JP2010110898A - Heat laminate laminated film and method for manufacturing the same - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide a PPS heat laminate laminated film which is superior in moldability and carbon dioxide gas coolant resistance. <P>SOLUTION: The laminated film has a structure in which a biaxially oriented polyarylene sulfide film and a biaxially oriented copolymerized polyarylene sulfide film are heat laminate-laminated without making an adhesive layer intervene between them. The heat laminate laminated film has an elongation at break at room temperature of 80% or above 160% or below and 100 or below bubbles of at least 5 mm per 1 m<SP>2</SP>after being subjected to a carbon dioxide gas coolant-proof recycle test. <P>COPYRIGHT: (C)2010,JPO&INPIT

Description

  The present invention relates to a heat laminated laminated film excellent in moldability and carbon dioxide gas resistance.

  Polyarylene sulfide film has excellent properties such as heat resistance, flame retardancy, rigidity, chemical resistance, electrical insulation and low moisture absorption, especially for electrical / electronic equipment, mechanical parts and automotive parts. It is preferably used.

  In recent years, polyphenylene sulfide (hereinafter sometimes abbreviated as PPS) films have been applied to electrical insulating materials by taking advantage of their high electrical insulation and low hygroscopicity. For example, it is known that (1) a biaxially oriented film is used as an electrical insulating material (see Patent Document 1). In addition, (2) a laminate in which a biaxially oriented PPS layer is laminated on an unoriented PPS layer without using an adhesive is known (see Patent Document 2 and Patent Document 3). Furthermore, (3) a thick laminate film in which a copolymerized polyphenylene sulfide laminate film is laminated by thermal lamination is known (Patent Document 4).

Also, (4) a refrigerant compressor using carbon dioxide as a working refrigerant and a heat pump water heater equipped with the refrigerant compressor are known (Patent Document 5). (5) about 150 kg / cm ² refrigerant pressure in the refrigerant compressor using the carbon dioxide in the high pressure side, the low-pressure side is disclosed to be a 30-40 kg / cm ² (Patent Document 6). In addition, (6) PPS blister generation is disclosed in a cycle test of a refrigerant compressor using carbon dioxide (Patent Document 7).

Conventional films and sheets, laminated films, and laminates have the following problems. That is, when the film of the above item (1) is used as a slot liner or wedge of a motor, there is a problem that the film is torn or the film is torn. Also, in the laminate of the above item (2) or (3), there has been a problem that the film is torn when used as a slot liner or wedge of a motor. Moreover, in order to ensure electrical insulation, a thick film exceeding 100 μm is used as the film used for the above-mentioned applications (4) to (6), but a PPS film is a film extrusion method exceeding 100 μm. Therefore, it is difficult to form a film by using a non-oriented PPS or a copolymerized PPS as an adhesive layer, as disclosed in the above (2) or (3), and by laminating the PPS films with each other, It was filmed. However, such a thick PPS film according to the conventional method has a problem that bubbles are generated at the interface of the heat laminate depending on the environment in which it is used.
JP 55-35456 A JP-A-2-45144 Japanese Patent No. 2956254 JP 2007-089441 A JP 2008-95506 A JP 2000-97177 A Japanese Patent Laid-Open No. 2004-6002

  Accordingly, an object of the present invention is to solve these problems and to provide a heat-laminated laminated film excellent in moldability and carbon dioxide gas refrigerant resistance.

That is, the present invention is a heat laminated laminated film having a structure in which a biaxially oriented polyarylene sulfide film and a biaxially oriented copolymerized polyarylene sulfide film are laminated without an adhesive layer, A heat laminated laminate film having a room temperature breaking elongation of 80% or more and 160% or less, and 100 bubbles or less having a diameter of 5 mm or more per 1 m ² of the heat laminated laminate film after the carbon dioxide gas refrigerant cycle test. In addition, a biaxially oriented two-layer laminated polyarylene sulfide film obtained by co-extrusion and co-extrusion so that polyarylene sulfide and copolymer polyarylene sulfide are the outermost layers, respectively, and separately prepared polyarylene Sulfide film roll surface temperature is 230 ° C or higher The present invention is intended to be a method for producing a heat-laminated laminated film, characterized in that it is thermocompression bonded after contacting a metal roll heated to 1.5 seconds or longer.

According to the present invention, a heat-laminated laminated film having excellent moldability and carbon dioxide gas refrigerant resistance can be obtained.

  The heat-laminated laminated film of the present invention can be used for various motor electric insulation molding materials such as a drive motor for a hybrid vehicle, a car air conditioner compressor motor, or a water heater motor, and in particular, motor electric insulation using a carbon dioxide refrigerant. It is suitably used for a molding material.

  The polyarylene sulfide used in the present invention is a homopolymer or copolymer having a repeating unit of-(Ar-S)-(this polyarylene sulfide is also referred to as a first PAS for convenience). Examples of Ar include units represented by the following formulas (A) to (K).

(R1 and R2 are substituents selected from hydrogen, an alkyl group, an alkoxy group, and a halogen group, and R1 and R2 may be the same or different.)
Preferable Ar is represented by the above formula (A), and typical examples thereof include polyphenylene sulfide, polyphenylene sulfide sulfone, polyphenylene sulfide ketone, random copolymers thereof, block copolymers and the like. And the like. Particularly preferred polyarylene sulfide is preferably polyphenylene sulfide (PPS) from the viewpoint of film properties and economy, and a poly-p-phenylene sulfide unit represented by the following structural formula is preferably used as the main structural unit of the polymer. It is a resin containing more than mol%, more preferably 95 mol% or more. When the poly-p-phenylene sulfide component is 92 mol% or less, the crystallinity and thermal transition temperature of the polymer are low, and the heat resistance, dimensional stability, mechanical properties, dielectric properties, etc., which are the characteristics of PPS, may be impaired. .

  As long as it is less than 8 mol% of the repeating unit, a unit containing a copolymerizable sulfide bond may be contained. Examples of such repeating units include trifunctional units, ether units, sulfone units, ketone units, meta bond units, aryl units having substituents such as alkyl groups, biphenyl units, terphenylene units, vinylene units, carbonate units. These are given as specific examples, and one or more of them can coexist. In this case, the structural unit may be in any form of random copolymerization or block copolymerization.

  The biaxially oriented film made of polyarylene sulfide as used in the present invention is a resin composition containing 80% by weight or more, preferably 90% by weight or more of the first PAS, melt-molded into a sheet, biaxially stretched and heat-treated. It is a film. When the content of the first PAS is less than 80% by weight, the crystallinity as the composition is lowered, and the heat resistance, thermal dimensional stability, hydrolysis resistance, and the like of the film may be impaired. The thermoplastic resin other than the first PAS preferably has, for example, a glass transition temperature of 150 ° C. or higher and a melting point of the first PAS or lower in order to obtain the moldability of the present invention. The glass transition temperature is more preferably 170 ° C. or higher and 250 ° C. or lower, and further preferably 190 ° C. or higher and 230 ° C. or lower. When the glass transition temperature is less than 150 ° C., the heat resistance of the biaxially oriented film made of polyarylene sulfide may be impaired, and when the glass transition temperature exceeds the melting point of the first PAS, the film forming property may be deteriorated. Examples of the thermoplastic resin having a glass transition temperature of 150 ° C. or higher include various polymers such as polyarylate, polyetherimide, polyethersulfone, polysulfone, polyphenylene ether, polyamideimide, polycarbonate, and polycycloolefin, and polymers of these polymers. A blend containing at least one kind can be used. In the present invention, from the viewpoint of the mixing property with the first PAS and the manifestation of the effect of the present invention, at least one selected from polyetherimide, polyethersulfone, and polysulfone is preferably used, and polyetherimide is particularly preferably used.

  Although such polyetherimide is not particularly limited, for example, as shown by the following general formula, a polymer which is a structural unit containing an ether bond in a polyimide constituent component can be preferably exemplified.

  However, R1, R2 in the above formula is a divalent organic group selected from the group consisting of a divalent aromatic or aliphatic group having 2 to 30 carbon atoms, and an alicyclic group. It may be different. As said R1, R2, the aromatic group shown by the following formula group can be mentioned, for example.

  In the present invention, when a polyetherimide having a glass transition temperature of 250 ° C. or lower is used, the effects of the present invention can be easily obtained, and the structural unit represented by the following formula is included from the viewpoint of compatibility with the first PAS, melt moldability, and the like. 2,2-bis [4- (2,3-dicarboxyphenoxy) phenyl] propane dianhydride and m-phenylenediamine or p-phenylenediamine are preferred.

