All-solid-state ionic conductive elastomer based on dynamic supramolecular acting force as well as preparation method and application of all-solid-state ionic conductive elastomer
A novel ion conductive elastomer with hydroxyl groups and dynamic supramolecular forces addresses stability and mechanical weaknesses in existing ion conductive elastomers, offering high strength, stretchability, and self-healing capabilities.
Patent Information
- Application Number
- CN202510451806.0
- Authority / Receiving Office
- CN · China
- Patent Type
- Applications(China)
- Current Assignee / Owner
- Filing Date
- 2025-04-11
- Publication Date
- 2025-07-15
AI Technical Summary
There are limitations in the mechanical properties of existing ionic conductive elastomers, which are prone to fatigue damage and performance degradation, and the gel material has poor stability under different environments.
By introducing hydroxyl groups, dynamic supramolecular forces are constructed using hydrogen bonds and ion-dipole forces to prepare all-solid ion conductive elastomers, and polymerization is performed using photo-induced or in-situ radical polymerization.
The mechanical properties and durability of the material are improved, the tensile strength reaches 1.09MPa, the strain can reach 1000%, and the room temperature conductivity reaches 6.03×10-5S·cm-1, overcoming the stability problem of gel material.
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Figure CN120309804A_ABST
Abstract
Description
Technical Field
[0001] The present invention belongs to the technical field of ion-conductive elastomers, and particularly relates to an all-solid-state ion-conductive elastomer based on dynamic supramolecular interactions, and a preparation method and application thereof. Background Art
[0002] Wearable sensors refer to a type of sensor that converts external mechanical stimuli into changes in electrical signals to simulate the sensing characteristics of human skin, and have attracted much attention due to their wide application prospects in emerging fields such as health monitoring, soft robotics, and humidity sensing. Ion-conductive materials are often used in this regard due to their high conductivity and good stretchability. The most common materials in ion-conductive materials are ion-conductive elastomers, hydrogels, ion gels, and ion-organic gels. Gels are considered to be the most ideal conductive materials because of their high conductivity and stretchability. However, gels show poor stability in the environment, mainly because gels, as hydrophilic materials, can swell in water and contain a large amount of water. At high temperatures, the water will volatilize severely, freeze at low temperatures, lose water severely in dry conditions, and absorb too much water in humid environments, leading to swelling and even rupture. These situations limit the working environment of gels.
[0003] In recent years, the preparation of solvent-free ion-conductive elastomers using polymerizable ionic liquid monomers has received extensive attention. Since ion-conductive elastomers do not contain any liquid ionic components, they effectively overcome the problem of easy leakage of ionic liquids in ion gels and have excellent environmental stability, with a thermal decomposition temperature as high as 400°C. Moreover, due to their properties such as high conductivity, high toughness, and high transparency, they have broad application prospects in fields such as flexible electronic devices and soft robots. However, as a flexible material, the mechanical properties of ion-conductive elastomers are often not satisfactory. Because in the absence of a cross-linked structure, the intermolecular forces in linear elastomers are too small, resulting in limited mechanical properties, and thus the material is prone to fatigue damage and performance degradation during long-term use. The present invention innovatively introduces hydroxyl groups into the polymerization monomer to construct a novel structure of ion-conductive elastomer. Without an external cross-linking agent, the mechanical properties and durability of the material are improved through multiple dynamic supramolecular interactions such as hydrogen bonding and ion-dipole interactions, and the elastomer structure is further regulated by changing the monomer ratio, so that different properties of the material are optimized. This material is a novel ion-conductive elastomer material, providing a new idea for the development of multifunctional flexible materials. Summary of the Invention
[0004] The object of the present invention is to provide an all-solid-state ion-conductive elastomer based on dynamic supramolecular interactions and a preparation method thereof. Relevant research shows that by designing and introducing acrylate monomers, the elastomer is endowed with high strength, high elongation rate and self-healing properties based on hydrogen bonds and ion-dipole interactions. The presence of these two interactions not only enhances the intermolecular forces but also effectively improves the mechanical properties of the material and overcomes the defects of the material in practical applications.
