CN110204850B - Block copolymer thermoplastic dielectric elastomer film and dielectric driver thereof - Google Patents
Block copolymer thermoplastic dielectric elastomer film and dielectric driver thereof Download PDFInfo
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- 229920002595 Dielectric elastomer Polymers 0.000 title claims abstract description 90
- 229920001400 block copolymer Polymers 0.000 title claims abstract description 30
- 229920001169 thermoplastic Polymers 0.000 title claims abstract description 30
- 239000004416 thermosoftening plastic Substances 0.000 title claims abstract description 30
- 229920001577 copolymer Polymers 0.000 claims abstract description 5
- 229920001485 poly(butyl acrylate) polymer Polymers 0.000 claims description 12
- 238000000034 method Methods 0.000 claims description 10
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 9
- SOGAXMICEFXMKE-UHFFFAOYSA-N Butylmethacrylate Chemical compound CCCCOC(=O)C(C)=C SOGAXMICEFXMKE-UHFFFAOYSA-N 0.000 claims description 8
- 229920001519 homopolymer Polymers 0.000 claims description 8
- PPBRXRYQALVLMV-UHFFFAOYSA-N Styrene Chemical compound C=CC1=CC=CC=C1 PPBRXRYQALVLMV-UHFFFAOYSA-N 0.000 claims description 6
- 229910021393 carbon nanotube Inorganic materials 0.000 claims description 5
- 239000002041 carbon nanotube Substances 0.000 claims description 5
- JIGUQPWFLRLWPJ-UHFFFAOYSA-N Ethyl acrylate Chemical compound CCOC(=O)C=C JIGUQPWFLRLWPJ-UHFFFAOYSA-N 0.000 claims description 4
- 230000009477 glass transition Effects 0.000 claims description 4
- PNJWIWWMYCMZRO-UHFFFAOYSA-N pent‐4‐en‐2‐one Natural products CC(=O)CC=C PNJWIWWMYCMZRO-UHFFFAOYSA-N 0.000 claims description 4
- GOXQRTZXKQZDDN-UHFFFAOYSA-N 2-Ethylhexyl acrylate Chemical compound CCCCC(CC)COC(=O)C=C GOXQRTZXKQZDDN-UHFFFAOYSA-N 0.000 claims description 3
- DXPPIEDUBFUSEZ-UHFFFAOYSA-N 6-methylheptyl prop-2-enoate Chemical compound CC(C)CCCCCOC(=O)C=C DXPPIEDUBFUSEZ-UHFFFAOYSA-N 0.000 claims description 3
- CQEYYJKEWSMYFG-UHFFFAOYSA-N butyl acrylate Chemical group CCCCOC(=O)C=C CQEYYJKEWSMYFG-UHFFFAOYSA-N 0.000 claims description 3
- ISXSCDLOGDJUNJ-UHFFFAOYSA-N tert-butyl prop-2-enoate Chemical compound CC(C)(C)OC(=O)C=C ISXSCDLOGDJUNJ-UHFFFAOYSA-N 0.000 claims description 3
- RUMACXVDVNRZJZ-UHFFFAOYSA-N 2-methylpropyl 2-methylprop-2-enoate Chemical compound CC(C)COC(=O)C(C)=C RUMACXVDVNRZJZ-UHFFFAOYSA-N 0.000 claims description 2
- 229910052799 carbon Inorganic materials 0.000 claims description 2
- 239000002131 composite material Substances 0.000 claims description 2
- 239000000017 hydrogel Substances 0.000 claims description 2
- 239000000178 monomer Substances 0.000 claims description 2
- 229920001490 poly(butyl methacrylate) polymer Polymers 0.000 claims description 2
- 229920000205 poly(isobutyl methacrylate) Polymers 0.000 claims description 2
- 229920000642 polymer Polymers 0.000 claims description 2
- 239000000758 substrate Substances 0.000 claims description 2
- 230000015556 catabolic process Effects 0.000 abstract description 24
- 238000005516 engineering process Methods 0.000 abstract description 2
- 239000010408 film Substances 0.000 description 109
- 229920002725 thermoplastic elastomer Polymers 0.000 description 16
- 239000004793 Polystyrene Substances 0.000 description 8
- 229920002223 polystyrene Polymers 0.000 description 8
- 239000000463 material Substances 0.000 description 7
- 230000002040 relaxant effect Effects 0.000 description 7
- 230000000694 effects Effects 0.000 description 4
- 239000011248 coating agent Substances 0.000 description 3
- 238000000576 coating method Methods 0.000 description 3
- 230000037303 wrinkles Effects 0.000 description 3