  A polyetherimide having this structural unit is available from Subic Innovative Plastics (formerly GE Plastics) under the trade name “Ultem” (registered trademark). For example, “Ultem 1000” and “Ultem 1010” may be mentioned as polyetherimide having a structural unit (former formula) containing a unit derived from m-phenylenediamine. Moreover, “Ultem CRS5000” is mentioned as a polyetherimide having a structural unit (the latter formula) containing a unit derived from p-phenylenediamine.

  As a compatibilizing agent from the viewpoint of improving the dispersibility of other thermoplastic resins contained in the biaxially oriented film comprising the polyarylene sulfide referred to in the present invention, it has one or more groups selected from an epoxy group, an amino group, and an isocyanate group. It is preferable to contain 0.1-3 weight part of compounds with respect to a total of 100 weight part of 1st PAS and the said thermoplastic resin.

  Specific examples of such compatibilizers include bisphenol A, resorcinol, hydroquinone, pyrocatechol, bisphenol F, saligenin, 1,3,5-trihydroxybenzene, bisphenol S, trihydroxy-diphenyldimethylmethane, 4,4′- Dihydroxybiphenyl, 1,5-dihydroxynaphthalene, cashew phenol, 2.2.5.5. -Glycidyl ethers of bisphenols such as tetrakis (4-hydroxyphenyl) hexane, those using halogenated bisphenol instead of bisphenol, glycidyl ether type epoxy compounds such as diglycidyl ether of butanediol, glycidyl such as glycidyl phthalate Glycidyl epoxy resins such as ester compounds, glycidylamine compounds such as N-glycidylaniline, linear epoxy compounds such as epoxidized polyolefin and epoxidized soybean oil, cyclic systems such as vinylcyclohexene dioxide and dicyclopentadiene dioxide Non-glycidyl epoxy resin etc. are mentioned. In addition, other novolac type epoxy resins are also included. The novolac type epoxy resin has two or more epoxy groups and is usually obtained by reacting a novolac type phenol resin with epichlorohydrin. Moreover, a novolak type phenol resin is obtained by a condensation reaction of phenols and formaldehyde. Although there is no restriction | limiting in particular as phenols of a raw material, A phenol, o-cresol, m-cresol, p-cresol, bisphenol A, resorcinol, p-tertiary butylphenol, bisphenol F, bisphenol S, and these condensates are mentioned.

  Moreover, the olefin copolymer which has another epoxy group is also mentioned. Examples of the olefin copolymer having an epoxy group (epoxy group-containing olefin copolymer) include an olefin copolymer obtained by introducing a monomer component having an epoxy group into an olefinic (co) polymer. . Moreover, the copolymer which epoxidized the double bond part of the olefin polymer which has a double bond in a principal chain can also be used.

  Examples of functional group-containing components for introducing a monomer component having an epoxy group into an olefinic (co) polymer include glycidyl acrylate, glycidyl methacrylate, glycidyl ethacrylate, glycidyl itaconate, glycidyl citraconic acid, etc. And a monomer containing an epoxy group. The method for introducing these epoxy group-containing components is not particularly limited, and methods such as copolymerization with α-olefin and the like, or graft introduction to an olefin (co) polymer using a radical initiator can be used.

  The introduction amount of the monomer component containing an epoxy group is 0.001 to 40 mol%, preferably 0.01 to 35 mol% with respect to the whole monomer as a raw material of the epoxy group-containing olefin copolymer. It is appropriate to be within the range.

  As an epoxy group-containing olefin copolymer particularly useful in the present invention, an olefin copolymer having an α-olefin and a glycidyl ester of an α, β-unsaturated carboxylic acid as a copolymerization component is preferably exemplified. As said alpha olefin, ethylene is mentioned preferably. These copolymers further include α, β-unsaturated carboxylic acids such as acrylic acid, methyl acrylate, ethyl acrylate, butyl acrylate, methacrylic acid, methyl methacrylate, ethyl methacrylate, butyl methacrylate, and the like. It is also possible to copolymerize the alkyl ester, styrene, acrylonitrile and the like. Such an olefin copolymer may be any random, alternating, block, or graft copolymerization mode. An olefin copolymer obtained by copolymerizing an glycidyl ester of an α-olefin and an α, β-unsaturated carboxylic acid is, among others, a glycidyl ester 1 of 60 to 99% by weight of an α-olefin and an α, β-unsaturated carboxylic acid. An olefin copolymer obtained by copolymerizing ˜40% by weight is particularly preferable. Specific examples of the glycidyl ester of α, β-unsaturated carboxylic acid include glycidyl acrylate, glycidyl methacrylate, and glycidyl ethacrylate. Among them, glycidyl methacrylate is preferably used. As a specific example of an olefin copolymer having an α-olefin and a glycidyl ester of α, β-unsaturated carboxylic acid as an essential copolymerization component, an ethylene / propylene-g-glycidyl methacrylate copolymer ("g" Representing a graft, the same applies hereinafter), ethylene / butene-1-g-glycidyl methacrylate copolymer, ethylene-glycidyl methacrylate copolymer-g-polystyrene, ethylene-glycidyl methacrylate copolymer-g-acrylonitrile-styrene copolymer Polymer, ethylene-glycidyl methacrylate copolymer-g-PMMA, ethylene / glycidyl acrylate copolymer, ethylene / glycidyl methacrylate copolymer, ethylene / methyl acrylate / glycidyl methacrylate copolymer, ethylene / methyl methacrylate / Glycidi methacrylate Copolymers thereof.

  Furthermore, specific examples of the compatibilizing agent include alkoxysilanes having one or more functional groups selected from epoxy groups, amino groups, and isocyanate groups. Specific examples of such compounds include epoxy group-containing alkoxysilanes such as γ-glycidoxypropyltrimethoxysilane, γ-glycidoxypropyltriethoxysilane, and β- (3,4-epoxycyclohexyl) ethyltrimethoxysilane. Compounds, ureido group-containing alkoxysilane compounds such as γ-ureidopropyltriethoxysilane, γ-ureidopropyltrimethoxysilane, γ- (2-ureidoethyl) aminopropyltrimethoxysilane, γ-isocyanatopropyltriethoxysilane, γ-isocyanatopropyltrimethoxysilane, γ-isocyanatopropylmethyldimethoxysilane, γ-isocyanatopropylmethyldiethoxysilane, γ-isocyanatopropylethyldimethoxysilane, γ-isocyanatopropylethyldisilane Isocyanato group-containing alkoxysilane compounds such as toxisilane, γ-isocyanatopropyltrichlorosilane, γ- (2-aminoethyl) aminopropylmethyldimethoxysilane, γ- (2-aminoethyl) aminopropyltrimethoxysilane, γ-amino Examples include amino group-containing alkoxysilane compounds such as propyltrimethoxysilane.

  An alkoxysilane having one or more functional groups selected from the above epoxy group, amino group, and isocyanate group is preferred as a compatibilizing agent of the present invention. Among them, an alkoxysilane having an isocyanate group contains a thermoplastic resin. It is easy to reduce the coarse dispersion due to poor dispersion of the disperse phase of the biaxially oriented film made of polyarylene sulfide, it is easy to control the average dispersion diameter within the preferred range of the present invention, and the effect of the present invention is most easily obtained. preferable.

In addition, when an alkoxysilane having one or more functional groups selected from an epoxy group, an amino group, and an isocyanate group is used, a siloxane bond is easily formed between the polyarylene sulfide and the thermoplastic resin, and in the vicinity of the interface of the dispersed phase. In this case, siloxane bonds are likely to exist. Silicon atoms can be detected in the vicinity of the interface of the dispersed phase using a TEM-EDX method or the like. In the present invention, it is preferable that silicon (Si) atoms derived from siloxane bonds are included at the interface of the dispersed phase made of the thermoplastic resin.
The content of the compatibilizer having one or more functional groups selected from the epoxy group, amino group, and isocyanate group is 0 when the sum of the polyarylene sulfide and the thermoplastic resin content is 100 parts by weight. 0.05 to 3 parts by weight, preferably 0.1 to 1 part by weight, and more preferably 0.2 to 0.5 part by weight. When the content of the compatibilizer is less than 0.05 parts by weight, the dispersibility of the thermoplastic resin may deteriorate. If the content of the compatibilizer exceeds 3 parts by weight, gas may be generated due to the reaction of the unreacted end groups of the compatibilizer during film formation, and film formation may occur frequently or the elongation at break of the film may increase. It may decrease.

  The preferable average dispersion diameter of the thermoplastic resin is 50 to 500 nm, more preferably 70 to 300 nm, and still more preferably 100 to 200 nm. By setting the average dispersion diameter within the above range, it is possible to obtain a biaxially oriented polyarylene sulfide film having an excellent balance between heat resistance and moldability improvement. If the average dispersed diameter of the dispersed phase is less than 50 nm, the moldability of the present invention may not be sufficiently imparted. When the average dispersion diameter is larger than 500 nm, heat resistance may be deteriorated, or film breakage may occur during film-forming stretching.