[0005] To achieve the above object, the technical solution adopted by the present invention is as follows:
[0006] An all-solid-state ion-conductive elastomer based on dynamic supramolecular interactions is prepared by a photoinitiated polymerization method or an in-situ radical polymerization method from a hydroxylated ionic liquid monomer and a hydroxylated acrylate monomer in a molar ratio of 1:100 to 100:1.
[0007] Preferably, in the above all-solid-state ion-conductive elastomer based on dynamic supramolecular interactions, the chemical structure of the hydroxylated ionic liquid monomer is any one of those shown in (Ⅰ):
[0008]
[0009] wherein, X1 - is TFSI - , SbF6 - , CF3SO3 - , CF3COO - , FSI - , N(C2F5SO2)2 - , CH3SO3 - any one of them; n represents the carbon chain length of the ionic liquid monomer, and the value range is 1 to 15.
[0010] Preferably, in the above all-solid-state ion-conductive elastomer based on dynamic supramolecular interactions, the chemical structure of the hydroxylated acrylate monomer is any one of those shown in (Ⅱ), (Ⅲ) and (Ⅳ):
[0011]
[0012] The preparation method of the all-solid-state ion-conductive elastomer based on dynamic supramolecular interactions according to any one of the above, by the photoinitiated polymerization method, includes the following steps: ultrasonically dispersing the hydroxylated ionic liquid monomer, the hydroxylated acrylate monomer and the photoinitiator at room temperature, mixing evenly to obtain a transparent homogeneous precursor solution, pouring the precursor solution into a mold, and inducing polymerization by ultraviolet light irradiation, irradiating with ultraviolet light of wavelength 365 nm and power 10 W for 10 min to 1 h to obtain the all-solid-state ion-conductive elastomer.
[0013] Preferably, in the above-mentioned photoinitiated polymerization method, the photoinitiator is any one of 2-hydroxy-2-methyl-1-phenyl-1-propanone, 2-methyl-2-(4-morpholinyl)-1-[4-(methylthio)phenyl]-1-propanone, 2-hydroxy-2-methyl-1-[4-(2-hydroxyethoxy)phenyl]-1-propanone, 2-hydroxy-2-methyl-1-[4-(2-hydroxyethoxy)phenyl]-1-propanone, and 2,4,6-trimethylbenzoyl-diphenylphosphine oxide.
[0014] Preferably, in the above-mentioned photoinitiated polymerization method, the mass of the photoinitiator is 1% to 5% of the total mass of the hydroxylated ionic liquid monomer and the hydroxylated acrylate monomer.
[0015] Preferably, in the above-mentioned photoinitiated polymerization method, the mold material is any one of polytetrafluoroethylene, glass, silica gel, and ceramic.
[0016] The preparation method of a kind of all-solid-state ion-conducting elastomer based on dynamic supramolecular forces described in any one of the above, through in-situ radical polymerization method, includes the following steps: Under an inert atmosphere, add the hydroxylated ionic liquid monomer, the hydroxylated acrylate monomer, and the radical initiator into a single-necked round-bottom flask, add an organic solvent with a boiling point of 80 to 150 °C, stir at room temperature for 0.1 to 1 h to obtain a homogeneous precursor solution, carry out a polymerization cross-linking reaction at 40 to 80 °C, and remove the organic solvent by vacuum drying to obtain the all-solid-state ion-conducting elastomer.
[0017] Preferably, in the above-mentioned in-situ radical polymerization method, the radical initiator is any one of azobisisobutyronitrile, diacyl peroxide, and persulfate.
[0018] The application of a kind of all-solid-state ion-conducting elastomer based on dynamic supramolecular forces described in any one of the above in flexible sensing materials.
[0019] The beneficial effects of the present invention are:
[0020] 1. The preparation method of the all-solid-state ion-conducting elastomer based on dynamic supramolecular forces provided by the present invention adopts a one-step method or a one-pot method, through a photoinitiated polymerization method or a radical polymerization method, which is simple and fast, saving time and cost.
