WO2020216179A1 - 一种用于微型发声装置的振膜和微型发声装置 - Google Patents

一种用于微型发声装置的振膜和微型发声装置 Download PDF

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Publication number
WO2020216179A1
WO2020216179A1 PCT/CN2020/085641 CN2020085641W WO2020216179A1 WO 2020216179 A1 WO2020216179 A1 WO 2020216179A1 CN 2020085641 W CN2020085641 W CN 2020085641W WO 2020216179 A1 WO2020216179 A1 WO 2020216179A1
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Prior art keywords
diaphragm
polyacrylate copolymer
parts
polyacrylate
copolymer
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PCT/CN2020/085641
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English (en)
French (fr)
Inventor
惠冰
凌风光
王婷
李春
刘春发
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歌尔股份有限公司
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Application filed by 歌尔股份有限公司 filed Critical 歌尔股份有限公司
Priority to KR1020217038425A priority Critical patent/KR20220005525A/ko
Priority to EP20794693.0A priority patent/EP3962109A4/en
Publication of WO2020216179A1 publication Critical patent/WO2020216179A1/zh

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    • H—ELECTRICITY
    • H04—ELECTRIC COMMUNICATION TECHNIQUE
    • H04R—LOUDSPEAKERS, MICROPHONES, GRAMOPHONE PICK-UPS OR LIKE ACOUSTIC ELECTROMECHANICAL TRANSDUCERS; DEAF-AID SETS; PUBLIC ADDRESS SYSTEMS
    • H04R7/00—Diaphragms for electromechanical transducers; Cones
    • H04R7/02—Diaphragms for electromechanical transducers; Cones characterised by the construction
    • H—ELECTRICITY
    • H04—ELECTRIC COMMUNICATION TECHNIQUE
    • H04R—LOUDSPEAKERS, MICROPHONES, GRAMOPHONE PICK-UPS OR LIKE ACOUSTIC ELECTROMECHANICAL TRANSDUCERS; DEAF-AID SETS; PUBLIC ADDRESS SYSTEMS
    • H04R7/00—Diaphragms for electromechanical transducers; Cones
    • H04R7/02—Diaphragms for electromechanical transducers; Cones characterised by the construction
    • H04R7/04—Plane diaphragms
    • H04R7/06—Plane diaphragms comprising a plurality of sections or layers
    • H04R7/10—Plane diaphragms comprising a plurality of sections or layers comprising superposed layers in contact
    • 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
    • C08J3/00—Processes of treating or compounding macromolecular substances
    • C08J3/24—Crosslinking, e.g. vulcanising, of macromolecules
    • H—ELECTRICITY
    • H04—ELECTRIC COMMUNICATION TECHNIQUE
    • H04R—LOUDSPEAKERS, MICROPHONES, GRAMOPHONE PICK-UPS OR LIKE ACOUSTIC ELECTROMECHANICAL TRANSDUCERS; DEAF-AID SETS; PUBLIC ADDRESS SYSTEMS
    • H04R9/00—Transducers of moving-coil, moving-strip, or moving-wire type
    • H04R9/02—Details
    • H—ELECTRICITY
    • H04—ELECTRIC COMMUNICATION TECHNIQUE
    • H04R—LOUDSPEAKERS, MICROPHONES, GRAMOPHONE PICK-UPS OR LIKE ACOUSTIC ELECTROMECHANICAL TRANSDUCERS; DEAF-AID SETS; PUBLIC ADDRESS SYSTEMS
    • H04R9/00—Transducers of moving-coil, moving-strip, or moving-wire type
    • H04R9/06—Loudspeakers
    • 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
    • C08J2333/00—Characterised by the use of homopolymers or copolymers of compounds having one or more unsaturated aliphatic radicals, each having only one carbon-to-carbon double bond, and only one being terminated by only one carboxyl radical, or of salts, anhydrides, esters, amides, imides, or nitriles thereof; Derivatives of such polymers
    • C08J2333/04—Characterised by the use of homopolymers or copolymers of compounds having one or more unsaturated aliphatic radicals, each having only one carbon-to-carbon double bond, and only one being terminated by only one carboxyl radical, or of salts, anhydrides, esters, amides, imides, or nitriles thereof; Derivatives of such polymers esters
    • C08J2333/06—Characterised by the use of homopolymers or copolymers of compounds having one or more unsaturated aliphatic radicals, each having only one carbon-to-carbon double bond, and only one being terminated by only one carboxyl radical, or of salts, anhydrides, esters, amides, imides, or nitriles thereof; Derivatives of such polymers esters of esters containing only carbon, hydrogen, and oxygen, the oxygen atom being present only as part of the carboxyl radical
    • C08J2333/08—Homopolymers or copolymers of acrylic acid esters
    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08K—Use of inorganic or non-macromolecular organic substances as compounding ingredients
    • C08K5/00—Use of organic ingredients
    • C08K5/0008—Organic ingredients according to more than one of the "one dot" groups of C08K5/01 - C08K5/59
    • C08K5/0016—Plasticisers
    • H—ELECTRICITY
    • H04—ELECTRIC COMMUNICATION TECHNIQUE
    • H04R—LOUDSPEAKERS, MICROPHONES, GRAMOPHONE PICK-UPS OR LIKE ACOUSTIC ELECTROMECHANICAL TRANSDUCERS; DEAF-AID SETS; PUBLIC ADDRESS SYSTEMS
    • H04R2307/00—Details of diaphragms or cones for electromechanical transducers, their suspension or their manufacture covered by H04R7/00 or H04R31/003, not provided for in any of its subgroups
    • H04R2307/025—Diaphragms comprising polymeric materials

Definitions

  • the technical field of electronic products of the present invention in particular, relates to a diaphragm of a miniature sounding device and a miniature sounding device.
  • Diaphragms used in sound devices are mostly multi-layer composite materials, such as engineering plastics such as PEEK, PAR, PEI, PI, elastomer materials such as TPU, TPEE, acrylic film, and silicone film.
  • silicone rubber has good thermal stability, good hydrophobic properties and excellent resilience performance. With the increase of high power, waterproof and high sound quality requirements, silicone rubber is gradually used to make diaphragms.
  • electronic devices need to be equipped with smaller and better-performance micro-sounding devices. This demand results in that the existing commonly used composite materials cannot meet the performance requirements.
  • An object of the present invention is to provide a new technical solution for the diaphragm of a miniature sounding device.
  • a diaphragm for a miniature sounding device.
  • the diaphragm is made of polyacrylate copolymer, and the polyacrylate copolymer is mixed with a plasticizer, and Plasticizers include aliphatic dibasic acid esters, phthalic acid esters, benzene polyacid esters, benzoic acid esters, polyol esters, chlorinated hydrocarbons, epoxy, citrate, polyester
  • Plasticizers include aliphatic dibasic acid esters, phthalic acid esters, benzene polyacid esters, benzoic acid esters, polyol esters, chlorinated hydrocarbons, epoxy, citrate, polyester
  • the glass transition temperature of the diaphragm is in the range of -70 to 0°C, and the diaphragm is configured such that the adhesion between the diaphragm and the adhesive layer is greater than 100g/25mm ( 180° peel).
  • the polyacrylate copolymer is made by cross-linking and polymerizing an alkyl acrylate as a polymerization main monomer with a cross-linking monomer, and the glass transition temperature of the diaphragm is in the range of -60 to 0°C.
  • the glass transition temperature of the diaphragm is in the range of -50°C to -20°C.
  • the mass parts of the polyacrylate copolymer itself is 100 parts, and the mass parts of the plasticizer itself is 1-13 parts.
  • the polyacrylate copolymer is mixed with a vulcanizing agent, the mass parts of the polyacrylate copolymer itself is 100 parts, and the mass parts of the vulcanizing agent itself is 0.5-5 parts.
  • the polyacrylate copolymer includes at least one of "ethylene-acrylate copolymer” and "ethylene-acrylate-carboxylic acid copolymer”.
  • the glass transition temperature of the diaphragm is in the range of -60°C to -20°C.
  • the mass parts of the polyacrylate copolymer itself is 100 parts, and the mass parts of the plasticizer itself is 1-10 parts.
  • the adhesive force between the diaphragm and the adhesive layer is greater than 200 g/25 mm (180° peeling).
  • the polyacrylate copolymer is mixed with an internal mold release agent, and the internal mold release agent includes stearic acid and stearate, stearylamine and alkyl phosphate, ⁇ -octadecyl At least one of the alkyl- ⁇ -hydroxy polyoxyethylene phosphates, the mass parts of the polyacrylate copolymer itself is 100 parts, and the mass parts of the internal mold release agent itself is 0.5-5 parts.
  • the internal mold release agent includes stearic acid and stearate, stearylamine and alkyl phosphate, ⁇ -octadecyl At least one of the alkyl- ⁇ -hydroxy polyoxyethylene phosphates, the mass parts of the polyacrylate copolymer itself is 100 parts, and the mass parts of the internal mold release agent itself is 0.5-5 parts.
  • the mass parts of the internal release agent itself is 1-3 parts.
  • the diaphragm is a single-layer diaphragm, and the single-layer diaphragm is composed of a polyacrylate copolymer film layer;
  • the diaphragm is a composite diaphragm
  • the composite diaphragm includes two, three, four, or five layers
  • the composite diaphragm includes at least one polyacrylate copolymer film layer.
  • the thickness of the polyacrylate copolymer film layer is 10-200 ⁇ m.