    The copolymerized polyarylene sulfide used in the present invention is a copolymer having a repeating unit of-(Ar-S)-(hereinafter also referred to as a second PAS for convenience). Examples of Ar include units represented by the following formulas (A) to (K).

(R1 and R2 are substituents selected from hydrogen, an alkyl group, an alkoxy group, and a halogen group, and R1 and R2 may be the same or different.)
Preferable Ar is represented by the above formula (A), and typical examples thereof include polyphenylene sulfide, polyphenylene sulfide sulfone, random copolymer of polyphenylene sulfide ketone, and block copolymer. .

  However, the second PAS includes a different structural unit from the first PAS, or has a different copolymerization ratio even if a common structural unit is used. The melting point and / or glass transition temperature of the second PAS is preferably 10 ° C. or higher, more preferably 15 ° C. or higher, lower than that of the first PAS.

  A particularly preferred second PAS is exemplified by a random copolymer or block copolymer of polyphenylene sulfide (PPS) from the viewpoint of film properties and economy, and a poly-p represented by the following structural formula as a main structural unit of the polymer. It is preferable that the phenylene sulfide unit is contained in an amount of 80 mol% or more and 92 mol% or less. When the poly-p-phenylene sulfide component is less than 80 mol%, the crystallinity and thermal transition temperature of the polymer are low, and heat resistance, dimensional stability, mechanical properties, dielectric properties, and the like may be impaired. If it exceeds 92 mol%, the interfacial adhesion cannot be sufficiently improved, and the carbon dioxide gas refrigerant resistance and moldability of the present invention may not be sufficient.

The second PAS is preferably a trifunctional unit of 8 mol% or more and 20 mol% or less of a repeating unit, an ether unit, a sulfone unit, a ketone unit, a meta bond unit, an aryl unit having a substituent such as an alkyl group, a biphenyl unit, a terphenylene. Includes arylene sulfide units including units, vinylene units, carbonate units.
An example of such a unit is as follows.

(Here, X represents an ether, alkylene, CO, or SO ₂ unit.)

(Here, R represents an alkyl, nitro, phenylene, or alkoxy group.)
A desirable structural unit is m-phenylene sulfide. The copolymerization amount of the arylene sulfide structural unit containing these units is preferably 8 mol% or more and 20 mol% or less, more preferably 10 mol% or more and 18 mol% or less. When the copolymerization amount is less than 8 mol%, the interfacial adhesion of the heat-laminated laminated film cannot be sufficiently increased, and the carbon dioxide gas refrigerant resistance and moldability may not be sufficiently increased. When it exceeds 20 mol%, the heat resistance may be significantly lowered.

  In the second PAS, the mode of copolymerization is not particularly limited, but is preferably a random copolymer.

  In the second PAS, the copolymerization amount of the trifunctional phenyl sulfide is preferably 1 mol% or less.

  The melting point of the second PAS is preferably 210 ° C. or higher and 260 ° C. or lower, more preferably 220 ° C. or higher and 260 ° C. or lower, and further preferably 230 ° C. or higher and 260 ° C. or lower. When the melting point of the second PAS is less than 210 ° C., the heat resistance may be significantly reduced, and when it exceeds 260 ° C., the interfacial adhesion with the biaxially oriented film made of polyarylene sulfide may not be sufficiently improved. Carbon dioxide refrigerant properties and moldability may deteriorate. The melting point of the second PAS can be appropriately adjusted depending on the molar ratio of the copolymerization components.

  The biaxially oriented film comprising the copolymerized polyarylene sulfide used in the present invention is a resin composition containing 80% by weight or more, preferably 90% by weight or more of the second PAS. It is a film formed by heat treatment. When the content of the second PAS is less than 80% by weight, the interfacial adhesiveness with the biaxially oriented film made of polyarylene sulfide may be impaired. Less than 20% by weight in the composition can contain polymers other than the second PAS. Examples of the polymer other than the second PAS include various polymers such as polyamide, polyetherimide, polyethersulfone, polysulfone, polyphenylene ether, polyester, polyarylate, polyamideimide, polycarbonate, polyolefin, polyetheretherketone, and polymers of these polymers. Mention may be made of blends comprising at least one.

  The thickness of the biaxially oriented film comprising the copolymerized polyarylene sulfide film referred to in the present invention is preferably 5 μm or more and 50 μm or less, more preferably 10 μm or more and 30 μm or less, and further preferably 10 μm or more and 20 μm or less. When the thickness of the biaxially oriented copolymer polyarylene sulfide film is less than 5 μm, the interfacial adhesiveness of the heat laminate laminate film may not be sufficiently obtained, and the carbon dioxide gas refrigerant resistance may be deteriorated. The heat resistance of the laminated film may decrease. Further, the biaxially oriented film having a polyarylene sulfide layer used in the present invention as an outermost layer is an outermost layer on at least one surface of the resin composition containing the first PAS in an amount of 80% by weight or more, preferably 90% by weight or more. It is a film formed by coextrusion with a thermoplastic resin other than the first PAS so as to have a sheet shape, biaxial stretching, and heat treatment, and a biaxially oriented film having a layer made of copolymerized polyarylene sulfide as the outermost layer is A resin composition containing 80% by weight or more, preferably 90% by weight or more of the second PAS is coextruded with a thermoplastic resin other than the second PAS in the outermost layer on at least one surface thereof to form a sheet, biaxially stretched, and heat-treated. Is a film. Here, the other thermoplastic resin is not particularly limited as long as it can be coextruded with the first PAS or the second PAS to form a sheet in each case.

  The biaxially oriented two-layer laminated polyarylene sulfide film used in the present invention is a biaxially oriented film having a biaxially oriented film having a layer made of the polyarylene sulfide as an outermost layer and a layer made of a copolymerized polyarylene sulfide in the outermost layer. It is a special embodiment of the film, and comprises a resin composition containing 80% by weight or more, preferably 90% by weight or more of the first PAS and a resin composition containing 80% by weight or more, preferably 90% by weight or more of the second PAS, respectively. It is a film formed by coextrusion, biaxial stretching and heat treatment so that The layer other than the outermost layer is not particularly limited, but the resin composition containing the first PAS at 80% by weight or more, preferably 90% by weight or more is regarded as the a layer, and the second PAS is 80% by weight or more, preferably 90% by weight or more. When the layer composed of the resin composition is viewed as layer b, it may be laminated in multiple layers such as a / b / a / b or a / b / a / b / a / b. The laminated structure can be appropriately changed depending on the thickness of the heat laminated laminated film.

  Biaxially oriented film made of polyarylene sulfide used in the present invention, biaxially oriented film having a layer made of polyarylene sulfide as an outermost layer, biaxially oriented film made of copolymerized polyarylene sulfide, and layer made of copolymerized polyarylene sulfide The biaxially oriented film having the outermost layer and the biaxially oriented two-layer laminated polyarylene sulfide film are heat stabilizers, antioxidants, ultraviolet absorbers, antistatic agents, difficult to the extent that the effects of the present invention are not impaired. Other components such as organic lubricants such as flame retardants, pigments, dyes, fatty acid esters and waxes may be added. In addition, inorganic particles, organic particles, and the like can be added in order to impart slipperiness, abrasion resistance, scratch resistance, and the like to the film surface. Examples of such additives include clay, mica, titanium oxide, calcium carbonate, kaolin, talc, wet or dry silica, colloidal silica, calcium phosphate, barium sulfate, alumina, zirconia, and other inorganic particles, acrylic acids, styrene And so-called internal particles, surfactants, and the like, which are precipitated by a catalyst added during the polymerization reaction of polyarylene sulfide.

  The biaxially oriented copolymer polyarylene sulfide film may be subjected to any processing such as heat treatment, molding, surface treatment, laminating, coating, printing, embossing and etching as necessary.

  In the present invention, the heat laminated laminate film is obtained by heat laminating the surface of the film desirably containing 80% by weight or more of the first PAS and the surface of the film desirably containing 80% or more of the second PAS. is there. Examples of such an embodiment include, for example, (1) an embodiment in which a biaxially oriented film made of polyarylene sulfide and a biaxially oriented film made of copolymerized polyarylene sulfide are thermally laminated, and (2) a biaxially oriented film made of polyarylene sulfide. A mode in which a biaxially oriented film having a layer made of a film and a copolymerized polyarylene sulfide as an outermost layer is thermally laminated on the outermost layer side, (3) Biaxially oriented having a layer made of a polyarylene sulfide as an outermost layer A mode in which the outermost layer side surface of the film and the outermost layer side surface of the biaxially oriented film having a layer made of copolymerized polyarylene sulfide as the outermost layer are thermally laminated, (4) Two biaxially oriented 2 layers Layer of polyarylene sulfide film of layer-laminated polyarylene sulfide film and copolymer polyarylene with the outermost surface A layer comprising Rufido the like manner the surface of the outermost layer to heat lamination. Of these, the embodiments (2), (3) and (4) are preferred, and the embodiment (4) is most preferred.