- VVQNEPGJFQJSBK-UHFFFAOYSA-N Methyl methacrylate Chemical compound COC(=O)C(C)=C VVQNEPGJFQJSBK-UHFFFAOYSA-N 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 239000000835 fiber Substances 0.000 description 2
- 230000000737 periodic effect Effects 0.000 description 2
- 238000002360 preparation method Methods 0.000 description 2
- 238000007790 scraping Methods 0.000 description 2
- 239000010409 thin film Substances 0.000 description 2
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 230000005684 electric field Effects 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 238000001125 extrusion Methods 0.000 description 1
- 238000011056 performance test Methods 0.000 description 1
- 238000004528 spin coating Methods 0.000 description 1
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
- B29C—SHAPING OR JOINING OF PLASTICS; SHAPING OF MATERIAL IN A PLASTIC STATE, NOT OTHERWISE PROVIDED FOR; AFTER-TREATMENT OF THE SHAPED PRODUCTS, e.g. REPAIRING
- B29C55/00—Shaping by stretching, e.g. drawing through a die; Apparatus therefor
- B29C55/02—Shaping by stretching, e.g. drawing through a die; Apparatus therefor of plates or sheets
- B29C55/10—Shaping by stretching, e.g. drawing through a die; Apparatus therefor of plates or sheets multiaxial
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- C—CHEMISTRY; METALLURGY
- C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
- C08J—WORKING-UP; GENERAL PROCESSES OF COMPOUNDING; AFTER-TREATMENT NOT COVERED BY SUBCLASSES C08B, C08C, C08F, C08G or C08H
- C08J5/00—Manufacture of articles or shaped materials containing macromolecular substances
- C08J5/18—Manufacture of films or sheets
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
- B29L—INDEXING SCHEME ASSOCIATED WITH SUBCLASS B29C, RELATING TO PARTICULAR ARTICLES
- B29L2007/00—Flat articles, e.g. films or sheets
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- C—CHEMISTRY; METALLURGY
- C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
- C08J—WORKING-UP; GENERAL PROCESSES OF COMPOUNDING; AFTER-TREATMENT NOT COVERED BY SUBCLASSES C08B, C08C, C08F, C08G or C08H
- C08J2353/00—Characterised by the use of block copolymers containing at least one sequence of a polymer obtained by reactions only involving carbon-to-carbon unsaturated bonds; Derivatives of such polymers
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- Chemical Kinetics & Catalysis (AREA)
- Medicinal Chemistry (AREA)
- Polymers & Plastics (AREA)
- Organic Chemistry (AREA)
- Manufacture Of Macromolecular Shaped Articles (AREA)
- Shaping By String And By Release Of Stress In Plastics And The Like (AREA)
Abstract
The invention discloses a block copolymer thermoplastic dielectric elastomer film and a dielectric driver thereof. The invention adopts the pre-stretching thermal relaxation technology to the segmented copolymer thermoplastic dielectric elastomer film, can obtain the dielectric elastomer which is free from frame fixation and self-supporting and has thinner thickness, simultaneously improves the driving performance, reduces the driving voltage of the dielectric elastomer, improves the breakdown field strength of the dielectric elastomer and improves the area deformation of the dielectric elastomer. Meanwhile, the dielectric elastomer with anisotropic mechanical property can be obtained through asymmetric pre-stretching thermal relaxation treatment, and the dielectric elastomer can be used for a driver with anisotropic driving property when the driver is driven without a frame, and has important significance in preparing anisotropic flexible drivers and flexible robots from the dielectric elastomer.