  • the thickness of the polyacrylate copolymer film layer is 30-120 ⁇ m.
  • the type of the adhesive layer includes one or more of epoxy, acrylic, silicone resin, polyester, polyurethane, vinyl acetate resin, phenol resin, and urea resin.
  • a miniature sounding device comprising a sounding device main body and the above-mentioned diaphragm, the diaphragm being arranged on the sounding device body, the diaphragm being configured to vibrate and produce sound .
  • the diaphragm has better acoustic performance and higher stability in use.
  • Figure 1 is a graph of the glass transition temperature and mechanical strength of the polyethylene block and polyacrylate block of the diaphragm provided by the present invention
  • 3 is a graph showing the influence of the amount of vulcanizing agent of the diaphragm provided by the present invention on the glass transition temperature and elongation at break;
  • Figure 5 is a graph of the relationship between the mixed amount of plasticizer in the diaphragm made of AEM polymer and the glass transition temperature and mechanical strength of the material provided by the present invention
  • Fig. 6 is a diagram of the relationship between the stress-strain curve of the diaphragm made of ACM polymer and the mixing fraction of carbon black provided by the present invention
  • Fig. 7 is a diagram of the relationship between the stress-strain curve of the diaphragm made of AEM polymer and the mixing fraction of carbon black provided by the present invention
  • FIG. 8 is a comparison diagram of stress-strain curves between the diaphragm provided by the present invention and the existing conventional diaphragm;
  • Fig. 9 is a comparison diagram of harmonic distortion test curves between the diaphragm provided by the present invention and the existing conventional diaphragm;
  • FIG. 10 is a comparison diagram of the high-order harmonic distortion test curve of the diaphragm provided by the present invention and the existing conventional diaphragm;
  • 11 is a test curve diagram of the vibration displacement of different parts of the diaphragm provided by the present invention at different frequencies;
  • Fig. 12 is a test curve diagram of the vibration displacement of different parts of the diaphragm in the prior art at different frequencies
  • Fig. 13 is a comparison diagram of impedance curves of diaphragms with different hardnesses in different embodiments of the present invention.
  • Fig. 14 is a comparison diagram of test curves of loudness at different frequencies between the diaphragm provided by the present invention and the existing diaphragm.
  • the invention provides a diaphragm for a sounding device, which is made of polyacrylate copolymer.
  • the material formed by polymerization of polyacrylate as the main body is polyacrylate rubber.
  • the polyacrylate copolymer of the present invention may specifically include two different materials, both of which are polyacrylate rubbers, and both can achieve the technical effects required by the present invention.
  • the polyacrylate copolymer includes "ethylene-acrylate copolymer", and this polyacrylate copolymer is an AEM type copolymer.
  • the molecular formula of "ethylene-acrylate copolymer” can be as follows:
  • x and y are natural numbers; R is an alkyl group.
  • the mass ratio of the polyethylene block to the polyacrylate block is 0.05-10.
  • the polyethylene block provides toughness in the material matrix, so that the rubber has better low temperature resistance. If the content of the polyethylene block is too high, the rigidity of the polyacrylate rubber is insufficient, and it is difficult to meet the needs of use.
  • the ratio of polyethylene block to polyacrylate block increases, the glass transition temperature of the material gradually decreases, and the mechanical strength first remains unchanged and then decreases sharply. Especially when the ratio is 15, its mechanical strength is only 6.3MPa.
  • the mass ratio of the polyethylene block and the polyacrylate block is preferably limited to the range of 0.05-10, which can not only meet the needs of the diaphragm for mechanical properties such as toughness, but also provide good low temperature resistance.
  • the mass ratio of the polyethylene block and the polyacrylate block is preferably 0.1-5.
  • polyacrylate copolymer may also include "ethylene-acrylate-carboxylic acid copolymer".
  • the molecular formula of "ethylene-acrylate-carboxylic acid copolymer” is as follows:
  • x, y, and z are natural numbers; R and R'are alkyl groups.
  • the mass ratio of the polyethylene block to the polyacrylate block is 0.1-10
  • the polycarboxylic acid block accounts for 0.5-10wt% of the total mass of the polyacrylate copolymer
  • the polycarboxylic acid block plays a crosslinking role in the matrix.
  • the higher the content the greater the degree of cross-linking of the material matrix, and the greater the rigidity of the material.
  • the excessively large degree of crosslinking causes the rubber to lose its high elasticity. If the mass ratio of the polycarboxylic acid block is too high, the crosslinking of the polyacrylate rubber will be too large, and the elasticity of the rubber will be significantly reduced.
  • Figure 2 shows the effect of the percentage of polycarboxylic acid block on the glass transition temperature and elongation at break of the material. It can be seen from the figure that as the mass proportion of the polycarboxylic acid block increases, the degree of crosslinking of the material increases Large, the movement of the molecular chain is restricted, the glass transition temperature increases, and the elongation at break decreases. Therefore, the present invention limits the range of the polycarboxylic acid block to the total mass of the polyacrylate copolymer in the range of 0.5-10wt%, so that the polyacrylate copolymer has the glass transition temperature and elongation at break that meet the performance requirements. rate.
  • the mass ratio of the polyethylene block and the polyacrylate block is preferably 0.2-5, and the polycarboxylic acid block accounts for the total mass of the polyacrylate copolymer in the range of 1-5 wt%.
  • the polyacrylate copolymer is made by crosslinking and polymerizing an alkyl acrylate as the main polymerizing monomer and a crosslinking monomer, and this polyacrylate copolymer is an ACM type copolymer.
  • ACM type copolymer The molecular formula of ACM type copolymer can be shown as follows:
  • R can be at least one of an alkyl main monomer, an ethyl main monomer, a methyl main monomer, or an n-butyl main monomer;
  • X is COO(CH 2 ) 2 OCH 3 -CN comonomer
  • Y is at least one of -COOH cross-linking functional group, -OCOCH 2 Cl cross-linking functional group, -OCH 2 CH 2 Cl cross-linking functional group, epoxy cross-linking functional group or unsaturated olefin group;
  • n, a are natural numbers.
  • the polyacrylate rubber has a higher damping factor, and its influencing factors include the degree of crosslinking, intermolecular hydrogen bonds, plasticizer content and other factors.
  • the content of the polyacrylate block affects the number of intermolecular hydrogen bonds.
  • the glass transition temperature increases and the damping factor increases.
  • Intermolecular hydrogen bonds are physical entanglements.
  • the amount of intermolecular hydrogen bonds has less influence on the mechanical strength than the degree of crosslinking has on the mechanical strength of the material.
  • a vulcanizing agent is mixed in the ACM type copolymer.
  • the mass parts of the polyacrylate copolymer is 100 parts, and the mass parts of the vulcanizing agent itself is 0.5-5 parts.
  • the addition of vulcanizing agent helps to form cross-linking points in the polyacrylate copolymer and increase the degree of cross-linking of the copolymer.
  • the mixing amount of the vulcanizing agent is too large, as shown in Figure 3, the degree of crosslinking of the polyacrylate copolymer will increase significantly, which will cause the molecular chain movement in the copolymer to be restricted, the glass transition temperature rises, and the elongation at break The rate is reduced.
  • the mass parts of the vulcanizing agent itself is 0.5-5 parts.
  • the mass parts of the vulcanizing agent itself is 0.8-3 parts. In the case of the above mass parts, it can not only ensure that the polyacrylate copolymer has an appropriate degree of crosslinking, but also meet the requirements for the glass transition temperature and mechanical properties of the material.
  • the vulcanizing agent includes trimercapto-s-triazine vulcanization system, polyamine, organic acid, ammonium salt, organic acid ammonium salt, dithiocarbamate, imidazole/anhydride, isocyanuric acid/quaternary salt, At least one of sulfur/accelerator and peroxide.
  • the polyacrylate copolymer may be mixed with a plasticizer, and the plasticizer includes aliphatic dibasic acid esters, phthalic acid esters, benzoic acid esters, benzoic acid esters, At least one of polyol esters, chlorinated hydrocarbons, epoxy, citrate esters, and polyesters.
  • the plasticizer includes aliphatic dibasic acid esters, phthalic acid esters, benzoic acid esters, benzoic acid esters, At least one of polyol esters, chlorinated hydrocarbons, epoxy, citrate esters, and polyesters.
  • the polar groups on the plasticizer and the polar groups on the polyacrylate block attract each other, which reduces the interaction of the polar groups on the polyacrylate block, so the addition of plasticizers, It is equivalent to covering up the polar groups on the polyacrylate block, which becomes a shielding effect, and as a result, the physical crosslinking points are reduced.
  • the molecules of plasticizers are much smaller than polyacrylate blocks, they are easier to move, and can conveniently provide the space required for segment activities, reduce the glass transition temperature of the material, and increase the material's cold resistance. , And improve the processing performance of the material.
  • the mass part of the plasticizer itself when the mass part of the polyacrylate copolymer itself is 100 parts, optionally, the mass part of the plasticizer itself is 1 part. -13 copies.
  • the mass part of the plasticizer itself is 1 part. -13 copies.
  • the mass fraction of the plasticizer itself meets the above range, it can ensure that the performance of the polyacrylate copolymer can meet the performance requirements of the diaphragm.
  • the mass parts of the plasticizer itself is 3-10 parts.
  • the mass parts of the plasticizer itself when the mass parts of the polyacrylate copolymer itself is 100 parts, optionally, the mass parts of the plasticizer itself is 1-10 servings.