  The thickness of the heat laminate laminate film of the present invention is preferably 125 μm or more and 500 μm or less, more preferably 200 μm or more and 400 μm or less, and further preferably 250 μm or more and 350 μm or less. If the thickness is less than 125 μm, the electric insulation as a motor insulating film may not be sufficient. If the thickness exceeds 500 μm, the interfacial adhesion of the heat-laminated laminated film is lowered, and the carbon dioxide refrigerant resistance and moldability deteriorate. There is a case.

  The heat-laminated laminated film of the present invention needs to be biaxially oriented for each layer constituting the heat-laminated laminated film. The orientation of each layer can be determined by measuring the cross section of the heat-laminated laminated film by laser Raman spectroscopy. When the biaxially oriented polyarylene sulfide film is oriented, the orientation parameter obtained by laser-Raman spectroscopy is preferably in the range of 2.0 to 8.0, more preferably 2.5. ~ 6.0. When the orientation parameter exceeds 8.0, the molecular chain orientation may proceed excessively or the crystallization may proceed excessively, resulting in damage during processing or use of the film, or in practical use. On the other hand, when the orientation parameter is less than 2.0, the molecular chain orientation may be insufficient or the progress of crystallization may be insufficient, which may reduce the heat resistance of the structure. On the other hand, it can be said that the layer containing the second PAS is oriented if the orientation parameter obtained by laser Raman spectroscopy is 1.3 or more.

  In order to set the orientation parameter within the above range, for example, the stretching temperature and stretching ratio in longitudinal stretching, the preheating temperature before transverse stretching, the stretching temperature and stretching ratio in transverse stretching, and the heat setting temperature after stretching are adjusted according to the present invention. It becomes possible to obtain by making it into a preferable range. The measurement method by the laser Raman spectroscopy is not particularly limited. For example, a laser Raman apparatus (PDP320 (manufactured by Photon Design)) is used, the microprobe objective lens is 100 times, and the objective lens is in the near infrared region (1064 to 1300 nm). ) Having transparency, NA of 0.95, and chromatic aberration correction can be used. Cross slit 1 mm, spot diameter 1 μm, light source Nd-YAG (wavelength 1064 nm, output: 1 W), diffraction grating Spectrograph 300 g / mm, slit: 100 μm, detector InGaAs (Roper Scientific 512) is preferably used.

The film used for measurement is sampled and embedded in an epoxy resin, and then the film cross section is prepared with a microtome. The film cross section was adjusted to be parallel to the film longitudinal direction or the width direction, and the average value was obtained by measuring five samples for each of the longitudinal direction and the width direction with the central point of each sample as the measurement point. . Measurement is performed through a polarizer placed in a polarization direction parallel to the polarization direction of the incident light, the sample is rotated, and the spectrum is measured in a polarization direction perpendicular to the polarization direction parallel to the film surface with respect to the polarization direction of the laser light. Got. The orientation parameter is
(Orientation parameter) = (I1575 / I740) (Parallel) / (I1575 / I740) (Vertical)
I1575 / I740 (parallel): In the Raman spectrum measured in the polarization direction parallel to the film surface, the Raman band near 1575 cm-1 is divided by the Raman band intensity near 740 cm-1.
I1575 / I740 (vertical): In the Raman spectrum measured in the polarization direction perpendicular to the film surface, the Raman band near 1575 cm-1 was divided by the Raman band intensity near 740 cm-1.

  The elongation at break of the heat-laminated laminated film of the present invention at room temperature is required to be from 80% to 160% in order to obtain moldability. More preferably, they are 100% or more and 160% or less, More preferably, they are 120% or more and 160% or less. If the elongation at break at room temperature is less than 80%, film cracking may occur in the motor processing process, and even if it can be processed, the film surface layer cracks when touched with a carbon dioxide-resistant refrigerant, and the film peels away from that part. Then, bubbles may expand. The upper limit of the elongation at break is not particularly provided, but if it exceeds 160%, the strength of the film is lowered and the heat resistance of the film may be lowered. The room temperature breaking elongation of the heat-laminated laminated film of the present invention is an average breaking elongation in the film longitudinal direction and width direction. In order to set the room temperature breaking elongation of the heat-laminated laminated film of the present invention within the above range, the film before heat-laminated lamination was formed according to the draw ratio and heat treatment conditions described separately, and the obtained biaxially oriented film Can be obtained by a method such as obtaining by heat laminating under the laminating conditions described later.

The heat-laminated laminated film of the present invention is improved in the resistance to carbon dioxide gas refrigerant of the present invention by having 100 or less bubbles having a maximum diameter of 5 mm or more around 1 m ² of the heat-laminated laminated film after the carbon dioxide gas refrigerant cycle test. Is important in terms of The carbon dioxide gas refrigerant cycle test is a method in which 125 sheets (1 m ² minutes) of 80 cm ² of laminated laminated films are put in an autoclave (500 cc manufactured by Pressure Glass Industrial Co., Ltd.) under an atmosphere of initial conditions of −20 ° C. After injecting carbon dioxide gas to 4.5 MPa, the temperature is raised to 100 ° C. at 20 ° C./min. Further, after confirming that the pressure in the autoclave is 10 MPa or more, the leak valve is opened to release the pressure at once. This is performed as 30 cycles.

The number of bubbles having a maximum diameter of 5 mm or more contained in 1 m ^{2 of the} sample after the carbon dioxide gas refrigerant cycle test is preferably 50 or less, more preferably 30 or less, and bubbles having a maximum diameter of 5 mm or more are generated. It is most desirable not to. In order to make the bubbles after the carbon dioxide gas refrigerant cycle test of the heat laminated laminated film within the above range, it can be obtained, for example, by laminating by a laminating method described later.

Furthermore, the heat-laminated laminated film of the present invention preferably has 1000 or less, more preferably 500, bubbles having a maximum diameter of 1 mm or more and less than 5 mm around 1 m ² of the heat-laminated laminated film after the carbon dioxide gas refrigerant cycle test. Or less, more preferably 250 or less. The lower limit is not particularly limited, but it is desirable that such bubbles do not exist.

  The bubbles observed after the carbon dioxide gas refrigerant cycle test are formed by peeling at the interface of the heat-laminated laminated film, and can be distinguished by visual observation. The maximum diameter of the bubbles is literally the length of the longest line segment connecting the two arbitrary points on the outer edge of the bubble. It is presumed that the bubbles are generated when pressure is applied to the interface of the heat-laminated laminated film in the process of sudden pressure reduction in the carbon dioxide gas refrigerant cycle test, and peeling occurs at a weak interface adhesion portion.

  The heat-laminated laminated film of the present invention is laminated by heat laminating the surface of the film desirably containing 80% by weight or more of the first PAS and the surface of the film desirably containing 80% or more of the second PAS without interposing an adhesive layer. Has been. As a specific method of laminating without using an adhesive layer, a heat laminating method by heat fusion is preferably used. The method of thermal lamination is not particularly limited, but thermal lamination using a heating roll is preferable from the viewpoint of processability.

  The use of the heat laminated laminated film of the present invention is not particularly limited, but can be used as an insulating material for various motors such as a drive motor, an air conditioner compressor motor, or a water heater motor used in a hybrid vehicle. It is suitable as an insulating material for a compressor motor using a gas refrigerant.

  Next, regarding the method for producing the heat laminated laminated film of the present invention, poly-m-phenylene sulfide copolymer obtained by using poly-p-phenylene sulfide resin as the first PAS and copolymerizing m-phenylene sulfide with PPS as the second PAS. The production of a heat-laminated laminated film using a poly-p-phenylene sulfide resin (hereinafter sometimes abbreviated as m-PPS resin) will be described as an example, but the present invention is not limited to the following description. Of course.

  Examples of the method for producing the PPS resin include the following methods. Sodium sulfide and p-dichlorobenzene are reacted in an amide polar solvent such as N-methyl-2-pyrrolidone (NMP) under high temperature and high pressure. If necessary, a copolymer component such as trihalobenzene may be included. As a polymerization degree adjusting agent, caustic potash or alkali metal carboxylate is added, and a polymerization reaction is performed at a temperature of 230 to 280 ° C. After the polymerization, the polymer is cooled, and the polymer is filtered as a water slurry through a filter to obtain a granular polymer. This is stirred in an aqueous solution such as acetate at a temperature of 30 to 100 ° C. for 10 to 60 minutes, washed several times with ion exchange water at a temperature of 30 to 80 ° C. and dried to obtain a PPS granular polymer. The obtained granular polymer was washed with NMP at an oxygen partial pressure of 10 torr or less, preferably 5 torr or less, and then washed several times with ion-exchanged water at a temperature of 30 to 80 ° C. to form a by-product salt, a polymerization aid, and Separate unreacted monomers. If necessary, an inorganic or organic additive or the like is added to the above-obtained polymer to the extent that the object of the present invention is not hindered to obtain a PPS resin.