Description
Technical Field
The invention relates to the field of thermoplastic dielectric elastomers, in particular to a segmented copolymer thermoplastic dielectric elastomer film and a dielectric driver thereof.
Background
The driving mechanism of the dielectric elastomer driver is that flexible electrodes are coated on the upper surface and the lower surface of a dielectric elastomer film, and certain voltage is applied. Because the voltages of the upper flexible electrode and the lower flexible electrode are different, an electric field is formed, so that Maxwell stress is generated to extrude the dielectric elastomer film, the thickness of the dielectric elastomer film is reduced, the in-plane expansion is realized, and the driving deformation is generated. However, the driving voltage of a general dielectric elastomer driver is higher, and the method of reducing the driving voltage mainly includes reducing the elastic modulus of the material, increasing the dielectric constant of the material or reducing the thickness of the film, wherein the reduction of the thickness of the film of the material is most obvious for reducing the driving voltage of the dielectric elastomer film.
However, the driving performance of the dielectric elastomer film for dielectric driving after the thickness of the dielectric elastomer film is reduced generally decreases, mainly because the dielectric elastomer film is more influenced by the defects of the film, the more influenced by the rigidity of the electrode, and the more influenced by the edge of the electrode. This results in a decrease in the thickness of the dielectric elastomer film, which also deteriorates the drive performance. For this reason, it becomes important how to improve the driving performance of the dielectric elastomer ultrathin film. Meanwhile, in the current methods for mainly preparing thin films such as solution film scraping, solution spin coating, melt extrusion and the like, the preparation of thick films with uniform high quality is easier than the preparation of ultrathin films with uniform high quality.
Meanwhile, in-plane expansion generated by electric drive is uniform expansion deformation, and anisotropic drive deformation is difficult to realize, and the method for realizing anisotropic drive generally realizes anisotropic drive by using a fixed frame to keep dielectric elastomer films with different pre-stretching ratios; the method is particularly important for truly realizing the anisotropic driving deformation of the self-supporting frameless fixed dielectric elastomer film, and has wide application prospect in the fields of anisotropic drivers and flexible robots. The current methods for realizing anisotropic driving mainly include adding anisotropic fibers (adv. mater,2015,27, 6814-.
The invention prepares the even block copolymer dielectric elastomer thick film by solution film scraping, and the dielectric elastomer thin film with thinner thickness can be obtained by pre-stretching thermal relaxation treatment. The uniform high-quality ultrathin film can be prepared by equal multi-axis symmetrical pre-stretching thermal relaxation treatment, and the Weber electrical breakdown test shows that the larger the pre-stretching degree is, the higher the electrical breakdown field intensity of the dielectric elastomer film obtained after thermal relaxation is, the better the driving performance is correspondingly and the larger the driving deformation is. The dielectric elastomer film which is self-supporting and can realize anisotropic drive without frame fixation can be obtained by carrying out anisotropic prestretching thermal relaxation treatment on the thermoplastic dielectric elastomer film. In contrast to the addition of anisotropic fibers to dielectric elastomers or the introduction of anisotropic electrodes or the introduction of crystalline units in dielectric elastomers, the present invention provides anisotropic electrically driven deformations by changing the stacking morphology of the hard segments in the thermoplastic elastomer, increasing its aspect ratio and achieving a certain orientation.
Disclosure of Invention
The present invention is directed to overcoming the disadvantages of the prior art and providing a block copolymer thermoplastic dielectric elastomer film and a dielectric actuator thereof. When the thermoplastic dielectric elastomer film subjected to pre-stretching thermal relaxation treatment is applied to a dielectric actuator, the thermoplastic dielectric elastomer film has higher driving performance, and simultaneously, the self-supporting anisotropic dielectric actuator without frame fixation can be obtained after thermal relaxation by controlling the pre-stretching mode and the pre-stretching degree.