  • the mass parts of the plasticizer itself is 3-7 parts.
  • the polyacrylate copolymer may be mixed with a reinforcing agent, and the reinforcing agent includes at least one of carbon black, silicon dioxide, calcium carbonate, and barium sulfate.
  • the mass parts of the polyacrylate copolymer itself is 100 parts
  • the mass parts of the reinforcing agent itself is 1-90 parts.
  • the surface of the reinforcing agent has groups such as hydrogen, carboxyl group, lactone group, free radical, quinone group, etc., which can undergo reactions such as substitution, reduction, and oxidation.
  • Carbon black is an amorphous structure, and particles form aggregates through physical and chemical bonding with each other.
  • the primary structure of carbon black is composed of aggregates, and there are van der Waals forces or hydrogen bonds between the aggregates, which can aggregate into a spatial network structure, that is, the secondary structure of carbon black.
  • the carbon black has the above-mentioned groups on the surface.
  • Carbon black particles can form the above-mentioned relationship with the molecular chain of the copolymer to enhance the mechanical strength of the polyacrylate copolymer. However, if the mechanical strength is too high, it will cause the resonance frequency of the miniature sound device to be too high, and the low frequency response ability will decrease.
  • the mass part of the polyacrylate copolymer itself when the mass part of the polyacrylate copolymer itself is 100 parts, optionally, the mass part of the reinforcing agent is 1 part. -85 copies.
  • the mass fraction of carbon black when the mass fraction of carbon black is 0.5, the mechanical strength and elongation at break of the polyacrylate copolymer are both small, which is due to the carbon black The amount is small, and its dispersion in the matrix is not uniform, and it is difficult to achieve a reinforcing effect.
  • the mass fraction of carbon black itself increases, the mechanical strength of the ACM copolymer increases, while the elongation at break gradually decreases.
  • the mass parts of the reinforcing agent itself is 1 to 85 parts, it can better meet the requirements of the present invention for the performance of the diaphragm.
  • the mass parts of the reinforcing agent itself is 2-75 parts.
  • the mass parts of the reinforcing agent itself when the mass parts of the polyacrylate copolymer itself is 100 parts, the mass parts of the reinforcing agent itself is 1-90 parts .
  • the mass fraction of carbon black when the mass fraction of carbon black is 0.5, the mechanical strength and elongation at break of the polyacrylate copolymer are both small, which is due to the carbon black The amount is small, and its dispersion in the matrix is not uniform, and it is difficult to achieve a reinforcing effect.
  • the mass fraction of carbon black itself increases, the mechanical strength of the AEM copolymer increases, while the elongation at break gradually decreases.
  • the mass parts of the reinforcing agent itself is 1-90 parts, it can meet the requirements of the present invention for the performance of the diaphragm.
  • the mass parts of the reinforcing agent itself is 2-70 parts.
  • a crosslinking agent is mixed in the polyacrylate copolymer, and the crosslinking agent includes a peroxide crosslinking agent and a crosslinking assistant agent.
  • the peroxide crosslinking agent is used to generate free radicals from the "ethylene-acrylate copolymer”.
  • the co-crosslinking agent is used for radical polymerization with the "ethylene-acrylate copolymer”.
  • the peroxide crosslinking agent includes 1,3-1,4-bis(tert-butylperoxyisopropyl)benzene, dicumyl peroxide, 2,5-dimethyl-2,5-bis (Tert-butylperoxy)hexane, tert-butyl cumene peroxide, 2,5-dimethyl-2,5-bis(tert-butylperoxy)-3-hexyne, 4,4 ⁇ -bis (Tert-butylperoxy) n-butyl valerate, 1,1 ⁇ -bis(tert-butylperoxy)-3,3,5 trimethylcyclohexane and 2,4-dichlorobenzene peroxide At least one of formyl.
  • the co-crosslinking agent includes trimethylolpropane triacrylate, trimethylolpropane trimethacrylate, N,N ⁇ -m-phenylene bismaleimide, diallyl phthalic acid At least one of ester, triallyl isocyanate and triallyl cyanate.
  • the crosslinking agent and the resulting crosslinking points can determine the degree of crosslinking of the polyacrylate copolymer. Within a certain range, the more crosslinking points and the greater the amount of crosslinking agent, the higher the degree of crosslinking. Too high a degree of crosslinking will make the molecular chain more difficult to move, resulting in an increase in the glass transition temperature of the polyacrylate copolymer and an increase in the damping factor. And the higher the mechanical strength of the material, the lower the elongation at break and the elastic recovery.
  • the material of the diaphragm may also include an amide cross-linked polymer and/or an imide cross-linked polymer formed by the reaction of "ethylene-acrylate-carboxylic acid copolymer" and an amine cross-linking agent .
  • the amine cross-linking agent includes at least one of hexamethylene diamine, hexamethylene diamine carbamate, triethylene tetramine, diphenylamine, and di-o-toluidine.
  • the glass transition temperature can be adjusted by adjusting the mass ratio of the polyethylene block to the polyacrylate block, the content of the polycarboxylic acid block and the amount of crosslinking agent.
  • the mass ratio of polyethylene block to polyacrylate block is 0.2-5
  • the mass percentage of polycarboxylic acid block is 1-5 wt%
  • the amount of crosslinking agent is between 1-5 parts, which makes polyacrylic acid
  • the glass transition temperature of ester rubber is ⁇ -20°C.
  • the glass transition temperature enables the speaker diaphragm to maintain a high elastic state at room temperature, and has good resilience.
  • the polyacrylate copolymer has a stable hinge structure, the diaphragm has a higher upper limit of use temperature. After testing, it can work continuously for more than 72 hours under the condition of 200°C, which can meet the application requirements of miniature sound device for high and low temperature and long time. There is no risk of structural collapse due to excessive temperature in field use.
  • the polyacrylate copolymer is mixed with an anti-aging agent, and the anti-aging agent includes anti-aging agent N-445, anti-aging agent 246, anti-aging agent 4010, anti-aging agent SP, and anti-aging agent RD. , At least one of anti-aging agent ODA, anti-aging agent OD, and anti-aging agent WH-02.
  • the mass parts of the anti-aging agent itself is 0.5-10 parts.
  • the mass parts of the polyacrylate copolymer is 100 parts
  • the mass parts of the anti-aging agent itself can be selected in the range of 0.5-10 parts.
  • the mass parts of the anti-aging agent itself is 1-5 parts.
  • an internal mold release agent is mixed in the polyacrylate copolymer.
  • the internal mold release agent includes at least one of stearic acid and stearate, stearylamine and alkyl phosphate, and ⁇ -octadecyl- ⁇ -hydroxypolyoxyethylene phosphate.
  • the Mooney viscosity and green strength of polyacrylate rubber including "ethylene-acrylate copolymer” are relatively low. This performance feature will cause process problems such as sticking rollers and sticking molds in the injection molding process of polyacrylate rubber.
  • the invention improves the processing performance of the polyacrylate copolymer by adding an internal mold release agent to the rubber compound of the polyacrylate copolymer.
  • the mixing amount of the internal release agent is small, it is difficult to improve the mucosal problem. However, if the mixing amount is too large, the adhesion between the polyacrylate rubber and the adhesive layer during the later preparation of the diaphragm is likely to decrease, and the performance of the final diaphragm is adversely affected.
  • the mass parts of the polyacrylate copolymer is 100 parts
  • the mass parts of the internal release agent itself may be 0.5-5 parts.
  • the mass parts of the internal release agent itself is 1-3 parts.
  • the glass transition temperature of the diaphragm is -70 to 0°C. Because the polyacrylate copolymer has a higher molecular weight, and its molecular chain is more flexible, it has better low temperature resistance.
  • the speaker diaphragm can maintain a high elastic state at room temperature and has good resilience.
  • the diaphragm can work normally at a lower temperature.
  • the thickness of the diaphragm is constant, the lower the glass transition temperature, the lower the resonance frequency F0 of the assembled miniature sound device.
  • the glass transition temperature of the diaphragm may be -60 to 0°C. It is preferably -50 to -20°C. This allows the speaker diaphragm to maintain better elasticity when working at a temperature below 0°C, so that the speaker exhibits a higher sound quality. At the same time, the risk of damage to the speaker diaphragm in a low temperature environment is reduced, and the reliability is higher.
  • the preferred range of the glass transition temperature of the diaphragm is -60 to -20°C. This allows the speaker diaphragm to maintain better elasticity when working at a temperature below 0°C, so that the speaker exhibits a higher sound quality. At the same time, the risk of damage to the speaker diaphragm in a low temperature environment is reduced, and the reliability is higher.
  • the polyacrylate copolymer used in the present invention contains a large amount of ester groups, when it is made into a diaphragm, it can form a hydrogen bond with the adhesive layer, and thus has excellent adhesion.
  • the adhesive force between the polyacrylate copolymer and the adhesive layer is greater than 100g/25mm (180° peeling), preferably, the adhesive force is greater than 200g/25mm (180° peeling).
  • the high cohesive force enables the diaphragm to have a good coordination and consistency with the Dome during the vibration process, and the sound quality is pure, and the speaker diaphragm still maintains its original state after a long period of vibration, with high performance stability.
  • the diaphragm may be a composite diaphragm, that is, the diaphragm includes multiple film layers, at least one of which is made of the above-mentioned polyacrylate copolymer.