  As a manufacturing method of m-PPS resin, there exists the following method, for example. Sodium sulfide and p-dichlorobenzene, m-dichlorobenzene, and other monomers as necessary are blended, and in the presence of a polymerization aid in an amide polar solvent such as N-methyl-2-pyrrolidone (NMP). The reaction is carried out under high temperature and pressure. As monomers other than p-dichlorobenzene and m-dichlorobenzene,

(Here, X represents an alkylene, CO, or SO ₂ unit.)

(Here, R represents an alkyl, nitro, phenylene, or alkoxy group.), And a plurality of these monomers may be used.

  Next, the manufacturing method of the heat laminated laminated film of this invention is demonstrated. When the above PPS resin alone or m-PPS resin is used, the PPS resin and m-PPS resin are supplied to separate melt-extrusion apparatuses and heated to the melting point or more of each raw material. Each raw material melted by heating is laminated in a single layer, two layers, or three layers in a molten state by a merging device provided between the melt extrusion device and the die outlet, and is extruded from the slit-like die outlet. Such a molten laminate is cooled on the cooling drum to below the glass transition point of PPS to obtain a substantially amorphous single-layer, or two-layer or three-layer laminate sheet. The lamination structure is not particularly limited, but in the case of a two-layer lamination, a two-layer lamination of a PPS layer / m-PPS layer is preferable, and in the case of a three-layer lamination, a three-layer lamination of m-PPS layer / PPS layer / m-PPS layer Is preferred. A well-known apparatus can be used as the melt-extrusion apparatus, but a monoaxial or biaxial extruder is simple and preferably used.

  Subsequently, the amorphous single layer, or the two-layer or three-layer laminated sheet thus obtained is subjected to a conventionally known sequential biaxial stretching machine in the range of the glass transition temperature of the PPS to the cold crystallization temperature or less. After biaxial stretching with a simultaneous biaxial stretching machine, a single-stage or multi-stage heat treatment is performed at a temperature in the range of 160 to 280 ° C. to obtain a biaxially oriented film. Stretching methods include sequential biaxial stretching methods (stretching methods that combine stretching in each direction, such as a method of stretching in the width direction after stretching in the longitudinal direction), and simultaneous biaxial stretching methods (in the longitudinal direction and the width direction). The method of extending | stretching simultaneously), or the method which combined them can be used. Here, a sequential biaxial stretching method in which stretching in the longitudinal direction and then in the width direction is performed first is used. First, an unstretched polyphenylene sulfide film is heated with a heating roll group, and is 3 to 4 times, preferably 3.0 to 3.8 times, more preferably 3.0 to 3.7 times in the longitudinal direction (MD direction). The film is stretched in one or two or more stages (MD stretching). The stretching temperature ranges from Tg (glass transition temperature of PPS) to (Tg + 40) ° C., preferably (Tg + 5) to (Tg + 30) ° C. Thereafter, it is cooled by a cooling roll group of 20 to 50 ° C. Here, Tg represents the glass transition temperature of polyphenylene sulfide, but when a biaxially oriented copolymer polyarylene sulfide layer is laminated, it is stretched in the above range according to the biaxially oriented polyarylene sulfide having a high Tg. Is preferred.

  As a stretching method in the width direction (TD direction) following MD stretching, for example, a method using a tenter is common. The both ends of this film are gripped with clips, guided to a tenter, and stretched in the width direction (TD stretching). The stretching temperature is preferably Tg to (Tg + 40) ° C., more preferably (Tg + 5) to (Tg + 30) ° C. The draw ratio is in the range of 3 to 4 times, preferably 3.0 to 3.6 times, more preferably 3.0 to 3.5 times from the viewpoint of improving the breaking elongation, and the area ratio (MD direction ratio). 14 times or less, more preferably 13.5 times or less, and even more preferably 13 times or less. When the area magnification exceeds 14 times, the thermal shrinkage rate of the film increases, and air biting is formed at the interface of the laminated film during lamination, which may deteriorate the carbon dioxide gas resistance. When it is less than 13 times, the flatness of the film is deteriorated, and the laminate property may be deteriorated.

  Next, this stretched film is heat-set under tension. The preferable heat setting temperature in the case of one-stage heat setting is 240 to 280 ° C., and the total time of the heat setting step and the relaxation treatment step is 1 to 60 seconds, preferably 5 to 30 seconds. A more preferable heat treatment is multistage heat setting. In this case, the heat setting temperature at the first stage is 160 to 220 ° C., preferably 180 to 220 ° C., and the treatment time is 1 to 30 seconds, preferably 1 to 15 seconds. The maximum temperature of the subsequent two-stage heat setting is 240 to 280 ° C, preferably 260 to 280 ° C. Furthermore, this film is subjected to a relaxation treatment in the width direction at 240 to 280 ° C, more preferably 260 to 280 ° C. The relaxation rate is preferably 0.1 to 8%, more preferably 2 to 5%. The total time of the two-stage heat setting step and the relaxation treatment step at 240 ° C. or higher is preferably 1 to 60 seconds, and more preferably 5 to 30 seconds.

  Further, the film is cooled and wound up to room temperature, if necessary, while being subjected to relaxation treatment in the longitudinal and width directions to obtain a desired biaxially oriented film.

  The biaxially oriented film obtained by the above method is, for example, heat laminated so that the PPS layer / m-PPS layer is a biaxially oriented bilayer laminated film so that the PPS layer is the outermost layer (PPS layer / A heat-laminated laminated film of (m-PPS layer) / (m-PPS layer / PPS layer) is obtained. Further, the biaxially oriented two-layer laminated film and the biaxially oriented PPS single film may be heat laminated as a (PPS layer / m-PPS layer) / PPS layer to form a thermally laminated laminated film. Furthermore, (PPS layer / m-PPS layer) / PPS layer / (m-PPS layer / PPS layer) can also be used. In addition, a biaxially oriented three-layer heat laminated laminated film of m-PPS layer / PPS layer / m-PPS layer was produced, and a biaxially oriented PPS single film and PPS layer / (m-PPS layer / PPS layer / m- A PPS layer) / PPS layer five-layer heat laminated laminate film can also be used. From the viewpoint of stability in film formation and improvement in planarity in lamination, a heat laminate laminate structure of (PPS layer / m-PPS layer) / PPS layer / (m-PPS layer / PPS layer) is preferable. Of course, the heat laminate laminated structure is not limited to these.

  In the present invention, as a method of heat laminating lamination, for example, a method of heat laminating by pressing nip between a heated metal roll and a nip roll is preferable. The metal roll surface temperature of the laminate is preferably 230 to 260 ° C, more preferably 235 to 260 ° C, and further preferably 240 to 260 ° C. When the surface temperature of the metal roll is less than 230 ° C., the interfacial adhesion of the heat-laminated laminate film may not be sufficiently increased, and the carbon dioxide gas refrigerant resistance may be deteriorated, and the breaking elongation of the heat-laminated laminate film is lowered There is. When the surface temperature of a metal roll exceeds 260 degreeC, adhesion with a metal roll generate | occur | produces and the planarity of a film may deteriorate. The surface temperature of the metal roll can be measured with a contact-type thermometer. The nip roll is not particularly limited, but a metal roll, a ceramic roll, a rubber material roll or the like can be used, and a rubber material roll is preferable from the viewpoint of uniform pressure load in the roll width direction, such as fluoro rubber and silicon rubber. However, it is not limited to these. The nip roll is preferably heated from the viewpoint of improving the carbon dioxide gas refrigerant resistance of the present invention, and the nip roll surface temperature is preferably 180 ° C to 240 ° C, more preferably 190 ° C to 240 ° C, More preferably, it is 200 degreeC-240 degreeC. When the nip roll surface temperature is less than 180 ° C., the interfacial adhesion of the heat laminated laminate film may not be sufficiently improved, and the carbon dioxide gas refrigerant resistance may be deteriorated, and the breaking elongation of the heat laminated laminate film may be lowered. . When the surface temperature of the nip roll exceeds 240 ° C., it may be difficult to use due to the heat resistance of the rubber adhesive used on the nip roll surface. The laminating speed is preferably 0.5 to 3 m / min, more preferably 0.5 to 2 m / min, and still more preferably 0.5 to 1 m / min. It is preferable from the viewpoint of improvement.