The purpose of the invention is realized by the following technical scheme: a block copolymer thermoplastic dielectric elastomer film prepared by the following method: first, a block copolymer thermoplastic dielectric elastomer is uniaxially prestretched, equi-biaxial prestretched, equi-multiaxial prestretched, or biaxially asymmetric prestretched. Wherein the uniaxial prestretching degree is 1-20 times of the initial area; the degree of equal biaxial pre-stretching and equal multiaxial pre-stretching is 1-30 times of the initial area, and the stretching ratio of biaxial asymmetric pre-stretching is 1-400: 20; then, under the condition of keeping the pre-stretching, placing the pre-stretched block copolymer thermoplastic elastomer at the temperature of 50-150 ℃ for thermal relaxation for 0.5-20 h to obtain a block copolymer thermoplastic dielectric elastomer film; the structural general formula of the block copolymer thermoplastic dielectric elastomer is A-B- (AB)n-A, n are positive integers. Wherein A is selected from homopolymers of styrene, homopolymers of methyl methacrylate, and copolymers of styrene and methyl methacrylate; b is a butyl acrylate homopolymer, a n-butyl methacrylate homopolymer, an isobutyl methacrylate homopolymer, a tert-butyl acrylate homopolymer, a 2-ethylhexyl acrylate homopolymer, an isooctyl acrylate homopolymer, an ethyl acrylate homopolymer or a copolymer of at least two monomers of butyl acrylate, n-butyl methacrylate, isobutyl methacrylate, tert-butyl acrylate, 2-ethylhexyl acrylate, isooctyl acrylate and ethyl acrylate.
Further, the pre-stretched condition is maintained by fixing the block copolymer thermoplastic elastomer to the frame or the non-stick substrate.
Further, in the block copolymer thermoplastic elastomer, A is a hard segment, and B is a soft segment; the glass transition temperature of the hard segment is more than 50 ℃, and the glass transition temperature of the soft segment is less than-10 ℃.
Further, the total molecular weight of the block copolymer thermoplastic elastomer is 5-50 ten thousand, the number average molecular weight of the hard segment is 0.5-5 ten thousand, the number average molecular weight of the soft segment is 5-40 ten thousand, and the soft segment accounts for 60% -95% of the total weight of the block copolymer thermoplastic elastomer.
A dielectric driver containing the block copolymer thermoplastic dielectric elastomer film is composed of an upper electrode, the block copolymer thermoplastic dielectric elastomer film and a lower electrode which are connected in sequence.
Further, the upper electrode and the lower electrode are flexible electrodes selected from carbon nanotubes, carbon paste, hydrogel, carbon powder and polymer composite materials.
The invention has the beneficial effects that: the invention applies the thermoplastic elastomer film obtained by the pre-stretching thermal relaxation treatment to the field of dielectric actuators, and can obtain the dielectric elastomer film with better driving performance or anisotropy by controlling the pre-stretching mode and the pre-stretching degree, thereby improving better material selection for the application of the dielectric elastomer actuators. The method comprises the following specific steps:
1. the appearance of the hard segment part in the initial film of the thermoplastic elastomer film subjected to pre-stretching and thermal relaxation is obviously changed, and the length-diameter ratio is increased. The greater the degree of pretension, the greater the aspect ratio.
2. The resulting actuators of dielectric elastomeric films have significant anisotropy through uniaxial prestretching or biaxial asymmetric prestretching thermal relaxation techniques. When the uniaxial prestretching heat relaxation dielectric elastomer driver is driven by voltage, the uniaxial prestretching heat relaxation dielectric elastomer driver generates small deformation parallel to the stretching direction and large deformation perpendicular to the stretching direction, and periodic folds with certain wavelength are generated perpendicular to the stretching direction; the greater the degree of pretension, the greater the number of wrinkle waves. When the biaxial asymmetric pre-stretching thermal relaxation dielectric elastomer driver is driven by applying voltage, the biaxial asymmetric pre-stretching thermal relaxation dielectric elastomer driver generates smaller deformation when being stretched to a larger degree in a direction perpendicular to the stretching direction and generates larger deformation when being stretched to a smaller degree in a direction parallel to the stretching direction, thereby generating asymmetric deformation.
