/Li;

fig. 10 is the electrochemical impedance of the full cell of example 5 at various cycles at 0.5C: (a) Li/SPE-0 Zn/Li; (b) Li/SPE-5 Zn/Li;

fig. 11 is a graph showing cycle performance at 0.2C of an electrolyte full cell prepared by uv polymerization of example 4.

Detailed Description

The disclosure is further illustrated with reference to specific examples. It should be understood that these examples are for illustrative purposes only and are not intended to limit the scope of the present disclosure. The experimental procedures, in which specific conditions are not noted in the following examples, are generally carried out according to conventional conditions or according to conditions recommended by the manufacturers.

Unless defined otherwise, all technical and scientific terms used herein have the same meaning as commonly understood by one of ordinary skill in the art. The reagents or starting materials used in the present invention can be purchased from conventional sources, and unless otherwise specified, the reagents or starting materials used in the present invention can be used in a conventional manner in the art or in accordance with the product specifications. In addition, any methods and materials similar or equivalent to those described herein can be used in the methods of the present invention. The preferred embodiments and materials described herein are intended to be exemplary only.

It is noted that the terminology used herein is for the purpose of describing particular embodiments only and is not intended to be limiting of example embodiments according to the present disclosure. As used herein, the singular forms "a", "an" and "the" are intended to include the plural forms as well, and it should be understood that when the terms "comprises" and/or "comprising" are used in this specification, they specify the presence of the stated features, steps, operations, and/or combinations thereof, unless the context clearly indicates otherwise.

As introduced by the background art, the current polymer solid electrolyte still has the problems that the solid battery cannot realize long circulation under a large multiplying power due to low ionic conductivity and serious lithium dendrite, and in order to solve the technical problems in the prior art, the disclosure provides a polymer solid electrolyte containing lithium-philic metal ions, and a preparation method and application thereof.

In one embodiment of the present disclosure, a polymer solid electrolyte containing lithium-philic metal ions is provided, the polymer solid electrolyte takes an acrylic acid derivative as a main structure of a polymer, carboxyl groups in lithium-philic metal acrylate are fixed on a main chain of the polymer, and the lithium-philic metal ions are free in a polymer matrix.

Further, the concentration of the lithium-philic metal ions in the polymer solid electrolyte is 0-4.24 multiplied by 10^-4mol/g, in order to improve the conductivity of the polymer solid electrolyte, realize the optimal regulation and control of ion current in the electrolyte, facilitate the uniform distribution of lithium ions in the electrolyte, promote the uniform deposition of the lithium ions and slow down the growth of lithium dendrites, preferably, the concentration of lithium-philic metal ions in the polymer solid electrolyte is 2.12 x 10^-4mol/g。

Further, the lithium-philic metal is at least one of aluminum, magnesium, zinc, calcium, gallium, germanium, silver, indium, platinum and gold; preferably, the lithium-philic metal is zinc.

Further, the acrylic acid derivatives are any two of polyethylene glycol diacrylate, methoxy polyethylene glycol acrylate, polyethylene glycol dimethacrylate, polyethylene glycol methyl ether methacrylate, tripropylene glycol diacrylate, trimethylolpropane triacrylate, ethoxyethoxyethyl acrylate and hydroxyethyl methacrylate; preferably, the acrylic acid derivatives are polyethylene glycol diacrylate and methoxypolyethylene glycol acrylate.

Further, the lithium-philic metal acrylate is selected from the group consisting of zinc acrylate, magnesium methacrylate, magnesium acrylate, zinc dimethacrylate, aluminum acrylate, aluminum methacrylate, silver acrylate; preferably, the lithium-philic metal acrylate is selected from zinc acrylate, magnesium methacrylate, magnesium acrylate or zinc dimethacrylate; still more preferably, the lithium-philic metal acrylate is zinc dimethacrylate.

In one or more embodiments of the present disclosure, a method for preparing a polymer solid electrolyte containing lithium-philic metal ions is provided, which includes adding a small molecule monomer, a lithium salt and an initiator into an organic solution, stirring, and polymerizing the stirred precursor solution under vacuum conditions.

Further, in the precursor solution, the mass ratio of the small molecular monomer to the lithium salt to the initiator is 2-5: 1-2: 0.005-0.02; preferably, it is 4:1.6: 0.01.