  In thermal lamination, from the viewpoint of improving carbon dioxide gas refrigerant resistance, a biaxially oriented bilayer laminated film of PPS layer / m-PPS layer is manufactured in advance, and the PPS layer side of the thermal laminated laminated film is placed on the metal roll side And laminating are preferably used from the viewpoint of the effects of the present invention.

  The thickness of the biaxially oriented two-layer laminated polyarylene sulfide film is preferably 100 μm or less (for example, PPS layer / m-PPS layer = 85 μm / 15 μm) or less, and 75 μm (not particularly limited, for example, PPS layer / m -PPS layer = 60 μm / 15 μm) or less is more preferable. The method for laminating the heat-laminated laminated polyarylene sulfide film of the present invention is not particularly limited, but the PPS layer side of the biaxially oriented bilayer laminated film of the PPS layer / m-PPS layer is disposed on the metal roll side, and the nip roll side is disposed. A biaxially oriented PPS film single film can be arranged to obtain a three-layer thermally laminated laminated film of (PPS layer / m-PPS layer) / PPS layer. After producing the three-layer heat laminate laminate film, the PPS layer side of the biaxially oriented two-layer laminate film of PPS layer / m-PPS layer is arranged on the metal roll side, and the PPS layer side of the three-layer heat laminate laminate film Can be arranged on the nip roll side to obtain a five-layer heat laminated laminate film of (PPS layer / m-PPS layer) / (PPS layer / m-PPS layer / PPS layer). In the present invention, it is possible to use a one-pass laminate in which a five-layer heat laminate laminate film of (PPS layer / m-PPS layer) / PPS layer / (m-PPS layer / PPS layer) is laminated at a time. However, the interfacial adhesion cannot be sufficiently increased, and the carbon dioxide gas refrigerant resistance of the present invention may deteriorate. In the present invention, when producing a heat laminate laminate film of 5 layers or more, after producing a 3 layer heat laminate laminate film, a biaxially oriented two layer laminate film of PPS layer / m-PPS layer is disposed on the metal roll side. And it is preferably used from the viewpoint of the carbon dioxide gas refrigerant resistance effect of the present invention to carry out the multi-stage lamination in which the previously produced thermal laminate laminated film is arranged on the nip roll side. As an angle made to hold in the metal roll of the heat laminated laminated film of this invention, 10-180 degree | times is preferable, More preferably, it is 30-150 degree | times, More preferably, it is 60-120 degree | times. By holding the film on a metal roll before lamination, wrinkles due to heat shrinkage of the film can be eliminated before lamination, and the interfacial adhesion and flatness of the heat-laminated laminated film can be improved. In addition, it is preferable to preheat and laminate the nip roll side in advance from the viewpoint of improving the adhesiveness of the interface, and the angle to be held by the nip roll is preferably 50 to 180 degrees, more preferably 60 to 180 degrees. More preferably, it is 90 to 180 degrees. In the present invention, from the standpoint of improving the carbon dioxide gas refrigerant resistance, preheating and laminating are preferred, and the metal roll surface temperature is 230 ° C or higher, preferably 235 ° C or higher, more preferably 240 ° C or higher. It is preferable to laminate after preheating for 1.5 seconds or more, more preferably 2 seconds or more, and even more preferably 3 seconds or more. The upper limit of the preheating time on the metal roll is not particularly limited, but if the preheating time is too long, the crystallization of the film may progress or the physical properties of the film may deteriorate due to the progress of orientation relaxation. Due to the precipitation of oligomers from the film surface, the drum surface may become dirty and the quality of the heat-laminated laminated film surface may deteriorate. From the above viewpoint, the preheating time is preferably 10 seconds or less.

  In the present invention, it is preferably used from the viewpoint of the flatness, interfacial adhesion, and elongation at break of the laminate film after being thermally fused with a metal roll and a nip roll and then immediately cooled to below the glass transition point of PPS. Although the cooling direction is not particularly limited, roll cooling, air cooling, or the like can be used.

  From the viewpoint of improving the interfacial adhesion, the biaxially oriented m-PPS film and the biaxially oriented PPS film are also included in a preferred embodiment of the present invention by subjecting the adhesive layer side to corona discharge treatment or plasma treatment. As the atmospheric gas during the corona discharge treatment, at least one gas selected from air (EC treatment), oxygen (OE treatment), nitrogen (NE treatment), carbon dioxide gas (CE treatment), and the like can be given. Among these, it is preferable to use EC treatment from the viewpoint of economy, and it is preferable to perform surface treatment by NE treatment or CE treatment from the viewpoint of improving adhesiveness. In the present invention, surface treatment is performed by NE treatment. Is more preferable from the viewpoint of improving adhesiveness.

  Moreover, in this invention, unless the effect of this invention is prevented, another sheet layer, a nonwoven fabric, etc. can be laminated | stacked as needed.

  Moreover, in this invention, in order to improve the handleability and workability of a heat laminated laminated film, an inert particle can be added to each layer. Examples of the inert particles used herein include inorganic fillers such as silica, alumina, calcium carbonate, barium carbonate, barium titanate, barium sulfate, calcium silicate, magnesium oxide, titanium oxide and zinc oxide, and do not melt at 300 ° C. Examples thereof include particles of an organic polymer compound (for example, crosslinked polystyrene).

[Measurement method of characteristics]
(1) Melting temperature of resin and film Using a differential scanning calorimeter DSC (RDC220) manufactured by Seiko Instruments Inc. according to JIS K7121-1987 and a disk station (SSC / 5200) manufactured by the same company as a data analyzer, 5 mg of a sample was made of aluminum. The temperature was raised from room temperature to 340 ° C. at a heating rate of 20 ° C./min on a tray, melted and held at 340 ° C. for 5 minutes, rapidly solidified and held for 5 minutes, and then from room temperature at a heating rate of 20 ° C./min. The temperature rose. At that time, the peak temperature of the endothermic peak of melting observed was defined as the melting temperature (Tm).

(2) Melt Viscosity Using a flow tester CFT-500 (manufactured by Shimadzu Corporation), the base length was 10 mm, the base diameter was 1.0 mm, the preheating time was set to 5 minutes, and the measurement was performed at 310 ° C. The melt viscosity at a shear rate of 1000 / s is a correlation line obtained by measuring the melt viscosities at shear rates of 500 to 1000 / s and 1000 to 2000 / s with n = 2, respectively, and linearly approximating them on a log-log plot. The value at a shear rate of 1000 / s.

(3) Elongation at room temperature In accordance with the following method defined in ASTM-D882, a sample film having a width of 10 mm is measured between chucks using an Instron type tensile tester (AMF / RTA-100 manufactured by Orientec Co., Ltd.). Set to 50 mm, and perform a tensile test at a temperature of 25 ° C. and a tensile speed of 300 mm / min. The elongation at break is determined by measuring and averaging both the film longitudinal direction and the width direction at n = 5. Measuring device: “Tensilon AMF / RTA-100”, an automatic measuring device for film strength and elongation, manufactured by Orientec Co., Ltd.

(4) Motor processability Using a motor slot processing machine (Odawara Engineering Co., Ltd.), the sample was processed into a slot with a width of 24 mm and a length of 39 mm at a processing speed of 2 / sec. Defective products were evaluated according to the following criteria. The number of processed samples is 100 for each sample.

A: Defect rate is 0%
○: The defect rate exceeds 0% and is 5% or less. Δ: The defect rate exceeds 5% and is 20% or less. X: The defect rate exceeds 20%.

(5) Adhesiveness A laminate sample is arbitrarily cut into 10 cm square and n = 30 pieces. A 1 cm cut is made in the center of one side of the cut sample. One side of the cut film is torn in the 45 ° direction (see FIG. 1). The interface peeling width at the tear end face portion was determined according to the following criteria.

◎: 1 mm or less ○: 1 mm to 2 mm or less △: 2 mm to 3 mm or less ×: 3 mm or more
(6) Carbon dioxide gas refrigerant cycle evaluation of heat-laminated laminated film: In the case of bubbles of 5 mm or more 125 laminated layers of 80 cm ² (1 m ² minutes) are put into an autoclave (500 cc made by pressure-resistant glass industry). An autoclave is charged into a thermostatic layer TRLN11L (manufactured by TOMAS), carbon dioxide gas is injected under an atmosphere of −20 ° C. to 4.5 MPa, and then the temperature is raised to 100 ° C. at 20 ° C./min. Further, after confirming that the pressure in the autoclave is 10 MPa or more, the leak valve is opened to release the pressure at once. After performing this as 30 cycles, the sample after the test was visually observed to measure the number of bubbles of 5 mm or more. The number of bubbles of 5 mm or more around 1 m ² was determined according to the following criteria.