[0021] 2. The all-solid-state ion-conducting elastomer prepared by the present invention selects a material without any liquid ion components, effectively overcoming the problem of easy leakage of ionic liquid in the ion gel and greatly improving the service life of the material.
[0022] 3. The all-solid-state ion-conductive elastomer based on dynamic supramolecular forces prepared in the present invention is introduced with hydroxyl groups, endowing the material with supramolecular forces such as hydrogen bonds and ion-dipoles, forming physical cross-linking points, endowing the material with excellent mechanical properties, with a tensile strength of up to 1.09 MPa and a strain of up to 1000%.
[0023] 4. The all-solid-state ion-conductive elastomer based on dynamic supramolecular forces prepared in the present invention does not add any conductive fillers, and conducts electricity through the free movement of mobile anions in the material. The conductivity at room temperature can reach 6.03×10 -5 S·cm -1 。 Description of the Drawings
[0024] Figure 1 is the attenuated total reflection infrared spectrum of the all-solid-state ion-conductive elastomer prepared in Example 1.
[0025] Figure 2 is the scanning electron micrograph of the all-solid-state ion-conductive elastomer prepared in Example 1.
[0026] Figure 3 is the cyclic tensile stress-strain curve of the all-solid-state ion-conductive elastomer prepared in Example 1.
[0027] Figure 4 is the cyclic stress-strain curve of the all-solid-state ion-conductive elastomer prepared in Example 1 under different strains. Detailed Embodiments
[0028] To further understand the present invention, the preferred experimental schemes of the present invention are described below in conjunction with embodiments. However, it should be understood that these descriptions are only for further explaining the features and advantages of the present invention, rather than limiting the claims of the present invention.
[0029] (I) Photoinitiated Polymerization
[0030] Example 1 PIL-co-HEA elastomer with a monomer molar ratio of 10:1
[0031] Taking the synthesis of an ion-conductive elastomer with a molar ratio of 1-vinyl-3-hydroxyethylimidazolium bis(trifluoromethanesulfonyl)imide ([HEVIm][TFSI]) monomer to hydroxyethyl acrylate (HEA) monomer of 10:1 as an example. [HEVIm][TFSI] monomer (8.3872 g, 0.02 mol), HEA monomer (0.2324 g, 0.002 mol), and 0.4309 g of 2-hydroxy-2-methyl-1-phenyl-1-propanone photoinitiator (equivalent to 5.0 wt% of the total monomer mass) were ultrasonically dispersed at room temperature and mixed evenly to obtain a transparent homogeneous precursor solution. The precursor solution was poured into a glass mold and polymerized by ultraviolet light irradiation (ultraviolet light with a wavelength of 365 nm and a power of 10 W for 1 h) to obtain a fully solid-state ion-conductive elastomer. After polymerization, obvious changes occurred in the infrared spectrum, and the characteristic peak originally belonging to the vinyl C═C completely disappeared (as shown in -1 ). The morphology of the fully solid-state ion-conductive elastomer was characterized by scanning, and the results showed that the surface of the fully solid-state ion-conductive elastomer presented uniform wrinkles, indicating that the fully solid-state ion-conductive elastomer had no phase separation and presented a homogeneous structure (as shown in Figure 1 ). Subsequently, the fatigue resistance of the fully solid-state ion-conductive elastomer was characterized by cyclic stretching. After 15 cycles of cyclic stretching and with the increase of strain, the material could still recover. This shows that the material not only has excellent fatigue resistance but also maintains good resilience and toughness with the increase of strain (as shown in Figure 2 ). Figure 3 and 4 ).
[0032] Example 2 PIL-co-HEA elastomer with a monomer molar ratio of 5:1
[0033] Taking the synthesis of an ion-conductive elastomer with a molar ratio of 1-vinyl-3-hydroxyethylimidazolium bis(trifluoromethanesulfonyl)imide ([HEVIm][TFSI]) monomer to hydroxyethyl acrylate (HEA) monomer of 5:1 as an example. [HEVIm][TFSI] monomer (4.1936 g, 0.01 mol), HEA monomer (0.2324 g, 0.002 mol), and 0.2213 g of 2-hydroxy-2-methyl-1-phenyl-1-propanone photoinitiator (equivalent to 5.0 wt% of the total monomer mass) were ultrasonically dispersed at room temperature and mixed evenly to obtain a transparent homogeneous precursor solution. The precursor solution was poured into a glass mold and polymerized by ultraviolet light irradiation (ultraviolet light with a wavelength of 365 nm and a power of 10 W for 1 h) to obtain a fully solid-state ion-conductive elastomer.