Further, introducing a reinforcing matrix into the precursor solution, wherein the reinforcing matrix is selected from polyvinylidene fluoride-hexafluoropropylene (PVDF-HFP), polyvinylidene fluoride or polyethylene oxide; preferably, in order to improve the strength of the polymer electrolyte, the reinforcing matrix is polyvinylidene fluoride-hexafluoropropylene.

Further, the mass fraction of the reinforcing matrix in the precursor solution is 10-14%, preferably 12%. The mass fraction of the reinforced matrix is roughly determined by the overall viscosity of the solution, and the proper solution viscosity can prevent the thickness of the liquid layer in a large area from being greatly changed due to the tiny inclination of the glass plate after the subsequent precursor solution is coated on the glass plate, so that the final electrolyte membrane is not easy to curl or cannot be formed. However, if the mass fraction is too high, the reinforced matrix is difficult to be completely dissolved in the organic solvent, and the solution is too viscous, which is not beneficial to the preparation and subsequent operation of the precursor solution.

Further, the organic solution is selected from N-methyl pyrrolidone, N-dimethyl formamide or dimethyl sulfoxide; in order to better dissolve lithium salt, small molecule monomer and can dissolve the reinforcing matrix, preferably, the organic solution is an organic solution of N-methylpyrrolidone.

Further, since the addition of the plasticizer can improve the conductivity of the whole electrolyte, the plasticizer selected from diethyl carbonate, dimethyl carbonate, ethyl methyl carbonate, dioxolane, polyethylene glycol dimethyl ether, succinonitrile or ionic liquid may be added to the precursor solution; preferably, the plasticizer is diethyl carbonate.

Further, the small molecule monomer is selected from any two of polyethylene glycol diacrylate, methoxy polyethylene glycol acrylate, polyethylene glycol dimethacrylate, polyethylene glycol methyl ether methacrylate, tripropylene glycol diacrylate, trimethylolpropane triacrylate, ethoxyethoxyethyl acrylate and hydroxyethyl methacrylate; preferably, the small molecule monomer is polyethylene glycol diacrylate and methoxy polyethylene glycol acrylate.

Further, the lithium salt is selected from lithium bistrifluoromethanesulfonylimide (LiTFSI), lithium difluorooxalato borate, lithium perchlorate, lithium hexafluorophosphate or lithium bis (fluorosulfonyl) imide; preferably, the lithium salt is lithium bistrifluoromethanesulfonylimide (LiTFSI).

Further, the polymerization mode is selected from free radical thermal polymerization, ultraviolet light polymerization, anionic polymerization or cationic polymerization; preferably, the polymerization mode is free radical thermal polymerization.

Further, the initiator includes a thermal initiator and a photoinitiator selected from Azobisisobutyronitrile (AIBN) or Benzoyl Peroxide (BPO); preferably, the initiator is azobisisobutyronitrile; the photoinitiator is selected from methyl benzoylformate, 2-dimethoxy-2-phenylacetophenone, 2-dimethoxy-2-phenylacetophenone (DMPA), 4-methylbenzophenone, benzophenone or 2-hydroxy-2-methyl propiophenone (HMPP), and preferably, the photoinitiator is 2-hydroxy-2-methyl propiophenone.

Further, the polymerization conditions are:

when the initiator is a thermal initiator, pouring the stirred precursor solution on a glass plate, carrying out blade coating by using a scraper to form a film, and polymerizing the film for 1-24 hours under the vacuum drying condition of 50-90 ℃; preferably, the temperature of vacuum drying is 80 ℃; preferably, the time of polymerization is 12 hours;

or, when the initiator is a photoinitiator, pouring the stirred precursor solution on a glass plate, carrying out blade coating by using a scraper to form a film, and irradiating by using ultraviolet light for 1-20min, wherein the preferable ultraviolet light irradiation time is 4 min.

Further, after the polymerization is finished, the mixture is continuously dried for 8 to 12 hours under the vacuum drying condition of 50 to 90 ℃; preferably, the vacuum drying temperature is 80 ℃; preferably, the drying time is 10 hours.