◎: 30 or less bubbles of 5 mm or more ○: 50 or less bubbles of 5 mm or more Δ: 100 or less bubbles of 5 mm or more ×: More than 100 bubbles of 5 mm or more (7) Resistance of heat laminated laminated film Carbon dioxide refrigerant cycle evaluation: When bubbles are 1 mm or more and less than 5 mm 125 laminated layers of 80 cm ² (1 m ² minutes) are put into an autoclave (500 cc manufactured by Pressure Glass Industrial Co., Ltd.). An autoclave is put into a thermostatic layer TRLN11L (manufactured by THOMAS), carbon dioxide gas is injected until it reaches 4.5 MPa in an atmosphere at an initial condition of −20 ° C., and then the temperature is increased to 100 ° C. at 20 ° C./min. Further, after confirming that the pressure in the autoclave is 10 MPa or more, the leak valve is opened to release the pressure at once. After performing this as 30 cycles, the number of bubbles of 1 mm or more and less than 5 mm was measured by visual observation of the sample after the test. The number of bubbles of 1 mm or more and less than 5 mm per 1 m ² was determined according to the following criteria.

◎ 1 mm or more and less than 5 mm bubbles 250 or less ○ 1 mm or more and less than 5 mm bubbles 500 or less △: 1 mm or more and less than 5 mm bubbles 1000 × 1 mm or more and less than 5 mm bubbles more than 1000

Example 1
(1) Production of m-PPS resin 100 mol of sodium sulfide nonahydrate, 45 mol of sodium acetate and 25 liters of N-methyl-2-pyrrolidone (hereinafter abbreviated as NMP) were charged into an autoclave. While stirring, the temperature was gradually raised to a temperature of 220 ° C., and the contained water was removed by distillation. In the system after dehydration, 5 liters of 91 mol of p-dichlorobenzene as a main component monomer, 10 mol of m-dichlorobenzene as a secondary component monomer, and 0.2 mol of 1,2,4-trichlorobenzene were added. It was added together with NMP, nitrogen was pressurized and sealed at 3 ° C./cm ² at a temperature of 170 ° C., the temperature was raised, and polymerization was carried out at a temperature of 260 ° C. for 4 hours. After completion of the polymerization, the mixture was cooled, the polymer was precipitated in distilled water, and a small block polymer was collected with a wire mesh having a 150 mesh opening. The small block polymer thus obtained was washed 5 times with distilled water at 90 ° C. and then dried under reduced pressure at a temperature of 120 ° C. so that the melt viscosity was 1000 poise and the melting point was 250 ° C. A copolymerized PPS resin was obtained. Next, 0.3% by weight of calcium carbonate powder having an average particle size of 1.2 μm was added and dispersed and blended uniformly, and extruded at a temperature of 320 ° C. with a 30 mmφ twin screw extruder to obtain m-PPS pellets. It was.

(2) Production of PPS resin The PPS resin was prepared in the same manner as in the production of m-PPS in (1) above except that 101 mol of p-dichlorobenzene was used as the main component monomer and no subcomponent monomer was used. Manufactured. The melt viscosity of the PPS resin was 3000 poise and the melting point was 283 ° C.

(3) Film formation The m-PPS resin and PPS resin obtained in the above (1) and (2) were each dried at a temperature of 180 ° C. for 3 hours under a reduced pressure of 1 mmHg, and then supplied to separate extruders. In a molten state, the double pipe type laminating device at the upper part of the die is led to have two layers, and subsequently discharged from the T-die die, which is rapidly cooled with a cooling drum having a temperature of 25 ° C. A two-layer laminated sheet of m-PPS layer / PPS layer was obtained. Next, the obtained laminated sheet was caused to travel in contact with a plurality of heating rolls having a surface temperature of 95 ° C., and 3.7 ° in the longitudinal direction between the heating rolls and the 30 ° C. cooling rolls having different peripheral speeds. The film was stretched twice. The uniaxially stretched sheet thus obtained was stretched 3.5 times (area stretch ratio: 12.95 times) at a temperature of 100 ° C. in a direction perpendicular to the longitudinal direction using a tenter, and subsequently at a temperature of 200 ° C. Heat treatment was performed for 10 seconds (one-stage heat setting) followed by heat treatment at 260 ° C. for 10 seconds (two-stage heat setting), followed by a 5% relaxation treatment in the transverse direction for 10 seconds in a 260 ° C. relaxation treatment zone. Then, after cooling to room temperature, the film edge was removed to obtain a biaxially oriented two-layer laminated film of m-PPS / PPS (15/60 μm) (hereinafter, such m-PPS / PPS laminated film was formed into a film) Also referred to as A). In addition, a single PPS resin was separately formed and heat-treated under the above film forming conditions to obtain a biaxially oriented PPS single film having a thickness of 100 μm (hereinafter, such a single film of PPS is also referred to as film B).

(4) Lamination The film A obtained by the film forming method is placed so that the surface of the PPS layer is on the metal roll side, and the film B is placed on the nip roll side and laminated. Next, the PPS layer / m-PPS layer / PPS layer three-layer heat laminate laminated film obtained above is arranged on the nip roll side, and the film A is arranged so that the surface of the PPS layer is on the metal roll side. Laminate. The metal roll (HCr (hard chromium) roll φ150) was heated so that the roll surface temperature was 240 ° C., and the nip roll (fluororubber roll φ150) was heated so that the roll surface temperature was 200 ° C. The laminating pressure was 20 kg / cm ² , the laminating speed was 1 m / min, the holding angle on the metal roll side was 60 degrees, and the holding angle on the nip roll side was 90 degrees. . Table 1 shows the evaluation results of the 5-layer heat laminated laminate film having a thickness of 250 μm obtained as described above.

(Example 2)
When obtaining the film A and the film B in Example 1, a five-layer heat laminated laminate film was produced in the same manner as in Example 1 except that the longitudinal direction (MD direction) of the draw ratio was 3.8 times. The evaluation results of the obtained five-layer heat laminated laminate film are shown in Table 1.

(Example 3)
A five-layer heat-laminated laminated film was produced in the same manner as in Example 1, except that the longitudinal direction (MD direction) of the draw ratio in Example 1 was 3.9 times and the width direction (TD direction) was 3.6 times. did. The evaluation results of the obtained five-layer heat laminated laminate film are shown in Table 1.

Example 4
95 parts by weight of the PPS resin prepared in Example 1 and 5 parts by weight of polyetherimide resin (manufactured by GE Plastics) “Ultem 1010” (registered trademark) (PEI) were dried under reduced pressure at 120 ° C. for 3 hours. After adding 0.5 parts by weight of γ-isocyanatopropyltriethoxysilane (manufactured by Shin-Etsu Chemical Co., Ltd., “KBE9007” (registered trademark)) as a compatibilizing agent to 100 parts by weight of PEI resin, heat to 310 ° C. The kneading paddle kneading section provided with five kneading paddles was put into a bi-directional rotating twin-screw kneading extruder (manufactured by Nippon Steel Co., Ltd., screw diameter 30 mm, screw length / screw diameter = 45.5) and stayed Melted and extruded at a screw speed of 300 rpm for 90 seconds, discharged into a strand, cooled with water at a temperature of 25 ° C, and immediately cut Was obtained PPS / PEI resin composition of PPS resin / PEI (95/5 wt%) was.

  Next, the PPS / PEI resin composition was used in place of the PPS resin in Example 1 (except that the longitudinal direction (MD direction) of the draw ratio was set to 3.0 times). A film A ′ replacing the film A and a film B ′ replacing the film B were prepared, and a five-layer heat laminated laminated film was produced in the same manner as in Example 1. The evaluation results of the obtained five-layer heat laminated laminated film were as follows. Table 1 shows.

(Example 5)
A five-layer heat-laminated laminated film was produced in the same manner as in Example 4 except that the longitudinal direction (MD direction) of the draw ratio was 3.5 when obtaining the films A ′ and B ′. The evaluation results of the obtained five-layer heat laminated laminate film are shown in Table 1.

(Example 6)
In Example 1, the film B is arranged so as to be on the metal roll side, and the film A is arranged so that the surface of the PPS layer is on the nip roll side, and the three-layer heat of PPS layer / m-PPS layer / PPS layer A five-layer heat laminate laminate film was produced in the same manner as in Example 1 except that a laminate laminate film was obtained. The evaluation results of the obtained five-layer heat laminated laminate film are shown in Table 1.

(Example 7)
A five-layer heat laminate laminate film was produced in the same manner as in Example 1 except that the surface temperature of the metal roll was heated to 235 ° C. in Example 1. The evaluation results of the obtained five-layer heat laminated laminate film are shown in Table 1.

(Example 8)
A five-layer heat laminated laminate film was produced in the same manner as in Example 1 except that the surface temperature of the metal roll was heated to 230 ° C. in Example 1. The evaluation results of the obtained five-layer heat laminated laminate film are shown in Table 1.