[0034] Example 3 PIL-co-HEA elastomer with a monomer molar ratio of 1:5
[0035] Taking the synthesis of an ion-conductive elastomer with a molar ratio of 1-vinyl-3-hydroxyethylimidazolium bis(trifluoromethylsulfonyl)imide ([HEVIm][TFSI]) monomer to 2-hydroxyethyl acrylate (HEA) monomer of 1:5 as an example. The [HEVIm][TFSI] monomer (0.4191 g, 0.001 mol), HEA monomer (0.5806 g, 0.005 mol), and 0.0499 g of 2-hydroxy-2-methyl-1-phenyl-1-propanone photoinitiator (equivalent to 5.0 wt% of the total monomer mass) were ultrasonically dispersed at room temperature, mixed evenly to obtain a transparent homogeneous precursor solution. The precursor solution was poured into a glass mold and induced to polymerize by ultraviolet light irradiation (ultraviolet light with a wavelength of 365 nm and a power of 10 W for 1 h) to obtain a fully solid-state ion-conductive elastomer.
[0036] Example 4 PIL-co-HEA elastomer with a monomer molar ratio of 1:10
[0037] Taking the synthesis of an ion-conductive elastomer with a molar ratio of 1-vinyl-3-hydroxyethylimidazolium bis(trifluoromethylsulfonyl)imide ([HEVIm][TFSI]) monomer to 2-hydroxyethyl acrylate (HEA) monomer of 1:10 as an example. The [HEVIm][TFSI] monomer (0.4191 g, 0.001 mol), HEA monomer (1.1612 g, 0.010 mol), and 0.0791 g of 2-hydroxy-2-methyl-1-phenyl-1-propanone photoinitiator (equivalent to 5.0 wt% of the total monomer mass) were ultrasonically dispersed at room temperature, mixed evenly to obtain a transparent homogeneous precursor solution. The precursor solution was poured into a glass mold and induced to polymerize by ultraviolet light irradiation (ultraviolet light with a wavelength of 365 nm and a power of 10 W for 1 h) to obtain a fully solid-state ion-conductive elastomer.
[0038] Example 5 PIL-co-HBA elastomer with a monomer molar ratio of 1:10
[0039] Taking the synthesis of an ion-conductive elastomer with a molar ratio of 1-vinyl-3-hydroxybutylimidazolium bis(trifluoromethylsulfonyl)imide ([HBVIm][TFSI]) monomer to 2-hydroxybutyl acrylate (HBA) monomer of 1:10 as an example. The [HBVIm][TFSI] monomer (0.4474 g, 0.001 mol), HBA monomer (1.4417 g, 0.010 mol), and 0.0945 g of 2-hydroxy-2-methyl-1-phenyl-1-propanone photoinitiator (equivalent to 5.0 wt% of the total monomer mass) were ultrasonically dispersed at room temperature, mixed evenly to obtain a transparent homogeneous precursor solution. The precursor solution was poured into a glass mold and induced to polymerize by ultraviolet light irradiation (ultraviolet light with a wavelength of 365 nm and a power of 10 W for 1 h) to obtain a fully solid-state ion-conductive elastomer.