In another embodiment of the present disclosure, a solid-state lithium ion battery is provided, which includes a positive electrode, a negative electrode, and an electrolyte, wherein the electrolyte is a polymer solid-state electrolyte containing lithium-philic metal ions and/or a polymer solid-state electrolyte obtained by the above method.

Further, the positive electrode material comprises lithium iron phosphate (LFP), Lithium Cobaltate (LCO) and a ternary positive electrode (NCM 811); preferably, lithium iron phosphate (LFP).

In another embodiment of the present disclosure, there is provided a use of a polymer solid electrolyte containing lithium-philic metal ions and/or a solid-state lithium metal battery in the field of flexible devices.

In order to make the technical solutions of the present disclosure more clearly understood by those skilled in the art, the technical solutions of the present disclosure will be described in detail below with reference to specific embodiments.

Example 1 (free radical thermal polymerization)

A composition containing Zn²⁺Ionic polymer solid electrolyte:

the related small molecular monomers comprise polyethylene glycol diacrylate (Poly (ethylene glycol) diacrylate, PEGDA, Mn is 600g mol < -1 >), methoxy polyethylene glycol acrylate (Poly (ethylene glycol) methyl acrylate, PEGMEA, Mn is 480g mol < -1 >), and Zinc dimethacrylate (ZnMA); the thermal free radical polymerization initiator is azobisisobutyronitrile (2,2' -Azobis (2-methyl propionitril), AIBN); lithium bistrifluoromethane sulphonimide (bis (trifluoromethylmethane) sulfonium salt, LiTFSI), acetonitrile (acetonitrile), N-methylpyrrolidone (1-Methyl-2-pyrrolidinone, NMP), polyvinylidene fluoride-hexafluoropropylene (Poly (vinylidine fluoride-co-hexafluoroacetone), PVDF-HFP, Mw ═ 400,000)).

Step (1): preparing PVDF-HFP solution: 0.4g of PVDF-HFP was dissolved in 2.93g of NMP in a mass fraction of 12%.

Step (2): preparing a precursor solution: 1.2g PEGMEA, 0.4g PEGDA, a quantity of ZnMA (0g, 0.05g, 0.1g, 0.15g, 0.2g), 0.65g lithium salt (LiTFSI), and 5mg thermal initiator (AIBN) were added to a previously prepared solution of PVDF-HFP in NMP and stirred well.

And (3): precursor solution polymerization: the stirred precursor solution was poured onto a glass plate and drawn down to form a film with a doctor blade and allowed to polymerize under vacuum drying at 80 ℃ for 12 hours.

And (4): drying the polymer electrolyte membrane: after the polymerization is finished, the mixture is dried for 10 hours under the vacuum drying condition of 80 ℃ to obtain the product containing Zn²⁺Ionic polymer solid electrolytes.

Meanwhile, in order to illustrate the superior performance of the prepared ionic solid polymer electrolyte compared with the conventional polymer solid electrolyte, the PEO-based polymer solid electrolyte is also prepared by a casting method. The specific process is as follows: PEO and lithium salt (LiTFSI) were mixed as 16:1 EO: and adding the Li molar ratio into an appropriate amount of acetonitrile, fully stirring, pouring the slurry into a mold, and performing vacuum drying at 60 ℃ for 24 hours after the acetonitrile is volatilized.

In order to study the influence of different zinc dimethacrylate dosages on the performance of the solid polymer electrolyte, four groups of samples were prepared by changing only the dosages of zinc dimethacrylate, wherein the dosages of methacrylic acid in the total mass of the polymer matrix are respectively 0, 2.5%, 5%, 7.5% and 10%, and the corresponding sample names are respectively SPE-0Zn, SPE-2.5Zn, SPE-5Zn, SPE-7.5Zn and SPE-10Zn, and the initial drug dosages of the samples are shown in the following table 1 (including samples when the dosages of acrylic acid in the total mass of the polymer matrix are respectively 5%):

TABLE 1 raw drug dosage for each sample

Sample name	PEGDA(g)	PEGMEA(g)	ZnMA(g)	PVDF-HFP(g)	LiTFSI(g)
						SPE-0Zn	0.4	1.2	0	0.4	0.65
SPE-2.5Zn	0.4	1.2	0.05	0.4	0.65
						SPE-5Zn	0.4	1.2	0.10	0.4	0.65
SPE-7.5Zn	0.4	1.2	0.15	0.4	0.65
						SPE-10Zn	0.4	1.2	0.20	0.4	0.65