Example 9
A five-layer heat laminate laminate film was produced in the same manner as in Example 1 except that the surface temperature of the nip roll was heated to 190 ° C. in Example 1. The evaluation results of the obtained five-layer heat laminated laminate film are shown in Table 1.

(Example 10)
A five-layer heat laminated laminate film was produced in the same manner as in Example 1 except that the lamination speed was 2 m / min in Example 1. The evaluation results of the obtained five-layer heat laminated laminate film are shown in Table 1.

(Example 11)
A five-layer thermally laminated laminated film was produced in the same manner as in Example 1 except that the laminating speed was 3 m / min in Example 1. The evaluation results of the obtained five-layer heat laminated laminate film are shown in Table 1.

Example 12
A biaxially oriented PPS single film was produced in the same manner as in Example 1 except that the thickness of the biaxially oriented PPS single film produced in Example 1 was 75 μm. The biaxially oriented PPS single film obtained was placed so as to be on the metal roll side, and the PPS layer of the biaxially oriented bilayer laminate film of PPS layer / m-PPS layer obtained in the same manner as in Example 1 was a nip roll. A three-layer heat laminated laminate film of PPS layer / m-PPS layer / PPS layer was prepared by being arranged so as to be on the side. The lamination conditions were the same as in Example 1. Table 1 shows the evaluation results of the obtained three-layer heat laminated laminate film.

(Comparative Example 1)
A five-layer heat-laminated laminated film was produced in the same manner as in Example 1, except that the longitudinal direction (MD direction) of the draw ratio in Example 1 was 4.2 times and the width direction (TD direction) was 3.6 times. did. The evaluation results of the obtained five-layer heat laminated laminate film are shown in Table 1.

(Comparative Example 2)
A five-layer heat-laminated laminated film was produced in the same manner as in Example 1 except that the one-stage heat fixing temperature was set to 260 ° C. in Example 1. The evaluation results of the obtained five-layer heat laminated laminate film are shown in Table 1.

(Comparative Example 3)
A five-layer heat-laminated laminated film was produced in the same manner as in Example 4 except that the one-step heat fixing temperature was set to 260 ° C. in Example 4. The evaluation results of the obtained five-layer heat laminated laminate film are shown in Table 1.

(Comparative Example 4)
A five-layer heat laminated laminate film was produced in the same manner as in Example 1 except that the surface temperature of the nip roll was set to 100 ° C. in Example 1. The evaluation results of the obtained five-layer heat laminated laminate film are shown in Table 1.

(Comparative Example 5)
A five-layer heat laminated laminate film was produced in the same manner as in Example 1 except that the surface temperature of the metal roll was heated to 200 ° C. and the surface temperature of the nip roll was 150 ° C. in Example 1. The evaluation results of the obtained five-layer heat laminated laminate film are shown in Table 1.

(Comparative Example 6)
In Example 1, the biaxially oriented PPS single film was placed so as to be on the metal roll side, and the PPS layer / m-PPS layer biaxially oriented bilayer laminated film was placed so that the PPS layer side was on the nip roll side. Laminate. Next, the obtained PPS layer / m-PPS layer / PPS layer three-layer heat laminate laminate film is disposed on the metal roll side, and the PPS layer / m-PPS layer biaxially oriented two-layer laminate film is a nip roll. A five-layer heat-laminated laminated film was produced in the same manner as in Example 1 except that the laminate was placed on the side and laminated. The evaluation results of the obtained five-layer heat laminated laminate film are shown in Table 1.

(Comparative Example 7)
In Example 1, the PPS layer / m-PPS layer biaxially oriented bilayer laminated film was placed so that the PPS layer side was on the metal roll side, and the biaxially oriented PPS single film was placed on the nip roll side. Laminate. Then, the obtained PPS layer / m-PPS layer / PPS layer three-layer heat laminate laminate film is disposed on the metal roll side, and PPS layer / m-PPS layer biaxially oriented two-layer laminate film PPS A five-layer thermally laminated laminated film was produced in the same manner as in Example 1 except that the lamination was performed so that the layer side was the nip roll side. The evaluation results of the obtained five-layer heat laminated laminate film are shown in Table 1.

(Comparative Example 8)
A five-layer thermally laminated laminated film was produced in the same manner as in Example 1 except that the laminating speed was 5 m / min in Example 1. The evaluation results of the obtained five-layer heat laminated laminate film are shown in Table 1.

(Comparative Example 9)
In the biaxially oriented two-layer laminated film and the biaxially oriented PPS single film obtained in Example 1, the PPS layer side of the biaxially oriented two-layer laminated film of m-PPS layer / PPS layer is the outside on the metal roll side. The holding angle to the metal roll is 90 degrees. It arrange | positions so that the PPS layer side of the biaxially oriented bilayer laminated film of m-PPS layer / PPS layer may become an outer side on the nip roll side, and the holding angle to a nip roll shall be 60 degree | times. The biaxially oriented PPS single film is arranged so that the holding angle is 0 between the metal roll and the nip roll, and is (PPS layer / m-PPS layer) / PPS layer / (m-PPS layer / PPS layer) at a time. A five-layer heat laminate laminate film was produced in the same manner as in Example 1 except that a five-layer heat laminate laminate film was used. The evaluation results of the obtained five-layer heat laminated laminate film are shown in Table 1.

(Comparative Example 10)
In the biaxially oriented two-layer laminated film and biaxially oriented PPS single film obtained in Example 4, the PPS layer side of the biaxially oriented two-layer laminated film of m-PPS layer / PPS layer is the outside on the metal roll side. The holding angle to the metal roll is 90 degrees. It arrange | positions so that the PPS layer side of the biaxially oriented bilayer laminated film of m-PPS layer / PPS layer may become an outer side on the nip roll side, and the holding angle to a nip roll shall be 60 degree | times. The biaxially oriented PPS single film is arranged so that the holding angle is 0 between the metal roll and the nip roll, and is (PPS layer / m-PPS layer) / PPS layer / (m-PPS layer / PPS layer) at a time. A five-layer heat laminate laminate film was produced in the same manner as in Example 4 except that a five-layer heat laminate laminate film was used. The evaluation results of the obtained five-layer heat laminated laminate film are shown in Table 1.

(Comparative Example 11)
Three-layer laminated film in the same manner as in Example 12, except that the biaxially oriented two-layer laminated film is 125 μm (m-PPS / PPS = 15 μm / 110 μm) and the biaxially oriented PPS single film is 125 μm in Example 12. Was made. The evaluation results of the obtained five-layer heat laminated laminate film are shown in Table 1.

  The heat-laminated laminated film of the present invention is a heat-laminated laminated film excellent in moldability and carbon dioxide gas refrigerant resistance, and is used for a drive motor or an air conditioner compressor motor used in a hybrid vehicle currently being developed by an automobile manufacturer. Or it is suitable for various motor insulation molding materials, such as a water heater motor.

It is a figure of the adhesiveness confirmation method used by this invention.

Claims (6)

A biaxially oriented film made of polyarylene sulfide or a biaxially oriented film having a layer made of polyarylene sulfide in the outermost layer and a biaxially oriented film made of copolymerized polyarylene sulfide or a layer made of copolymerized polyarylene sulfide as the outermost layer A heat-laminated laminated film in which a surface composed of the polyarylene sulfide and a surface composed of the copolymerized polyarylene sulfide of the biaxially oriented film having the laminate are laminated without an adhesive layer, The laminated film has a room-temperature breaking elongation of 80% or more and 160% or less, and heat of 100 or less bubbles having a maximum diameter of 5 mm or more around 1 m ² of the heat-laminated laminated film after the carbon dioxide gas refrigerant cycle test. Laminated laminated film. The heat-laminated laminated film according to claim 1, wherein the polyarylene sulfide is poly-p-phenylene sulfide. The heat-laminated laminated film according to claim 1 or 2, wherein the copolymerized polyarylene sulfide is a copolymerized polyphenylene sulfide. Thermal laminate laminated film in any of耐炭acid claims 1-3 heat laminated multilayer film 1 m ² around a maximum diameter of less than 5mm than 1mm bubbles after the gas refrigerant cycle test is 1,000 or less. Polyarylene sulfide and copolymer polyarylene sulfide are coextruded so as to constitute the outermost layer, respectively, and a biaxially oriented two-layer laminated polyarylene sulfide film and a separately prepared polyarylene sulfide film are roll surface temperature. A method for producing a heat-laminated laminated film, comprising: thermocompression bonding after contact with a metal roll heated to 230 ° C. or more for 1.5 seconds or more. The method for producing a heat-laminated laminated film according to claim 5, wherein the biaxially oriented two-layer laminated polyarylene sulfide film according to claim 5 has a thickness of 100 µm or less.

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