  • the layers of the multilayer film can be combined by means of gluing, hot pressing, etc., to form the above-mentioned composite diaphragm.
  • the good adhesion performance of the polyacrylate copolymer can ensure the structural stability and reliability of the composite diaphragm.
  • the diaphragm needs to be bonded and assembled with the voice coil, the centering piece, and the reinforcement (DOME) through an adhesive layer.
  • the good adhesion performance of the diaphragm can play a role in the assembly and improve the acoustic performance and structural reliability of the miniature sounder product.
  • the type of the adhesive layer includes one or more of epoxy, acrylic, silicone resin, polyester, polyurethane, vinyl acetate resin, phenol resin, and urea resin.
  • the elongation at break of the diaphragm is greater than 100%.
  • the elongation at break of the diaphragm is greater than 150%. The high elongation at break makes the diaphragm less prone to reliability problems such as membrane rupture when used in a sounder.
  • the strain of the diaphragm provided by the embodiment of the present invention is significantly greater than that of the PEEK diaphragm in the prior art.
  • the Young's modulus of the diaphragm provided by the embodiment of the present invention is significantly smaller than that of the PEEK diaphragm in the prior art.
  • the existing PEEK diaphragm has an obvious yield point, which is about 0.4-0.5% strain.
  • the speaker diaphragm provided by the present invention does not have a yield point, which indicates that the diaphragm provided by the present invention has a wider elastic area and has excellent resilience performance.
  • the diaphragm made of polyacrylate copolymer has good flexibility, for example, the elongation at break is ⁇ 100%.
  • the polyethylene block has an important influence on the elongation at break, and those skilled in the art can make a selection according to actual needs. This makes the vibration displacement of the speaker diaphragm larger and louder. And the reliability and durability are good.
  • the material When the diaphragm is vibrating in a state of large amplitude, the material produces a large strain, and there is a risk of membrane folding, membrane cracking or membrane rupture when vibrating for a long time.
  • the diaphragm of the present invention using polyacrylate copolymer as the substrate has good flexibility and reduces the risk of diaphragm damage.
  • the polyacrylate copolymer provided by the present invention has a wider elastic area.
  • the strain of the diaphragm occurs in this area, the diaphragm has excellent resilience after the external force is removed.
  • the vibration process of the diaphragm there is less rocking vibration and better sound quality and listening stability.
  • it can be used continuously at a temperature of 200°C and has higher damping performance than existing materials.
  • the elastic recovery rate of the diaphragm after 20% strain is ⁇ 90%. Due to the good resilience of the diaphragm, the sound device has a better transient response and lower distortion.
  • the diaphragm provided by the present invention has lower THD (Total Harmonic Distortion) and HOHD than the existing PEEK diaphragm, and has no spikes. This shows that the diaphragm of the present invention has better anti-polarization ability and better sound quality.
  • the diaphragm provided by the invention is in a highly elastic state at room temperature, the molecular chain is easy to move, the friction between the molecules is large, and has good damping performance.
  • the loss factor of the diaphragm is greater than 0.06. Excellent damping performance, so that the diaphragm has a lower impedance.
  • the damping of the diaphragm is improved, the ability of the vibration system of the sound device to suppress the polarization phenomenon during the vibration process is enhanced, and the vibration consistency is good.
  • the damping of the existing diaphragm made of engineering plastics is low, and its loss factor is generally less than 0.01, and the damping is small.
  • the loss factor of the diaphragm provided by the present invention is greater than 0.1.
  • Fig. 11 is a test curve of the vibration displacement of different parts of the diaphragm of the sound generating device at different frequencies according to an embodiment of the present invention.
  • Fig. 12 is a test curve of the vibration displacement of different parts of the existing diaphragm at different frequencies.
  • the diaphragm is a rectangular folded ring diaphragm.
  • the abscissa is the frequency (Hz), and the ordinate is the loudness displacement (mm).
  • the Shore hardness of the diaphragm is 15-90A, preferably 20-80A.
  • the resonance frequency F0 of the sound generating device is proportional to the modulus, hardness and thickness of the diaphragm, while for polyacrylate copolymers, the modulus is proportional to the hardness. Therefore, hardness can be used to reflect the modulus of the diaphragm.
  • the strength and hardness of the polyacrylate copolymer can be adjusted by reinforcing agents.
  • an increase in the amount of polyacrylate blocks will increase intermolecular hydrogen bonds, which in turn will increase the strength and hardness of the material and increase the number of cross-linking points.
  • the higher the strength and hardness of the polyacrylate copolymer the higher the F0 of the diaphragm.
  • the loudness of the sound device will be reduced and the bass performance will be worse.
  • Figure 13 is the impedance curve of the diaphragm with the same thickness but different hardness. It can be seen from the figure that as the hardness increases, F0 increases sharply.
  • the diaphragm of the miniature sound device provided by the present invention is a folded ring diaphragm or a flat diaphragm.
  • the resonance frequency F0 of the sound device is proportional to the Young's modulus and thickness of the diaphragm.
  • the change of F0 can be achieved by changing the thickness and Young's modulus of the speaker diaphragm.
  • the specific adjustment principle is as follows:
  • Mms is the equivalent vibration quality of the speaker
  • Cms is the equivalent compliance of the speaker:
  • C m1 is elastic wave compliance
  • C m2 is diaphragm compliance
  • the equivalent compliance of the speaker is the diaphragm compliance:
  • W is the total width of the folded ring of the diaphragm
  • t is the thickness of the diaphragm
  • dvc is the outer diameter of the diaphragm and voice coil
  • E is the Young's modulus of the diaphragm material
  • u is the Poisson's ratio of the diaphragm material .
  • the resonance frequency F0 of the sound emitting device is proportional to the modulus and thickness of the diaphragm.
  • the modulus of the diaphragm is directly proportional to its hardness. Therefore, hardness can be used instead of its modulus.
  • the diaphragm should have sufficient rigidity and damping.
  • the size of F0 by adjusting the hardness and thickness of the speaker diaphragm.
  • the Shore hardness of the diaphragm is preferably 20-80A, and the thickness of the diaphragm is 60-120 ⁇ m.
  • the resonance frequency F0 of the miniature sound emitting device can reach 150-1500 Hz. The low frequency performance of the miniature sound device is excellent.
  • the diaphragm may be a single-layer structure or a multilayer composite diaphragm.
  • the single-layer diaphragm is a diaphragm composed of a layer of polyacrylate copolymer film.
  • the composite diaphragm is a diaphragm formed by successively stacking multiple polyacrylate copolymer film layers.
  • the composite diaphragm may include at least one polyacrylate copolymer film layer, which is laminated and compounded with a film layer made of other materials to form a composite diaphragm made of multiple materials.
  • the composite diaphragm may be a two-layer, three-layer, four-layer or five-layer composite diaphragm, which is not limited in the present invention.
  • At least one film layer in the composite diaphragm is a polyacrylate copolymer film layer made of the polyacrylate copolymer provided by the present invention.
  • the thickness may be 10-200 ⁇ m, preferably 30-120 ⁇ m. When the thickness of the polyacrylate copolymer film layer is within this range, it can better meet the performance requirements and assembly space requirements of the miniature sound emitting device.
  • the present invention provides a comparison curve diagram of a specific implementation of the diaphragm provided by the present invention and the existing conventional diaphragm, as shown in FIG. 14.
  • Figure 14 shows the test curves (SPL curves) of the loudness of the two diaphragms at different frequencies.
  • the diaphragm is a folded ring diaphragm.
  • the abscissa is frequency (Hz), and the ordinate is loudness.
  • the dotted line is the test curve of the diaphragm for the miniature sounding device provided by the present invention.
  • the solid line is the test curve of the existing conventional diaphragm.
  • the F0 of the miniature sounding device using the diaphragm provided by the present invention is 806 Hz, that is, at a in the figure.
  • the F0 of the sound device using the existing diaphragm is 886 Hz, which is at b in the figure.
  • the present invention also provides a miniature sounding device, which comprises a main body of the sounding device and the above-mentioned diaphragm made of polyacrylate copolymer.
  • the polyacrylate copolymer may be the above-mentioned AEM-type copolymer or the above-mentioned ACM-type copolymer, which is not limited in the present invention.
  • the diaphragm is arranged on the main body of the sound emitting device, and the diaphragm is configured to be driven to vibrate, and to generate sound through vibration.
  • the main body of the sound generating device may be equipped with components such as a coil, a magnetic circuit system, etc., and the diaphragm is driven to vibrate through electromagnetic induction.