[0040] Example 6 PIL-co-MEA Elastomer with a Monomer Molar Ratio of 1:10
[0041] Take the synthesis of an ion-conductive elastomer with a molar ratio of 1-vinyl-3-hydroxyhexylimidazolium bis(trifluoromethylsulfonyl)imide ([HHVIm][TFSI]) monomer to 2-methoxyethyl acrylate (MEA) monomer of 1:10 as an example. The [HHVIm][TFSI] monomer (0.4754 g, 0.001 mol), MEA monomer (1.3014 g, 0.010 mol), and 0.0888 g of 2-hydroxy-2-methyl-1-phenyl-1-propanone photoinitiator (equivalent to 5.0 wt% of the total monomer mass) were ultrasonically dispersed at room temperature and mixed evenly to obtain a transparent homogeneous precursor solution. The precursor solution was poured into a glass mold and polymerized by ultraviolet light irradiation (irradiated with a 365 nm wavelength and 10 W power ultraviolet lamp for 1 h) to obtain a fully solid-state ion-conductive elastomer.
[0042] (II) In-situ Radical Polymerization Method
[0043] Example 7 PIL-co-HEA Elastomer with a Monomer Molar Ratio of 10:1
[0044] Take the synthesis of an ion-conductive elastomer with a molar ratio of 1-vinyl-3-hydroxyethylimidazolium bis(trifluoromethylsulfonyl)imide ([HEVIm][TFSI]) monomer to 2-hydroxyethyl acrylate (HEA) monomer of 10:1 as an example. Under an inert atmosphere, the [HEVIm][TFSI] monomer (8.3872 g, 0.02 mol), HEA monomer (0.2324 g, 0.002 mol), and 0.4309 g of azobisisobutyronitrile radical initiator (equivalent to 5.0 wt% of the total monomer mass) were added to a single-neck round-bottom flask, an appropriate amount of ethyl acetate was added, and the mixture was stirred at room temperature for 20 min to obtain a homogeneous precursor solution. A polymerization cross-linking reaction was carried out at 70 °C, and the organic solvent was removed by vacuum drying to obtain a fully solid-state ion-conductive elastomer.
[0045] Example 8 PIL-co-HEA Elastomer with a Monomer Molar Ratio of 5:1
[0046] Taking the synthesis of an ion-conductive elastomer with a molar ratio of 1-vinyl-3-hydroxyethylimidazolium bis(trifluoromethylsulfonyl)imide ([HEVIm][TFSI]) monomer to 2-hydroxyethyl acrylate (HEA) monomer of 5:1 as an example. Under an inert atmosphere, [HEVIm][TFSI] monomer (4.1936 g, 0.01 mol), HEA monomer (0.2324 g, 0.002 mol), and 0.2213 g of azobisisobutyronitrile free radical initiator (equivalent to 5.0 wt% of the total monomer mass) were added to a single-neck round-bottom flask, an appropriate amount of ethyl acetate was added, and the mixture was stirred at room temperature for 20 min to obtain a homogeneous precursor solution. A polymerization cross-linking reaction was carried out at 70 °C, and the organic solvent was removed by vacuum drying to obtain a fully solid-state ion-conductive elastomer.
[0047] Example 9 PIL-co-HEA elastomer with a monomer molar ratio of 1:5
[0048] Taking the synthesis of an ion-conductive elastomer with a molar ratio of 1-vinyl-3-hydroxyethylimidazolium bis(trifluoromethylsulfonyl)imide ([HEVIm][TFSI]) monomer to 2-hydroxyethyl acrylate (HEA) monomer of 1:5 as an example. Under an inert atmosphere, [HEVIm][TFSI] monomer (0.4191 g, 0.001 mol), HEA monomer (0.5806 g, 0.005 mol), and 0.0499 g of azobisisobutyronitrile free radical initiator (equivalent to 5.0 wt% of the total monomer mass) were added to a single-neck round-bottom flask, an appropriate amount of ethyl acetate was added, and the mixture was stirred at room temperature for 20 min to obtain a homogeneous precursor solution. A polymerization cross-linking reaction was carried out at 70 °C, and the organic solvent was removed by vacuum drying to obtain a fully solid-state ion-conductive elastomer.