3. The dielectric elastomer film with more uniform thickness can be prepared from the thick film by the equal multi-axis pre-stretching thermal relaxation technology, and the driving voltage of the obtained dielectric elastomer film is driven within 0.05-5 KV. The breakdown field strength of the obtained dielectric elastomer film is increased to 1-5 times of the original breakdown field strength. Meanwhile, the driving performance of the dielectric elastomer driver is improved to 1-5 times of the original driving performance. Wherein the greater the degree of pretension, the better the driving properties after thermal relaxation.
Drawings
FIG. 1 is a failure probability distribution graph for analyzing the electrical breakdown field strength of a dielectric elastomer film based on a Weber distribution;
FIG. 2 is a probability density distribution graph for analyzing the electrical breakdown field strength of a dielectric elastomer film based on a Weber distribution;
FIG. 3 is a graph comparing the driving performance of dielectric elastomer films of the same thickness for a dielectric actuator;
FIG. 4 is a graph showing the electric driving effect of dielectric elastomer films with different degrees of uniaxial pre-stretching heat relaxation, wherein (a) is the electric driving effect of the initial film, (b) is the electric driving effect of the films after uniaxial 200% pre-stretching heat relaxation, and (c) is the electric driving effect of the films after uniaxial 400% pre-stretching heat relaxation.
Detailed Description
The following are specific examples of the present invention and further describe the technical solutions of the present invention, but the present invention is not limited to these examples.
Example 1: evaluation of electric breakdown field Strength of dielectric elastomer film after Iso 4-Axis Pre-stretching thermal relaxation based on polystyrene-Poly (n-butyl acrylate) -polystyrene (molecular weight: 1.5W-12W-1.5W) triblock thermoplastic elastomer film
Pre-stretching an initial film (the thickness is about 83 microns) of a polystyrene-poly (n-butyl acrylate) -polystyrene triblock thermoplastic elastomer to 2 times (the thickness is about 44 microns), 3 times (the thickness is about 26 microns) and about 7 times (the thickness is about 12 microns) of the area of the initial film by equal 4 axes respectively; under the condition of fixed prestretching, the material is placed at 115 ℃ for thermal relaxation for 10 hours and then cooled at normal temperature. The electric breakdown field intensity of the dielectric elastomer film is obtained by using the Weber distribution to compare the prestretching heat relaxation and the prestretching heat relaxation. It can be seen from fig. 1 and 2 that the greater the degree of pre-stretching of the film, the higher the electric breakdown field strength of the film obtained after thermal relaxation; after the film pre-stretched to about 2 times the area of the initial film is thermally relaxed, the electric breakdown field intensity is about 1.3 times of the initial film; after the film pre-stretched to about 3 times the area of the initial film is thermally relaxed, the electric breakdown field intensity is about 1.7 times of the initial film; after the film pre-stretched to about 7 times of the area of the initial film is thermally relaxed, the electric breakdown field intensity is about 2.2 times of that of the initial film; it can be seen that the greater the degree of pre-stretching of the film, the higher the electrical breakdown field strength of the resulting film after thermal relaxation.
In fig. 1 and 2, 1, initial film; 2, pre-stretching to 2 times of the area of the initial film, and thermally relaxing to obtain a dielectric elastomer film; 3, pre-stretching to about 3 times of the area of the initial film, and thermally relaxing to obtain a dielectric elastomer film; 4, pre-stretching to about 7 times of the area of the initial film, and thermally relaxing to obtain the dielectric elastomer film.