Abstract

本发明公开了一种用于微型发声装置的振膜和微型发声装置。所述用于微型发声装置的振膜采用聚丙烯酸酯共聚物制成，所述聚丙烯酸酯共聚物中混合有增塑剂，所述增塑剂包括脂肪族二元酸酯类、苯二甲酸酯类、苯多酸酯类、苯甲酸酯类、多元醇酯类、氯化烃类、环氧类、柠檬酸酯类、聚酯类中的至少一种，所述振膜的玻璃化转变温度的范围为-70～0℃，所述振膜被配置为，在装配时与胶层之间的粘接力大于100g/25mm(180°剥离)。本发明提供的振膜具有更优的声学性能。

Description

一种用于微型发声装置的振膜和微型发声装置 技术领域
本发明电子产品技术领域，具体地，涉及一种微型发声装置的振膜和微型发声装置。
背景技术
用于发声装置的振膜多采用多层复合材料，例如，PEEK、PAR、PEI、PI等工程塑料，TPU、TPEE等弹性体材料，丙烯酸胶膜、硅胶胶膜等胶膜。此外，硅橡胶具有良好的热稳定性、良好的疏水性能和优异的回弹性能，随着高功率化、防水以及高音质要求的提高，硅橡胶也逐渐被用于制作振膜。但是近年来，随着手机、平板电脑等小型电子设备的快速发展，电子设备中需要配置体积更小、性能更好的微型发声装置。这种需求导致现有的常用复合材料并不能满足性能要求。
上述材料都存在各自的缺点。例如，PEEK、PAR等工程塑料，虽然耐温性较好，但材料回弹性较差，产品易产生膜折，无法起到防水的作用。TPU、TPEE等弹性体材料的熔点较低，耐温性较差。硅橡胶材料虽然热稳定性和回弹性均较好，但因其化学结构对称，立构规整度高，对称取代的甲基空间位阻小，硅橡胶的模量或硬度相对较低，导致材料的阻尼性较低，造成硅橡胶振膜的产品失真较大。
可见，上述振膜的综合性能较差，不能满足微型发声装置的全面性能要求。因此，提供一种综合性能强、可靠性高的用于微型发声装置的振膜成为本技术领域面临的一大技术问题。
发明内容
本发明的一个目的是提供一种用于微型发声装置的振膜的新技术方案。
根据本发明的第一方面，提供了一种用于微型发声装置的振膜，所述振膜采用聚丙烯酸酯共聚物制成，所述聚丙烯酸酯共聚物中混合有增塑剂，所述增塑剂包括脂肪族二元酸酯类、苯二甲酸酯类、苯多酸酯类、苯甲酸酯类、多元醇酯类、氯化烃类、环氧类、柠檬酸酯类、聚酯类中的至少一种，所述振膜的玻璃化转变温度的范围为-70～0℃，所述振膜被配置为，在装配时与胶层之间的粘接力大于100g/25mm(180°剥离)。
可选地，所述聚丙烯酸酯共聚物采用丙烯酸烷基酯作为聚合主单体与交联单体交联聚合制成，所述振膜的玻璃化转变温度的范围为-60～0℃。
可选地，所述振膜的玻璃化转变温度的范围为-50～-20℃。
可选地，所述聚丙烯酸酯共聚物自身的质量份数为100份，所述增塑剂自身的质量份数为1-13份。
可选地，所述聚丙烯酸酯共聚物中混合有硫化剂，所述聚丙烯酸酯共聚物自身的质量份数为100份，所述硫化剂自身的质量份数为0.5-5份。
可选地，所述聚丙烯酸酯共聚物包括“乙烯-丙烯酸酯共聚物”和“乙烯-丙烯酸酯-羧酸共聚物”中的至少一种。
可选地，所述振膜的玻璃化转变温度的范围为-60～-20℃。
可选地，所述聚丙烯酸酯共聚物自身的质量份数为100份，所述增塑剂自身的质量份数为1-10份。
可选地，所述振膜与胶层之间的粘接力大于200g/25mm(180°剥离)。
可选地，所述聚丙烯酸酯共聚物中混合有内脱模剂，所述内脱模剂包括硬脂酸及硬脂酸盐、十八烷基胺和磷酸烷基酯、α-十八烷基-ω-羟基聚氧乙烯磷酸酯中的至少一种，所述聚丙烯酸酯共聚物自身的质量份数为100份，所述内脱模剂自身的质量份数为0.5-5份。
可选地，所述内脱模剂自身的质量份数为1-3份。
可选地，所述振膜为单层振膜，所述单层振膜采用一层聚丙烯酸酯共聚物膜层构成；
或者，所述振膜为复合振膜，所述复合振膜包括两层、三层、四层或五层膜层，所述复合振膜至少包括一层聚丙烯酸酯共聚物膜层。
可选地，所述聚丙烯酸酯共聚物膜层的厚度为10-200μm。
可选地，所述聚丙烯酸酯共聚物膜层的厚度为30-120μm。
可选地，所述胶层的类型包括环氧类、丙烯酸类、有机硅树脂类、聚酯类、聚氨酯类、氯醋树脂类、酚醛树脂类、脲醛树脂类中的一种或多种。
根据本发明的另一方面，还提供了一种微型发声装置，包括发声装置主体和上述的振膜，所述振膜设置在所述发声装置主体上，所述振膜被配置为能振动发声。
根据本发明公开的一个实施例，所述振膜具有更优的声学性能和更高的使用稳定性。
通过以下参照附图对本发明的示例性实施例的详细描述，本发明的其它特征及其优点将会变得清楚。
附图说明
被结合在说明书中并构成说明书的一部分的附图示出了本发明的实施例，并且连同其说明一起用于解释本发明的原理。
图1是本发明提供的振膜的聚乙烯嵌段与聚丙烯酸酯嵌段比对玻璃化转变温度及力学强度的图表；
图2是本发明提供的振膜的聚羧酸嵌段对玻璃化转变温度及断裂伸长率的影响的图表；
图3是本发明提供的振膜的硫化剂用量对玻璃化转变温度及断裂伸长率的影响的图表；
图4是本发明提供的采用ACM型聚合物制成的振膜中增塑剂混合量与材料的玻璃化转变温度及力学强度的关系的图表；
图5是本发明提供的采用AEM型聚合物制成的振膜中增塑剂混合量与材料的玻璃化转变温度及力学强度的关系的图表；
图6是本发明提供的采用ACM型聚合物制成的振膜的应力-应变曲线与炭黑混合份数的关系图；
图7是本发明提供的采用AEM型聚合物制成的振膜的应力-应变曲线与炭黑混合份数的关系图；
图8是本发明提供的振膜与现有常规振膜的应力应变曲线对比图；
图9是本发明提供的振膜与现有常规振膜的谐波失真测试曲线对比图；
图10是本发明提供的振膜与现有常规振膜的高次谐波失真测试曲线对比图；
图11是本发明提供的振膜的不同部位在不同频率下振动位移的测试曲线图；
图12是现有技术中的振膜的不同部位在不同频率下振动位移的测试曲线图；
图13本发明的不同实施方式中具有不同硬度的振膜的阻抗曲线对比图；
图14本发明提供的振膜与现有的振膜的不同频率下响度的测试曲线对比图。
具体实施方式
现在将参照附图来详细描述本发明的各种示例性实施例。应注意到：除非另外具体说明，否则在这些实施例中阐述的部件和步骤的相对布置、数字表达式和数值不限制本发明的范围。
以下对至少一个示例性实施例的描述实际上仅仅是说明性的，决不作为对本发明及其应用或使用的任何限制。
对于相关领域普通技术人员已知的技术、方法和设备可能不作详细讨论，但在适当情况下，所述技术、方法和设备应当被视为说明书的一部分。
在这里示出和讨论的所有例子中，任何具体值应被解释为仅仅是示例性的，而不是作为限制。因此，示例性实施例的其它例子可以具有不同的值。
应注意到：相似的标号和字母在下面的附图中表示类似项，因此，一旦某一项在一个附图中被定义，则在随后的附图中不需要对其进行进一步讨论。
本发明提供了一种用于发声装置的振膜，该振膜采用聚丙烯酸酯共聚物制成。由聚丙烯酸酯作为主体聚合形成的材料为聚丙烯酸酯橡胶。
本发明的所述聚丙烯酸酯共聚物具体可以包括两种不同的材料，这两种具体材料均属于聚丙烯酸酯橡胶，均能够达到本发明所要求的技术效果。
在其中一种实施方式中，所述聚丙烯酸酯共聚物中包括“乙烯-丙烯酸酯共聚物”，这种聚丙烯酸酯共聚物为AEM型共聚物。“乙烯-丙烯酸酯共聚物”的分子式可以呈如下所示：
Figure PCTCN2020085641-appb-000001
在以上分子式中，x,y为自然数；R为烷基。
特别地，聚乙烯嵌段与聚丙烯酸酯嵌段的质量比在0.05-10。聚乙烯嵌段在材料基体中提供韧性，使橡胶具有较好的耐低温性能。而如果聚乙烯嵌段的含量过高时，聚丙烯酸酯橡胶的刚性不足，难以满足使用需求。如图1，随着聚乙烯嵌段与聚丙烯酸酯嵌段比例增大，材料的玻璃化转变温度逐渐降低，力学强度先保持不变后急剧降低。尤其当比值为15时，其力学强度仅剩6.3MPa。因此，本发明将聚乙烯嵌段和聚丙烯酸酯嵌段的质量比优选限制在0.05-10这一范围内，既能够满足振膜对韧性等力学性能的需要，又能够提供良好的低温耐性。所述聚乙烯嵌段和聚丙烯酸酯嵌段的质量比优选在0.1-5。