[0049] Example 10 PIL-co-HEA elastomer with a monomer molar ratio of 1:10
[0050] Taking the synthesis of an ion-conductive elastomer with a molar ratio of 1-vinyl-3-hydroxyethylimidazolium bis(trifluoromethylsulfonyl)imide ([HEVIm][TFSI]) monomer to 2-hydroxyethyl acrylate (HEA) monomer of 1:10 as an example. Under an inert atmosphere, [HEVIm][TFSI] monomer (0.4191 g, 0.001 mol), HEA monomer (1.1612 g, 0.010 mol), and 0.0791 g of azobisisobutyronitrile free radical initiator (equivalent to 5.0 wt% of the total monomer mass) were added to a single-neck round-bottom flask, an appropriate amount of ethyl acetate was added, and the mixture was stirred at room temperature for 20 min to obtain a homogeneous precursor solution. A polymerization cross-linking reaction was carried out at 70 °C, and the organic solvent was removed by vacuum drying to obtain a fully solid-state ion-conductive elastomer.
[0051] Example 11 PIL-co-HBA elastomer with a monomer molar ratio of 1:10
[0052] Taking the synthesis of an ion-conductive elastomer with a molar ratio of 1-vinyl-3-hydroxybutylimidazolium bis(trifluoromethanesulfonyl)imide ([HBVIm][TFSI]) monomer to hydroxybutyl acrylate (HBA) monomer of 1:10 as an example. Under an inert atmosphere, [HBVIm][TFSI] monomer (0.4474 g, 0.001 mol), HBA monomer (1.4417 g, 0.010 mol), and 0.0945 g of azobisisobutyronitrile free radical initiator (equivalent to 5.0 wt% of the total monomer mass) were added to a single-neck round-bottom flask, an appropriate amount of ethyl acetate was added, and the mixture was stirred at room temperature for 20 min to obtain a homogeneous precursor solution. A polymerization cross-linking reaction was carried out at 70 °C, and the organic solvent was removed by vacuum drying to obtain a fully solid-state ion-conductive elastomer.
[0053] Example 12 PIL-co-MEA elastomer with a monomer molar ratio of 1:10
[0054] Taking the synthesis of an ion-conductive elastomer with a molar ratio of 1-vinyl-3-hydroxyhexylimidazolium bis(trifluoromethanesulfonyl)imide ([HHVIm][TFSI]) monomer to 2-methoxyethyl acrylate (MEA) monomer of 1:10 as an example. Under an inert atmosphere, [HHVIm][TFSI] monomer (0.4754 g, 0.001 mol), MEA monomer (1.3014 g, 0.010 mol), and 0.0888 g of azobisisobutyronitrile free radical initiator (equivalent to 5.0 wt% of the total monomer mass) were added to a single-neck round-bottom flask, an appropriate amount of ethyl acetate was added, and the mixture was stirred at room temperature for 20 min to obtain a homogeneous precursor solution. A polymerization cross-linking reaction was carried out at 70 °C, and the organic solvent was removed by vacuum drying to obtain a fully solid-state ion-conductive elastomer.
[0055] (III) Characterization
[0056] Figure 1 is the attenuated total reflection infrared spectrum of the fully solid-state ion-conductive elastomer prepared in Example 1. It can be seen from the figure that the stretching vibration peak attributed to the C═C of the monomer disappears at 1640 cm -1 −1, indicating that almost all the monomers have undergone polymerization reactions to form the target poly(ionic liquid)-based conductive elastomer.
[0057] Figure 2 is the scanning electron microscopy image of the fully solid-state ion-conductive elastomer prepared in Example 1. It can be seen from the figure that the surface morphology of the synthesized ion-conductive elastomer is in a wrinkled form and no phase separation phenomenon appears.
[0058] Figure 3It is the cyclic tensile stress-strain curve diagram of the all-solid-state ion-conductive elastomer prepared in Example 1. As can be seen from the figure, the synthesized all-solid-state ion-conductive elastomer was subjected to 15 loading-unloading tensile cycles at 100% deformation, and obvious hysteresis phenomenon appeared in the curve, indicating that the elastomer dissipates the generated energy through the breakage of reversible supramolecular forces during the stretching process, and this reversible supramolecular force cannot be restored immediately. With the increase of the number of cycles, the dissipated energy remains basically unchanged, indicating that the breakage-reconstruction of the reversible non-covalent bonds of the elastomer tends to be stable.