Example 2: drive performance test of dielectric elastomer film after equal 4-axis pre-stretching thermal relaxation based on polystyrene-poly (n-butyl acrylate) -polystyrene (molecular weight: 1.5W-12W-1.5W) triblock thermoplastic elastomer film
Pre-stretching an initial film (with the thickness of 200 microns, 100 microns, 50 microns, 25 microns and 12 microns respectively) of a polystyrene-poly (n-butyl acrylate) -polystyrene triblock thermoplastic elastomer to form a dielectric elastomer film with the thickness of 12 microns by equal 4 axes respectively; under the condition of fixed prestretching, the material is placed at 115 ℃ for thermal relaxation for 10 hours and then cooled at normal temperature. And then coating the same carbon nanotube flexible electrode on the upper and lower surfaces of the dielectric elastomer film for electric drive test. As shown in FIG. 3, the initial film thickness of 12 microns had an electrical breakdown voltage of about 450V, a breakdown field strength of about 42.8V/μm, and a maximum driven deformation of 11.7%; the initial film with the thickness of 25 microns is pre-stretched to 12 microns, the electric breakdown voltage after thermal relaxation is about 475V, the breakdown field strength is about 46.9V/mum, and the maximum driving deformation is 13.1 percent; the initial film with the thickness of 50 microns is pre-stretched to 12 microns, the electric breakdown voltage after thermal relaxation is about 500V, the breakdown field strength is about 49.4V/mum, and the maximum driving deformation is 12.4 percent; the initial film with the thickness of 100 microns is pre-stretched to 12 microns, the electric breakdown voltage after thermal relaxation is about 650V, the breakdown field strength is about 62.1V/mum, and the maximum driving deformation is 14.0 percent; an initial film having a thickness of 25 microns was pre-stretched to 12 microns, the electrical breakdown voltage after thermal relaxation was about 800V, the breakdown field strength was about 82.0V/. mu.m, and the maximum driven deformation was 22.4%.
In fig. 3, 1, initial film; 2, pre-stretching to 2 times of the area of the initial film, and thermally relaxing to obtain a dielectric elastomer film; 3, pre-stretching to about 4 times of the area of the initial film, and thermally relaxing to obtain a dielectric elastomer film; 4, pre-stretching to about 8 times of the area of the initial film, and thermally relaxing to obtain a dielectric elastomer film; 5, pre-stretching to about 16 times of the area of the initial film, and thermally relaxing to obtain the dielectric elastomer film.
Example 3: based on the anisotropic driving performance of a polystyrene-poly (n-butyl acrylate) -polystyrene (molecular weight: 1.5W-12W-1.5W) triblock thermoplastic elastomer film subjected to different degrees of uniaxial pre-stretching and thermal relaxation
Respectively pre-stretching an initial film of a polystyrene-poly (n-butyl acrylate) -polystyrene triblock thermoplastic elastomer to 2 times and 4 times of the length of the initial film by a single shaft; under the condition of fixed prestretching, the material is placed at 110 ℃ for thermal relaxation for 10 hours and then cooled at normal temperature. And then coating the same carbon nanotube flexible electrode on the upper and lower surfaces of the dielectric elastomer film for electric drive test. As shown in fig. 4, the self-supporting frameless electric driving generates anisotropic deformation, and the initial film without pre-stretching treatment (as shown in fig. 4 (a)) has no obvious anisotropic deformation when being deformed by applied voltage; when the dielectric elastomer film (shown in fig. 4 (b)) is uniaxially 2 times pre-stretched and thermally relaxed, the dielectric elastomer film is greatly deformed perpendicular to the stretching direction by electric driving, thereby causing periodic wrinkles; the heat-relaxed dielectric elastomer film was uniaxially pre-stretched 4 times (as shown in fig. 4 (c)), resulting in more wrinkles.
