JP2006199734A - Polyarylene sulfide film - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To obtain a polyarylene sulfide film having a few film cracks in motor processing of slot, wedge, etc. <P>SOLUTION: The polyarylene sulfide film has ≥125 μm and ≤450 μm thickness and ≥100% and ≤200% breaking elongation at least in one direction. <P>COPYRIGHT: (C)2006,JPO&NCIPI

Description

  The present invention relates to a polyarylene sulfide film, and more particularly to a polyarylene sulfide film that causes less film cracking in motor processing when used in motor electrical insulating materials such as slots or wedges.

  In recent years, electric insulating materials for motors have been required to have heat resistance and hydrolysis resistance at high temperatures. For example, as an electrical insulation material for motors used in refrigerators and air conditioners, a new alternative refrigerant related to the complete abolition of specific chlorofluorocarbons has been proposed due to environmental problems. In addition to heat resistance, hydrolysis resistance is required. Moreover, in addition to heat resistance, the electric insulation material of the motor used in the hybrid vehicle is required to have hydrolysis resistance because moisture enters under the usage environment.

  Various polymer films have been proposed to meet these requirements. Among them, biaxial orientation has excellent heat resistance, hydrolysis resistance, chemical resistance, electrical insulation and low hygroscopic properties. A polyphenylene sulfide (hereinafter sometimes referred to as PPS) film is attracting attention.

In recent years, taking advantage of its high electrical insulation and low hygroscopicity, the application of polyphenylene sulfide films to electrical insulation materials has been promoted. For example, (1) using biaxially oriented PPS films as electrical insulation materials Is known (see Patent Document 1). However, since the obtained biaxially oriented PPS film was as thin as 25 μm and the elongation at break was low, the processability of the motor slot was not excellent. Moreover, the film which reduced the volatile component of the biaxially oriented PPS film is proposed (refer patent document 2). However, the obtained biaxially oriented PPS film had a low elongation at break and was not excellent in workability. 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 Documents 3 and 4). This is because the tear strength of the laminated film is increased by laminating non-oriented PPS on the base layer part, but the breaking elongation of the biaxially oriented PPS film of the surface layer is low, and the interlayer adhesive strength is low. Since it was not sufficient, the biaxially oriented PPS film in the surface layer was torn in the bending process in slot processing, and the slot cuff part was cracked.
Japanese Patent Laid-Open No. 6-1863 JP 2003-48982 A JP-A-2-45144 JP-A-3-227624

  An object of the present invention is to solve the above-mentioned problems of the prior art and provide a polyarylene sulfide film having a thickness suitable for motor insulating materials such as slots and wedges, and more specifically, in the film width direction. The purpose of the present invention is to suppress the occurrence of film cracking in motor processing by using a polyarylene sulfide film with improved breaking elongation.

  The present invention has the following configuration in order to solve the above problems. That is, it is characterized by a polyarylene sulfide film having a thickness of 125 μm or more and 450 μm or less and a breaking elongation in at least one direction of 100% or more and 200% or less.

  ADVANTAGE OF THE INVENTION According to this invention, the polyarylene sulfide film suitable for a motor insulation film can be obtained, and the polyarylene sulfide film without the crack of a film in motor processings, such as a slot and a wedge, can be provided.

  Hereinafter, the present invention will be described in detail with reference to preferred embodiments.

  The polyarylene sulfide of the present invention is preferably a homopolymer or a copolymer having a repeating unit of-(Ar-S)-. As Ar, units represented by the following formulas (A) to (K) and the like can be used.

(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.)
As the repeating unit of polyarylene sulfide used in the present invention, the structural formula represented by the above formula (A) is preferable, and representative examples thereof include polyphenylene sulfide, polyphenylene sulfide sulfone, polyphenylene sulfide ketone, and random thereof. Examples thereof include copolymers, block copolymers, and mixtures thereof. Particularly preferred polyarylene sulfide is preferably polyphenylene sulfide (PPS) from the viewpoint of film physical properties and economy, and the p-phenylene sulfide unit represented by the following structural formula is preferably 80 mol% as the main structural unit of the polymer. More preferably, it is a resin containing 90 mol% or more. When the p-phenylene sulfide component is less than 80 mol%, 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.