进一步可选地，所述聚丙烯酸酯共聚物中还可以包括“乙烯-丙烯酸酯-羧酸共聚物”。“乙烯-丙烯酸酯-羧酸共聚物”的分子式呈如下所示：
Figure PCTCN2020085641-appb-000002
在以上分子式中，x,y,z为自然数；R、R’为烷基。
特别地，聚乙烯嵌段与聚丙烯酸酯嵌段的质量比在0.1-10，聚羧酸嵌段占聚丙烯酸酯共聚物总质量的0.5-10wt％，聚羧酸嵌段在基体中起交联作用，含量越高，材料基体的交联度越大，材料的刚性越大。而过大的交联度，使橡胶损失其高弹性。如果聚羧酸嵌段的质量占比过高，会造成聚丙烯酸酯橡胶的交联度过大，橡胶的弹性明显降低。图2为聚羧酸嵌段百 分含量对材料玻璃化转变温度和断裂伸长率的影响，由图可以看出，随着聚羧酸嵌段质量占比增大，材料的交联度增大，分子链运动受限制，玻璃化转变温度增大，断裂伸长率降低。因此，本发明将聚羧酸嵌段占聚丙烯酸酯共聚物的总质量的范围限制在0.5-10wt％这一范围内，以使聚丙烯酸酯共聚物具备满足性能要求的玻璃化转变温度和断裂伸长率。所述聚乙烯嵌段和聚丙烯酸酯嵌段的质量比优选在0.2-5，聚羧酸嵌段占聚丙烯酸酯共聚物的总质量的范围为1-5wt％。
在另一种实施方式中，所述聚丙烯酸酯共聚物采用丙烯酸烷基酯作为聚合主单体与交联单体交联聚合制成，这种聚丙烯酸酯共聚物为ACM型共聚物。ACM型共聚物的分子式可选呈如下所示：
Figure PCTCN2020085641-appb-000003
以上分子式中，R可为烷基主单体、乙基主单体、甲基主单体、或正-丁基主单体中的至少一种；
X为COO(CH 2) 2OCH 3-CN共聚单体；
Y为-COOH交联官能团、-OCOCH 2Cl交联官能团、-OCH 2CH 2Cl交联官能团、环氧基交联官能团或不饱和烯烃基团中的至少一种；
m、n、a为自然数。
所述聚丙烯酸酯橡胶具有较高的阻尼因子，其影响因素包括交联程度、分子间氢键、增塑剂含量等因素影响，以上因素均在一定范围内越大，阻尼因子越大，阻尼性能越好，振膜发声时的失真越低。
聚丙烯酸酯嵌段的含量影响分子间氢键的数量。聚丙烯酸酯嵌段的含量越高，分子间氢键越多，分子链越难运动。相应地，玻璃化转变温度升高，阻尼因子增大。分子间氢键属于物理缠结，分子间氢键越多，在一定范围内导致材料力学强度越高。不过，分子间氢键的量对力学强度的影响小于交联程度对材料的力学强度的影响。
可选地，ACM型共聚物中混合有硫化剂。聚丙烯酸酯共聚物的质量份数为100份，所述硫化剂自身的质量份数为0.5-5份。硫化剂的添加有助 于在聚丙烯酸酯共聚物中形成交联点，提高共聚物的交联程度。但是，如果硫化剂的混合量过大，如图3所示，聚丙烯酸酯共聚物的交联度会显著上升，进而造成共聚物中分子链运动受限制，玻璃化转变温度上升，断裂伸长率降低。因此，在本发明的实施方式中，所述硫化剂自身的质量份数为0.5-5份。优选地，所述硫化剂自身的质量份数为0.8-3份。上述质量份数的情况下，既能够保证聚丙烯酸酯共聚物具有适当的交联度，又能够满足对材料的玻璃化转变温度、力学性能的要求。
可选地，所述硫化剂包括三巯基均三嗪硫化体系、多胺、有机酸、铵盐、有机酸铵盐、二硫代氨基甲酸盐、咪唑/酸酐、异氰尿酸/季盐、硫黄/促进剂、过氧化物中的至少一种。
可选地，所述聚丙烯酸酯共聚物中可以混合有增塑剂，所述增塑剂包括脂肪族二元酸酯类、苯二甲酸酯类、苯多酸酯类、苯甲酸酯类、多元醇酯类、氯化烃类、环氧类、柠檬酸酯类、聚酯类中的至少一种。
增塑剂上的极性基团与聚丙烯酸酯嵌段上的极性基团有相互吸引的作用，减少了聚丙烯酸酯嵌段上极性基团的相互作用，因而增塑剂的加入，相当于把聚丙烯酸酯嵌段上的极性基团给遮盖起来，成为屏蔽作用，结果使物理交联点减少。另一方面，增塑剂的分子比聚丙烯酸酯嵌段小得多，它们活动比较容易，可以很方便的提供链段活动所需要的空间，降低材料的玻璃化转变温度，增加材料的耐寒性能，并且改善材料的加工性能。
在一种实施方式中，对于上述ACM型共聚物，在所述聚丙烯酸酯共聚物自身的质量份数为100份的情况下，可选地，所述增塑剂自身的质量份数为1-13份。如图4所示，随着增塑剂用量增加，材料的玻璃化转变温度降低，但相应的，材料的拉伸强度也会降低。当增塑剂含量为15时，材料拉伸强度大幅下降。此外，过量的增塑剂会从材料内部析出，降低材料的力学性能。在增塑剂自身的质量份数符合上述范围时，能够保证聚丙烯酸酯共聚物的性能能够满足振膜的性能要求。优选地，所述增塑剂自身的质量份数为3-10份。
在另一种实施方式中，对于上述AEM型共聚物，在所述聚丙烯酸酯共聚物自身的质量份数为100份的情况下，可选地，所述增塑剂自身的质量 份数为1-10份。如图5所示，随着增塑剂用量增加，材料的玻璃化转变温度降低，但相应的，材料的拉伸强度也会降低。当增塑剂含量为12时，材料拉伸强度大幅下降。此外，过量的增塑剂会从材料内部析出，降低材料的力学性能。优选地，所述增塑剂自身的质量份数为3-7份。
可选地，所述聚丙烯酸酯共聚物中可以混合有补强剂，所述补强剂包括炭黑、二氧化硅、碳酸钙和硫酸钡中的至少一种。在所述聚丙烯酸酯共聚物自身的质量份数为100份的情况下，所述补强剂自身的质量份数为1-90份。
补强剂的表面具有能够发生取代、还原、氧化等反应的氢、羧基、内酯基、自由基、醌基等基团。将补强剂混合入聚丙烯酸酯共聚物中后，由于补强剂与聚合物嵌段的界面之间的强相互作用，材料受力时，分子链比较容易在补强剂微粒表面上滑动，但不易和补强剂微粒脱离，聚丙烯酸酯共聚物与补强剂微粒构成一种能够滑动的强固的键，力学强度增大。
以炭黑为例，炭黑是一种无定形结构，粒子通过相互之间的物理化学结合构成聚集体。炭黑的一次结构由聚集体构成，同时聚集体之间存在范德华力或氢键，能够聚集成空间网络结构，也就是炭黑的二次结构。炭黑表面具有上述基团。炭黑微粒能够与共聚物分子链形成上述关系，增强聚丙烯酸酯共聚物的力学强度。但如果力学强度过高，反而会造成微型发声装置的谐振频率过高，低频响应能力下降。
在一种实施方式中，对于上述ACM型共聚物，在所述聚丙烯酸酯共聚物自身的质量份数为100份的情况下，可选地，所述补强剂自身的质量份数为1-85份。如图6所示，以选择炭黑作为补强剂为例，当炭黑的质量份数为0.5时，聚丙烯酸酯共聚物的力学强度和断裂伸长率均较小，这是由于炭黑量较少，其在基体中分散不均匀，难以起到补强效果。随着炭黑自身的质量份数增加，ACM型共聚物的力学强度增大，而断裂伸长率逐渐减小。尤其当炭黑份数为90份时，其断裂伸长率降低到83％。在这种情况下，所制成的振膜在长期使用中存在破膜风险。因此，优选地，所述补强剂自身的质量份数为1-85份时，能够更好的满足本发明对振膜性能的要求。优选地，所述补强剂自身的质量份数为2-75份。
在另一种实施方式中，对于上述AEM型共聚物，在所述聚丙烯酸酯共聚物自身的质量份数为100份的情况下，所述补强剂自身的质量份数为1-90份。如图7所示，以选择炭黑作为补强剂为例，当炭黑的质量份数为0.5时，聚丙烯酸酯共聚物的力学强度和断裂伸长率均较小，这是由于炭黑量较少，其在基体中分散不均匀，难以起到补强效果。随着炭黑自身的质量份数增加，AEM型共聚物的力学强度增大，而断裂伸长率逐渐减小。尤其当炭黑份数为95份时，其断裂伸长率降低到95％。在这种情况下，所制成的振膜在长期使用中存在破膜风险。因此可选地，所述补强剂自身的质量份数为1-90份时，能够满足本发明对振膜性能的要求。优选地，所述补强剂自身的质量份数为2-70份。
可选地，所述聚丙烯酸酯共聚物中混合有交联剂，所述交联剂包括过氧化物交联剂和助交联剂。所述过氧化物交联剂用于使所述“乙烯-丙烯酸酯共聚物”产生自由基。所述助交联剂则用于与所述“乙烯-丙烯酸酯共聚物”发生自由基聚合。
所述过氧化物交联剂包括1,3-1,4-二(叔丁基过氧异丙基)苯、过氧化二异丙苯、2,5-二甲基-2,5-双(叔丁基过氧基)己烷、过氧化叔丁基异丙苯、2,5-二甲基-2,5-双(过氧化叔丁基)-3-己炔、4,4`-双(叔丁基过氧基)戊酸正丁酯、1,1`-双(叔丁基过氧基)-3,3,5三甲基环己烷和2,4-二氯过氧化苯甲酰中的至少一种。