From the conductivity tests of five groups of samples at different temperatures, it was found that the conductivity of the solid electrolyte prepared at each temperature showed a decreasing trend as the amount of zinc dimethacrylate was increased (as shown in table 2). As shown in fig. 2, the logarithm of the conductivity of the sample at each ratio shows a linear relationship with the reciprocal of the temperature, according to the Arrhenius equation:the activation energy of lithium ion transfer of each sample can be obtained according to the slope of the logarithm of the conductivity of each sample and the reciprocal of the temperature, and the calculation result shows that the activation energy of lithium ion transfer of the electrolyte is increased along with the increase of the using amount of the methacrylic acid, and the trend is matched with the change of the conductivity. These phenomena are related to carboxylic acid groups fixed to the main chain. Strong electrostatic interaction exists between carboxylic acid groups and lithium ions, which can hinder free movement of the lithium ions to a certain extent; meanwhile, charge attraction between carboxylic acid groups and zinc ions can also cause physical crosslinking between chain segments, so that free movement of the chain segments is limited, and further the transfer of lithium ions is influenced.

TABLE 2 conductivity and activation energy and lithium ion transport number for each sample at different temperatures

Nevertheless, the polymer electrolyte of the present embodiment has higher conductivity than a general single ion polymer electrolyte. In general, all anionic groups in a single ionic polymer are theoretically fixed to the polymer backbone in an amount corresponding to the amount of lithium ions contained in the matrix. In the scheme, the polymer matrix is introduced with additional lithium salt, the total charge quantity of the cationic ions is far more than that of the negative charges carried by the carboxylic acid groups fixed on the polymer main chain, and the lithium ions are subjected to much smaller resistance from the fixed anionic charges in the migration process than the lithium ions are subjected to the migration resistance in the single-ion polymer electrolyte, so that the lithium ions are macroscopically represented by higher conductivity.

The number of carboxylic acid groups also has an influence on the ion migration number of the electrolyte, and the ion migration number of the sample is improved to a certain extent along with the increase of the using amount of the zinc dimethacrylate. This is because the number of mobile cations in the electrolyte is greater than that of anions due to the fixation of carboxylic acid groups, and the contribution of cations to the overall ion flow is increased under the action of an external electric field, so that the transference number of lithium ions is increased.

Example 2

A composition containing Mg²⁺Ionic polymer solid electrolyte:

step (1): preparing a polyvinylidene fluoride solution: 0.4g of polyvinylidene fluoride was dissolved in 3.0g of NMP.

Step (2): preparing a precursor solution: 1.2g of PEGMEA, 0.4g of PEGDA,0.1g of magnesium methacrylate, 0.65g of lithium salt (LiTFSI) and 5mg of initiator (succinonitrile) were added to the previously prepared NMP solution of polyvinylidene fluoride and stirred well.

And (3): precursor solution polymerization: the stirred precursor solution was poured onto a glass plate and drawn down to form a film with a doctor blade and allowed to polymerize under vacuum drying at 80 ℃ for 12 hours.

And (4): drying the polymer electrolyte membrane: after the polymerization is finished, the mixture is dried for 10 hours under the vacuum drying condition of 80 ℃ to obtain the product containing Mg²⁺Ionic polymer solid electrolytes.

Example 3 (UV polymerization)

Step (1): preparing PVDF-HFP solution: 0.4g of PVDF-HFP was dissolved in 2.93g of NMP in a mass fraction of 12%.

Step (2): preparing a precursor solution: 1.2g of PEGMEA, 0.4g of PEGDA,0.1g of zinc dimethacrylate, 0.65g of lithium salt (LiTFSI) and 8mg of 2-Hydroxy-2-methylpropiophenone (HMPP), a photoinitiator, were added to a previously prepared solution of PVDF-HFP in NMP and stirred well.

And (3): precursor solution polymerization: pouring the stirred precursor solution on a glass plate, and carrying out blade coating by using a scraper to form a film at 50mWcm^-1And polymerizing for 16min under the ultraviolet light with the wavelength of 365 nm.