  The repeating unit may contain a unit containing a copolymerizable sulfide bond as long as it is preferably less than 20 mol%. 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 melt viscosity of the polyarylene sulfide resin of the present invention is preferably in the range of 700 to 20,000 poise at a temperature of 300 ° C. and a shear rate of 200 sec ^{−1 from} the viewpoint of sheet formability.

  The polyarylene sulfide film in the present invention is preferably a film formed by melt-molding polyarylene sulfide. The polyarylene sulfide is preferably a film formed by melt-molding a resin composition containing 90% by weight or more of p-phenylene sulfide. When the content of p-phenylene sulfide is less than 90% by weight, the crystallinity of the composition is lowered, and the heat resistance, thermal dimensional stability, hydrolysis resistance, etc. of the film may be impaired. Less than 10% by weight in the composition may contain additives such as polymers other than p-phenylene sulfide, inorganic or organic fillers, lubricants, colorants, ultraviolet absorbers, and compatibilizers.

  In the case of the present invention, the polyarylene sulfide film is preferably biaxially oriented (biaxially stretched) in order to satisfy the breaking elongation of the film and the heat resistance required for the motor slot or wedge. Heat treatment is preferably performed after biaxial orientation.

  If the elongation at break of the present invention is satisfied, a film other than the above-mentioned biaxially oriented polyarylene sulfide film may be laminated. In the present invention, the biaxially oriented polyarylene sulfide film is a single film. It is preferable.

  It is important for the polyarylene sulfide film of the present invention that the elongation at break in at least one direction is 100% or more and 200% or less. More preferably, they are 120% or more and 180% or less, More preferably, they are 140% or more and 160% or less. When the elongation at break in at least one direction is less than 100%, film cracking may occur in the process of bending the slot. When the elongation at break exceeds 200%, the film strength decreases, and the slot and wedge A buckling defect may occur in the processing step.

  In the case of the present invention, it is preferable that the film direction stretched by bending the slot cuff coincides with the film direction having the above-mentioned breaking elongation.

  The breaking strength of the polyarylene sulfide film of the present invention is preferably 100 MPa or more and 300 MPa or less, more preferably 100 MPa or more and 250 MPa or less, and still more preferably 100 MPa or more and 200 MPa or less. If the breaking strength is less than 100 MPa, the strength of the film may not be sufficient, and if it exceeds 300 MPa, film cracking may occur in the slot bending process.

  The thickness of the polyarylene sulfide film of the present invention is preferably 125 μm or more and 450 μm or less. More preferably, they are 200 micrometers or more and 350 micrometers or less, More preferably, they are 250 micrometers or more and 300 micrometers or less. When the film thickness is less than 125 μm, the electrical insulation of the film may be deteriorated. On the other hand, if it exceeds 450 μm, the workability of the slots and wedges may be lowered, and the film forming property may be lowered. When the film has the above thickness, it can be suitably used as an electric insulating film for motor slots.

  In order to obtain the elongation at break of the present invention, the micro endothermic peak (Tmeta) just below the melting point in the DSC measurement of the polyarylene sulfide film of the present invention is preferably from 200 ° C. to 260 ° C., more preferably 225 The temperature is not lower than 250 ° C and more preferably not lower than 235 ° C and not higher than 245 ° C. When the minute endothermic peak (Tmeta) just below the melting point is less than 200 ° C., the heat resistance may be insufficient, and when the minute endothermic peak (Tmeta) just below the melting point exceeds 260 ° C., the elongation at break of the present invention The range may not be satisfied.