所述助交联剂包括三羟甲基丙烷三丙烯酸酯、三羟甲基丙烷三甲基丙烯酸酯、N,N`-间苯撑双马来酰亚胺、二烯丙基邻苯二酸酯、三烯丙基异氰酸酯和三烯丙基氰酸酯中的至少一种。
交联剂以及所产生的交联点能够决定聚丙烯酸酯共聚物的交联程度。在一定范围内时，交联点越多，交联剂用量越大，交联程度越高。交联程度过高会导致分子链越难运动，导致聚丙烯酸酯共聚物的玻璃化转变温度升高，阻尼因子增大。并且材料力学强度越高，断裂伸长率和弹性回复率下降。
进一步地，所述振膜的材料中还可以包括由“乙烯-丙烯酸酯-羧酸共聚物”与胺类物质交联剂反应形成的酰胺交联聚合物和/或酰亚胺交联聚合 物。所述胺类物质交联剂包括己二胺、六亚甲基二胺氨基甲酸盐、三乙撑四胺、亚基二苯胺和二邻甲苯胍中的至少一种。
通过调整聚乙烯嵌段与聚丙烯酸酯嵌段的质量比、聚羧酸嵌段含量及交联剂用量，可以调节的玻璃化转变温度。例如，聚乙烯嵌段与聚丙烯酸酯嵌段的质量比在0.2-5，聚羧酸嵌段质量百分比在1-5wt％，交联剂添加量在1-5份之间，这使得聚丙烯酸酯橡胶的玻璃化转变温度≤-20℃。该玻璃化转变温度使得该扬声器振膜在常温下能够保持高弹态，回弹性良好。进一步地，由于聚丙烯酸酯共聚物具有稳定的铰链结构，所述振膜具有较高的使用温度上限。经测试，在200℃的条件下，可连续工作超过72小时，可满足微型发声装置对高低温、长时间的应用需求。在实地使用中不会出现温度过高而结构塌陷的风险。
可选地，所述聚丙烯酸酯共聚物中混合有防老化剂，所述防老化剂包括防老化剂N-445、防老化剂246、防老化剂4010、防老化剂SP、防老化剂RD、防老化剂0DA、防老化剂OD、防老化剂WH-02中的至少一种。所述防老化剂自身的质量份数为0.5-10份。
聚丙烯酸酯橡胶在使用过程中，随着使用时间的推移，聚丙烯酸酯共聚物的分子链会逐渐出现断裂，产生游离的自由基。这种现象是聚丙烯酸酯橡胶的自然老化现象。通过在聚丙烯酸酯共聚物中混合防老化剂，能够防止或中止、减缓聚丙烯酸酯橡胶中产生活性游离基的自催化现象。如果防老化剂的混合量过少，则有可能达不到延长聚丙烯酸酯橡胶的使用寿命的效果。而如果防老化剂的混合量过多，由于防老化剂难以与聚丙烯酸酯共聚物充分的互溶，难以均匀分散，因此有可能导致聚丙烯酸酯共聚物的力学性能下降。所以，在聚丙烯酸酯共聚物的质量份数为100份的情况下，防老化剂自身的质量份数可选在0.5-10份这一范围内。优选地，防老化剂自身的质量份数为1-5份。
可选地，所述聚丙烯酸酯共聚物中混合有内脱模剂。所述内脱模剂包括硬脂酸及硬脂酸盐、十八烷基胺和磷酸烷基酯、α-十八烷基-ω-羟基聚氧乙烯磷酸酯中的至少一种。
包括有“乙烯-丙烯酸酯共聚物”的聚丙烯酸酯橡胶的门尼粘度和生 胶强度相对较低。这一性能特点会导致聚丙烯酸酯橡胶在注塑加工工艺中出现粘辊、粘模等工艺问题。本发明通过在聚丙烯酸酯共聚物的胶料中加入内脱模剂的方式，改善该共聚物的加工性能。
如果内脱模剂的混合量较少，则难以达到改善粘膜问题。而如果混合量过大，容易导致聚丙烯酸酯橡胶在后期制备振膜时与胶层的粘接力下降，使最终制成的振膜的性能受到不利影响。在本发明的实施方式中，在聚丙烯酸酯共聚物的质量份数为100份的情况下，所述内脱模剂自身的质量份数可选为0.5-5份。优选地，内脱模剂自身的质量份数为1-3份。
可选地，所述振膜的玻璃化转变温度范围为-70～0℃。由于聚丙烯酸酯共聚物具有较高的分子量，并且其分子链较柔顺，具有较好的耐低温性能。振膜满足上述玻璃化转变温度的范围时，使得该扬声器振膜在常温下能够保持高弹态，回弹性良好。在一定范围，玻璃化转变温度越低，振膜即可在更低的温度下正常工作。在振膜的厚度不变的情况下，玻璃化转变温度越低，所装配的微型发声装置的谐振频率F0越低。
在一种实施方式中，对于上述ACM型共聚物，所述振膜的玻璃化转变温度范围可选为-60～0℃。优选为-50～-20℃。这使得在低于0℃时，扬声器振膜工作时可以一直保持较好的弹性，从而扬声器表现出较高的音质。同时，降低了在低温环境中扬声器振膜破坏的风险，可靠性更高。
在另一种实施方式中，对于上述AEM型共聚物，所述振膜的玻璃化转变温度的优选范围为-60～-20℃。这使得在低于0℃时，扬声器振膜工作时可以一直保持较好的弹性，从而扬声器表现出较高的音质。同时，降低了在低温环境中扬声器振膜破坏的风险，可靠性更高。
由于本发明采用的聚丙烯酸酯共聚物中含有大量的酯基，其在制成振膜时，能够与胶层可以形成氢键结合作用，因而具有优异的粘接性。可选地，聚丙烯酸酯共聚物与胶层的粘接力大于100g/25mm(180°剥离)，优选地，粘接力大于200g/25mm(180°剥离)。粘结力高使振膜在振动过程中与Dome的协调一致性良好，音质纯正，且在长时间振动后扬声器振膜仍然保持初始状态，性能稳定性高。
所述振膜的粘接力主要在两个方面发挥作用。在本发明的特殊实施方 式中，所述振膜可以是复合振膜，即振膜中包括了多层膜层，其中至少有一层膜层是采用上述聚丙烯酸酯共聚物制成的。多层膜层之间可以通过胶粘、热压等方式进行复合，进而构成上述复合振膜。聚丙烯酸酯共聚物的良好粘接性能能够保证复合振膜的结构稳定性和可靠性。另一方面，振膜在实际应用中需要与音圈、定心支片、补强件(DOME)等通过胶层粘接装配。振膜的良好粘接性能能够在装配中发挥作用，提高微型发声器产品的声学性能和结构可靠性。
可选地，所述胶层的类型包括环氧类、丙烯酸类、有机硅树脂类、聚酯类、聚氨酯类、氯醋树脂类、酚醛树脂类、脲醛树脂类中的一种或多种。
可选地，所述振膜的断裂伸长率大于100％。优选地，所述振膜的断裂伸长率大于150％。具有较高的断裂伸长率使得振膜在发声装置中使用时不易出现破膜等可靠性问题。
如图8所示，在相同的应力下，本发明实施例提供的振膜的应变明显大于现有技术的PEEK振膜。这表明，本发明实施例提供的振膜的杨氏模量明显小于现有技术的PEEK振膜。
此外，现有的PEEK振膜形成了明显的屈服点，约在应变0.4-0.5％。而本发明提供的扬声器振膜不存在屈服点，这表明，本发明提供的振膜具有更宽的弹性区域，并且回弹性能优良。
聚丙烯酸酯共聚物制成的振膜具有良好的柔韧性，例如，断裂伸长率≥100％。其中，聚乙烯嵌段对断裂伸长率有重要影响,本领域技术人员可以根据实际需要进行选择。这使得扬声器振膜的振动位移更大，响度更大。并且可靠性、耐用性良好。材料的柔韧性越好，断裂伸长率越大，则振膜抵抗破坏的能力越强。振膜处于大振幅状态振动时，材料产生了较大的应变，长时间振动时会出现膜折、膜裂或破膜的风险。而以聚丙烯酸酯共聚物作为基材的本发明的振膜，具有良好的柔韧性，降低了振膜破坏的风险。断裂伸长率越高，振膜在长期使用中的破膜率越低。
相对于工程塑料，本发明提供的聚丙烯酸酯共聚物具有更宽的弹性区域，在振膜的应变发生在该区域时，待外力去除后，振膜具有优异的回复性。相应地，振膜在振动过程中，摇摆振动少，音质和听音稳定性更优。 进一步地，可在200℃的温度下连续使用，并且具有相较于现有材料更高的阻尼性能。以AEM型共聚物制成的振膜为例，膜层产生20％应变后的弹性回复率≥90％。由于振膜的回弹性良好，故使得发声装置具有较好的瞬态响应和较低的失真。
如图9、10所示，本发发明提供的振膜相对于现有的PEEK振膜具有更低的THD(总谐波失真)及HOHD，并且无尖峰。这表明，本发明的振膜具有更优的抗偏振能力，并且音质更佳。
本发明提供的振膜在室温下处于高弹态，分子链易于运动，分子间摩擦力大，具有较好的阻尼性能。可选地，所述振膜的损耗因子大于0.06。优异的阻尼性能，使振膜具有更低的阻抗。所述振膜的阻尼性提高，发声装置的振动系统在振动过程中抑制偏振现象的能力得到增强，振动一致性良好。而现有的工程塑料制成的振膜的阻尼低，其损耗因子一般小于0.01，阻尼性较小。优选地，本发明提供的振膜的损耗因子大于0.1。
图11是根据本发明的一个实施例的发声装置的振膜不同部位在不同频率下振动位移的测试曲线。图12是现有振膜的不同部位在不同频率下振动位移的测试曲线。