Example 4: based on the anisotropic driving performance of a three-block thermoplastic elastomer film of polystyrene-poly (n-butyl acrylate) -polystyrene (molecular weight: 1.5W-12W-1.5W) after biaxial asymmetric pre-stretching and thermal relaxation
The method comprises the following steps of (1) pre-stretching an initial film of a polystyrene-poly (n-butyl acrylate) -polystyrene triblock thermoplastic elastomer through biaxial asymmetric pre-stretching, wherein one side of the initial film is pre-stretched to be 2 times of the length of the initial film, and the other side of the initial film is pre-stretched to be 4 times of the length of the initial film; under the condition of fixed pre-stretching, the film is placed at 120 ℃ to be thermally relaxed for 9 hours and then cooled at normal temperature to obtain the self-supporting dielectric elastomer film without frame fixation. And then coating the same carbon nanotube flexible electrode on the upper and lower surfaces of the dielectric elastomer film for electric drive test. When the biaxial asymmetric pre-stretching thermal relaxation dielectric elastomer driver is driven by applying voltage, the biaxial asymmetric pre-stretching thermal relaxation dielectric elastomer driver generates small deformation when being stretched to a larger degree in a direction parallel to the stretching direction, and generates large deformation when being stretched to a smaller degree in a direction parallel to the stretching direction, thereby generating asymmetric deformation.
Claims (6)
1. A block copolymer thermoplastic dielectric elastomer film, characterized in that it is prepared by the following method: firstly, carrying out uniaxial prestretching, equibiaxial prestretching, equimultiaxial prestretching or biaxial asymmetric prestretching on the block copolymer thermoplastic dielectric elastomer; wherein the uniaxial prestretching degree is 1-20 times of the initial area; the degree of equal biaxial pre-stretching and equal multiaxial pre-stretching is 1-30 times of the initial area, and the stretching ratio of biaxial asymmetric pre-stretching is 1-400: 20; then, under the condition of keeping the pre-stretching, placing the pre-stretched block copolymer thermoplastic dielectric elastomer at the temperature of 50-150 ℃ for thermal relaxation for 0.5-20 h to obtain a block copolymer thermoplastic dielectric elastomer film; the structural general formula of the block copolymer thermoplastic dielectric elastomer is A-B-A; wherein A is selected from homopolymers of styrene; b is n-butyl acrylate homopolymer, n-butyl methacrylate homopolymer, isobutyl methacrylate homopolymer, tert-butyl acrylate homopolymer, 2-ethylhexyl acrylate homopolymer, ethyl acrylate homopolymer or copolymer of at least two monomers of butyl acrylate, n-butyl methacrylate, isobutyl methacrylate, isooctyl acrylate and ethyl acrylate.
2. The block copolymer thermoplastic dielectric elastomer film of claim 1, wherein the pre-stretched condition is maintained by fixing the block copolymer thermoplastic dielectric elastomer to the frame or the non-tacky substrate.
3. The block copolymer thermoplastic dielectric elastomer film as claimed in claim 1, wherein in the block copolymer thermoplastic dielectric elastomer, A is a hard segment and B is a soft segment; the glass transition temperature of the hard segment is more than 50 ℃, and the glass transition temperature of the soft segment is less than-10 ℃.
4. The block copolymer thermoplastic dielectric elastomer film as claimed in claim 3, wherein the total molecular weight of the block copolymer thermoplastic dielectric elastomer is 5 to 50 ten thousand, the number average molecular weight of the hard segment is 0.5 to 5 ten thousand, the number average molecular weight of the soft segment is 5 to 40 ten thousand, and the soft segment accounts for 60 to 95% of the total weight of the block copolymer thermoplastic dielectric elastomer.
5. A dielectric actuator comprising the block copolymer thermoplastic dielectric elastomer film of claim 1, wherein the dielectric actuator is comprised of an upper electrode, the block copolymer thermoplastic dielectric elastomer film and a lower electrode connected in series.
6. A dielectric driver according to claim 5, wherein the upper and lower electrodes are flexible electrodes selected from the group consisting of carbon nanotubes, carbon paste, hydrogel, carbon powder and polymer composites.
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