[0059] Figure 4 It is the cyclic stress-strain curve diagram of the all-solid-state ion-conductive elastomer prepared in Example 1 under different strains. As can be seen from the figure, the elastomer shows a large hysteresis loop, indicating that the elastomer can effectively dissipate energy through the breakage of dynamic non-covalent bonds. In addition, with the increase of the cyclic tensile strain, the area of the hysteresis loop increases significantly. When the cyclic strain is 250%, no obvious plastic deformation is observed, indicating that the elastomer has good resilience performance.
Claims
1. A fully solid-state ion-conducting elastomer based on dynamic supramolecular interactions, characterized in that, The all-solid-state ion-conductive elastomer is prepared by a photoinitiated polymerization method or an in-situ radical polymerization method from a hydroxylated ionic liquid monomer and a hydroxylated acrylate monomer in a molar ratio of 1:100 to 100:
1.
2. The all-solid-state ion-conductive elastomer based on dynamic supramolecular interactions according to claim 1, wherein The chemical structure of the hydroxylated ionic liquid monomer is any one of those shown in (Ⅰ): Among them, X1 - is TFSI - , SbF6 - , CF3SO3 - , CF3COO - , FSI - , N(C2F5SO2)2 - , CH3SO3 - ; n represents the carbon chain length of the ionic liquid monomer, and the value range is 1 to 15.
3. The all-solid-state ion-conductive elastomer based on dynamic supramolecular forces according to claim 1, wherein The chemical structure of the hydroxylated acrylate monomer is any one of those shown in (Ⅱ), (Ⅲ), and (Ⅳ):
4. A method for preparing an all-solid-state ion-conducting elastomer based on dynamic supramolecular interactions according to any one of claims 1-3, characterized in that, It includes the following steps: ultrasonically disperse the hydroxylated ionic liquid monomer, hydroxylated acrylate monomer, and photoinitiator at room temperature, mix them evenly to obtain a transparent homogeneous precursor solution, pour the precursor solution into a mold, and induce polymerization by ultraviolet light irradiation. Irradiate with ultraviolet light of wavelength 365 nm and power 10 W for 10 min to 1 h to obtain the all-solid-state ion-conductive elastomer.
5. The preparation method according to claim 4, characterized in that The photoinitiator is any one of 2-hydroxy-2-methyl-1-phenyl-1-propanone, 2-methyl-2-(4-morpholinyl)-1-[4-(methylthio)phenyl]-1-propanone, 2-hydroxy-2-methyl-1-[4-(2-hydroxyethoxy)phenyl]-1-propanone, 2-hydroxy-2-methyl-1-[4-(2-hydroxyethoxy)phenyl]-1-propanone, 2,4,6-trimethylbenzoyl-diphenylphosphine oxide.
6. The preparation method according to claim 4, characterized in that, The mass of the photoinitiator is 1% to 5% of the total mass of the hydroxylated ionic liquid monomer and hydroxylated acrylate monomer.
7. The preparation method according to claim 4, characterized in that, The mold material is any one of polytetrafluoroethylene, glass, silica gel, and ceramic.
8. A method for preparing an all-solid-state ion-conductive elastomer based on dynamic supramolecular interactions according to any one of claims 1 to 3, characterized in that, It includes the following steps: Under an inert atmosphere, add the hydroxylated ionic liquid monomer, hydroxylated acrylate monomer, and radical initiator into a single-neck round-bottom flask, add an organic solvent with a boiling point of 80 to 150 °C, stir at room temperature for 0.1 to 1 h to obtain a homogeneous precursor solution, carry out a polymerization cross-linking reaction at 40 to 80 °C, and remove the organic solvent by vacuum drying to obtain the all-solid-state ion-conductive elastomer.
9. The preparation method according to claim 8, characterized in that, The radical initiator is any one of azobisisobutyronitrile, peroxydiacyl, and persulfate.
10. Application of an all-solid-state ion-conductive elastomer based on dynamic supramolecular forces according to any one of claims 1-3 in flexible sensing materials.