其中，振膜为矩形折环振膜。横坐标为频率(Hz),纵坐标为响度位移量(mm)。在振膜的中心部的边缘位置以及中心位置取点进行测试。
可以看出，图11中的各个曲线更集中，而图12中的各个曲线较为分散。这表明，本发明实施例的发声装置的振膜的各个部分的振动一致性更好，在振动过程中，振膜的摇摆振动少，音质和听音稳定性更加优良。
可选地，所述振膜的邵氏硬度范围为15-90A，优选为20-80A。发声装置的谐振频率F0与振膜的模量、硬度以及厚度呈正比，而对于聚丙烯酸酯共聚物而言，其模量与硬度呈正比。因此，可以用硬度来体现振膜的模量。
聚丙烯酸酯共聚物的强度和硬度可以通过补强剂调节。另一方面，聚丙烯酸酯嵌段量的增加，会使得分子间氢键增多，进而使材料的强度和硬度增大、交联点增多。聚丙烯酸酯共聚物的强度和硬度越高，振膜的F0越高，相应的，发声装置的响度会有所降低，低音性能变差。图13为相同厚 度而不同硬度振膜的阻抗曲线，由图可以看出，随着硬度增大，F0急剧增大。
本发明提供的微型发声装置的振膜为折环振膜或者平板振膜。该发声装置的谐振频率F0正比于振膜的杨氏模量和厚度，可以通过改变扬声器振膜的厚度以及杨氏模量来实现F0的变化，具体调节原理如下：
Figure PCTCN2020085641-appb-000004
其中Mms为扬声器的等效振动质量，Cms为扬声器的等效顺性：
Figure PCTCN2020085641-appb-000005
其中，C m1为弹波顺性,C m2为振膜顺性。无弹波设计时，扬声器的等效顺性即为振膜顺性：
Figure PCTCN2020085641-appb-000006
其中W为振膜的折环部的总宽度，t为膜片厚度；dvc为振膜音圈贴合外径；E为振膜材质的杨氏模量；u为振膜材质的泊松比。
可见，发声装置的谐振频率F0正比于振膜的模量和厚度。而振膜的模量又正比于其硬度。因此，可以采用硬度替代其模量。为得到饱满的低音和舒适的听感，在发声装置具有较低的谐振频率F0的同时，应使振膜具有足够的刚度和阻尼。本领域技术人员可以通过调节扬声器振膜的硬度以及厚度来调节F0的大小。优选地，所述振膜的邵氏硬度优选为20-80A，所述振膜的厚度为60-120μm。在上述优选的范围内，能够使得微型发声装置的谐振频率F0达到150-1500Hz。微型发声装置的低频性能优良。
可选地，所述振膜可以为单层结构，也可以为多层的复合振膜。单层振膜是由一层聚丙烯酸酯共聚物膜层构成的振膜。而复合振膜则是由多层聚丙烯酸酯共聚物膜层依次层叠形成的振膜。或者，复合振膜可以包括至少一层聚丙烯酸酯共聚物膜层，该聚丙烯酸酯共聚物膜层与其它材料制成 的膜层层叠复合，构成多种材料制成的复合振膜。所述复合振膜可以为两层、三层、四层或五层复合振膜，本发明不对此进行限制。所述复合振膜中至少有一层膜层是由本发明提供的聚丙烯酸酯共聚物制成的聚丙烯酸酯共聚物膜层。
对于所述聚丙烯酸酯共聚物膜层，其厚度可选为10-200μm，优选为30-120μm。聚丙烯酸酯共聚物膜层的厚度在该范围内时，能够更好的满足微型发声装置的性能要求和装配空间的要求。
本发明给出了本发明提供的振膜的一个具体实施方式与现有常规振膜的对比曲线图，如图14所示。图14示出了两种振膜在不同频率下响度的测试曲线(SPL曲线)。振膜为折环振膜。横坐标为频率(Hz),纵坐标为响度。
其中，虚线为本发明提供的用于微型发声装置的振膜的测试曲线。实线为现有的常规振膜的测试曲线。
由SPL曲线可以看出，两种振膜的中频性能相近。而采用本发明提供的振膜的微型发声装置的F0为806Hz，即图中a处。采用现有振膜的发声装置的F0为886Hz，即图中b处。这表明，本发明实施例的振膜的低频灵敏度高于现有的PEEK振膜。也就是说，采用本发明提供的振膜，能够使微型发声装置具有更高的响度和舒适度。
本发明还提供了一种微型发声装置，该发声装置包括发声装置主体和上述采用聚丙烯酸酯共聚物制成的振膜。所述聚丙烯酸酯共聚物可以是上述的AEM型共聚物，也可以是上述的ACM型共聚物，本发明不对此进行限制。所述振膜设置在所述发声装置主体上，所述振膜被配置为能够被驱动振动，通过振动进而产生声音。所述发声装置主体中可以配置有线圈、磁路系统等部件，通过电磁感应驱动所述振膜振动。
虽然已经通过例子对本发明的一些特定实施例进行了详细说明，但是本领域的技术人员应该理解，以上例子仅是为了进行说明，而不是为了限制本发明的范围。本领域的技术人员应该理解，可在不脱离本发明的范围和精神的情况下，对以上实施例进行修改。本发明的范围由所附权利要求来限定。

Claims (16)

  1. 一种用于微型发声装置的振膜，其特征在于，所述振膜采用聚丙烯酸酯共聚物制成，所述聚丙烯酸酯共聚物中混合有增塑剂，所述增塑剂包括脂肪族二元酸酯类、苯二甲酸酯类、苯多酸酯类、苯甲酸酯类、多元醇酯类、氯化烃类、环氧类、柠檬酸酯类、聚酯类中的至少一种，所述振膜的玻璃化转变温度的范围为-70～0℃，所述振膜被配置为，在装配时与胶层之间的粘接力大于100g/25mm(180°剥离)。
  2. 根据权利要求1所述的振膜，其特征在于，所述聚丙烯酸酯共聚物采用丙烯酸烷基酯作为聚合主单体与交联单体交联聚合制成，所述振膜的玻璃化转变温度的范围为-60～0℃。
  3. 根据权利要求2所述的振膜，其特征在于，所述振膜的玻璃化转变温度的范围为-50～-20℃。
  4. 根据权利要求2所述的振膜，其特征在于，所述聚丙烯酸酯共聚物自身的质量份数为100份，所述增塑剂自身的质量份数为1-13份。
  5. 根据权利要求2所述的振膜，其特征在于，所述聚丙烯酸酯共聚物中混合有硫化剂，所述聚丙烯酸酯共聚物自身的质量份数为100份，所述硫化剂自身的质量份数为0.5-5份。
  6. 根据权利要求1所述的振膜，其特征在于，所述聚丙烯酸酯共聚物包括“乙烯-丙烯酸酯共聚物”和“乙烯-丙烯酸酯-羧酸共聚物”中的至少一种。
  7. 根据权利要求6所述的振膜，其特征在于，所述振膜的玻璃化转变温度的范围为-60～-20℃。
  8. 根据权利要求6所述的振膜，其特征在于，所述聚丙烯酸酯共聚物自身的质量份数为100份，所述增塑剂自身的质量份数为1-10份。
  9. 根据权利要求1所述的振膜，其特征在于，所述振膜与胶层之间的粘接力大于200g/25mm(180°剥离)。
  10. 根据权利要求1所述的振膜，其特征在于，所述聚丙烯酸酯共聚物中混合有内脱模剂，所述内脱模剂包括硬脂酸及硬脂酸盐、十八烷基胺 和磷酸烷基酯、α-十八烷基-ω-羟基聚氧乙烯磷酸酯中的至少一种，所述聚丙烯酸酯共聚物自身的质量份数为100份，所述内脱模剂自身的质量份数为0.5-5份。
  11. 根据权利要求10所述的振膜，其特征在于，所述内脱模剂自身的质量份数为1-3份。
  12. 根据权利要求1所述的振膜，其特征在于，所述振膜为单层振膜，所述单层振膜采用一层聚丙烯酸酯共聚物膜层构成；
    或者，所述振膜为复合振膜，所述复合振膜包括两层、三层、四层或五层膜层，所述复合振膜至少包括一层聚丙烯酸酯共聚物膜层。
  13. 根据权利要求12所述的振膜，其特征在于，所述聚丙烯酸酯共聚物膜层的厚度为10-200μm。
  14. 根据权利要求13所述的振膜，其特征在于，所述聚丙烯酸酯共聚物膜层的厚度为30-120μm。
  15. 根据权利要求1所述的振膜，其特征在于，所述胶层的类型包括环氧类、丙烯酸类、有机硅树脂类、聚酯类、聚氨酯类、氯醋树脂类、酚醛树脂类、脲醛树脂类中的一种或多种。
  16. 一种微型发声装置，其特征在于，包括发声装置主体和权利要求1-15任意之一所述的振膜，所述振膜设置在所述发声装置主体上，所述振膜被配置为能振动发声。
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CN111866670A (zh) 2020-10-30

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