And (4): drying the polymer electrolyte membrane: after the polymerization is finished, the mixture is dried for 10 hours under the vacuum drying condition of 80 ℃ to obtain the product containing Zn²⁺Ionic polymer solid electrolytes.

Example 4

Electrochemical performance study:

because the zinc dimethacrylate of the SPE-5Zn sample has moderate dosage and higher conductivity, the electrochemical performance of the zinc dimethacrylate is further researched, and the polymer solid electrolyte obtained by the ultraviolet photopolymerization preparation method in the embodiment 3 is also researched.

First, assembling a lithium symmetric battery to study the lithium stability of SPE-5Zn, assembling the symmetric battery (Li/SPE-0 Zn/Li and Li/SPE-5Zn/Li) by SPE-0Zn and SPE-5Zn respectively, and testing the battery at 60 ℃ at 0.1mA cm^-1And 0.2mA cm^-1Current density (one hour each charge and discharge) of (c).

As shown in the results of fig. 3 and 4, the Li/SPE-5Zn/Li maintains a stable polarization voltage at different current densities, the polarization voltage of Li/SPE-0Zn/Li is larger and increases faster, while the symmetric cell assembled by a general polyethylene oxide (PEO) -based solid electrolyte performs worse under the same conditions (as shown in fig. 5). Impedance analysis of the symmetric cell before and after cycling showed interface layer impedance (R) after Li/SPE-0Zn/Li cycling_SEI) And a charge transfer resistance (R)_ct) Has greatly improved interface layer impedance (R) after Li/SPE-5Zn/Li circulation_SEI) And a charge transfer resistance (R)_ct) The increase amplitude is smaller. The stable polarization voltage and slow interfacial resistance increase indicate that SPE-5Zn has excellent stability to lithium.

The lithium electrode after cycling was further analyzed. The lithium sheet surface after cycling of the Li/SPE-0Zn/Li symmetric cell was quite rough and there were a large number of lithium dendrites. While the Li/SPE-5Zn/Li electrode surface was relatively flat after cycling for over 300 hours (FIG. 3). The elemental analysis results show that Zn is uniformly distributed on the surface of the alloy. The results of X-ray photoelectron spectroscopy showed the presence of zero-valent Zn and Li-Zn alloy therein (see FIG. 6).

As in fig. 7-10, SPE-5 Zn-assembled lithium iron phosphate (LFP) full cells (LFP/SPE-5Zn/Li) also exhibited good cycling stability at 0.5C (1C ═ 170mAh g)^-1) Under the condition of (1), the discharge capacity after the circulation of 400 circles is 144mA h g^-1The capacity retention rate reaches 93.4% and the coulombic efficiency is 99.91%. Under the same conditions, the reversible capacity of the SPE-0Zn assembled full battery LFP/SPE-0Zn/Li in 119 cycles is from 150.5mAh g^-1The decline reaches 112.5mAh g^-1Coulombic efficiency was 99.79%. The full cell LFP/PEO/Li cycle life for the PEO-based solid state electrolyte assembly is shorter. The charging and discharging voltage platform of LFP/SPE-5Zn/Li during the circulation period is more stable, and the polarization voltage is smaller. The electrochemical impedance results show that the LFP/SPE-5Zn/Li impedance remains stable during cycling, while the LFP/SPE-0Zn/Li impedance increases uncontrollably. Under the multiplying power of 1C, after LFP/SPE-5Zn/Li cycles for 200 circles, 113.5mA h g can be kept^-1The reversible capacity of (2) is 88.8 percent, the capacity retention rate is 99.91 percent, and the coulombic efficiency is far better than that of LFP/SPE-0 Zn/Li. LFP/SPE-5Zn/Li also has good rate performance, and has higher reversible capacity and more stable coulombic efficiency than LFP/SPE-0Zn/Li under the high rate conditions of 2C, 3C and 4C.

As shown in fig. 11, the electrolyte full cell prepared by uv polymerization still has good cycle performance at 0.2C.

Although the present invention has been described in detail with reference to the foregoing embodiments, it will be apparent to those skilled in the art that changes may be made in the embodiments and/or equivalents thereof without departing from the spirit and scope of the invention. Any modification, equivalent replacement, or improvement made within the spirit and principle of the present invention should be included in the protection scope of the present invention.