  The polyarylene sulfide film of the present invention preferably has a melt crystallization temperature (Tmc) of 140 ° C. or higher and 220 ° C. or lower in DSC measurement in order to form a polyarylene sulfide film satisfying the thickness of the present invention. . More preferably, it is 150 degreeC or more and 200 degrees C or less, More preferably, it is 160 degreeC or more and 180 degrees C or less. When the melt crystallization temperature (Tmc) is less than 140 ° C., the crystallinity of the polymer may be lowered, and the heat resistance of the film may be insufficient. When the melt crystallization temperature (Tmc) exceeds 220 ° C., the melt polymer When the film is formed, the polymer may be easily crystallized and may be easily broken in the stretching process.

In order to obtain polyarylene sulfide having the above-mentioned melt crystallization temperature, for example, in the case of polyphenylene sulfide, it can be controlled by modifying the terminal group of the polymer with aminocarboxylic acid metal salt. For example, the melt crystallization temperature can be adjusted to about 170 ° C. by modifying the end groups with COOCa _1/2 so that the Ca concentration is 400 to 600 ppm. Moreover, melt crystallization temperature can be adjusted to about 240 degreeC by making a terminal group into carboxylic acid terminal.

  In the case of the present invention, as described above, it is easy to obtain a polyarylene sulfide film having the thickness of the present invention by reducing the melt crystallization temperature of the polymer and decreasing the crystallization speed of the polymer. Furthermore, in melt extrusion film formation, when the polymer is rapidly cooled on the casting drum, a method of cooling the film surface from the non-drum surface (surface opposite to the surface of the film facing the drum (the surface of the drum)) is preferably used. It is done. As a method for cooling the film surface from the non-drum surface side, an air chamber method, an air knife method, a press roll method, or the like can be used, but the air chamber method is preferably used in the present invention.

  The impact strength of the polyarylene sulfide film of the present invention is preferably 3 N / μm or more and 10 N / μm or less in order to suppress the occurrence of film cracking in the slot and wedge processing steps, more preferably 4 N / μm. It is 10 N / μm or less, more preferably 5 N / μm or more and 10 N / μm or less. If the impact strength is less than 3 N / μm, the slot and wedge may be cracked in the process of processing the slot. If the impact strength exceeds 10 N / μm, the strength of the polyarylene sulfide film may be reduced. In some cases, buckling defects may occur in the process of processing slots and wedges.

  The method for producing the polyarylene sulfide film of the present invention will be described with reference to the case where polyphenylene sulfide is used as the polyarylene sulfide resin, but the present invention is not limited thereto.

  Examples of the polymerization method of 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) at high temperature and high pressure. If necessary, a copolymer component such as trihalobenzene may be included. 400-600 ppm of caustic potash, carboxylic acid alkali metal salt, or the like is added as a polymerization degree adjusting agent, and a polymerization reaction is performed at 230-280 ° 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 30 to 100 ° C. for 10 to 60 minutes, washed several times with ion exchange water at 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 30 to 80 ° C. to produce a by-product salt, a polymerization aid, and no reaction. Separate monomers and the like. If necessary, an inorganic or organic additive or the like is added to the polymer obtained above to the extent that the object of the present invention is not hindered, and a PPS resin having a Tmc of 140 ° C. or higher and 220 ° C. or lower is obtained.

  After the PPS resin obtained above is sufficiently dried, it is supplied to a melt extruder heated to a temperature equal to or higher than the melting point of the resin composition under a nitrogen stream or under reduced pressure so that the intrinsic viscosity does not decrease, and extruded from the die. The surface temperature of the drum or the like is tightly cooled and solidified on a casting drum having a glass transition point lower than the glass transition point of the resin composition by an electrostatic application method, an air chamber method, an air knife method, a press roll method, etc., which are non-oriented polyphenylene Create a sulfide sheet. In the present invention, it is preferable to use an electrostatic application method and an air chamber method in combination because the molten polymer can be rapidly cooled on the casting drum. The internal pressure of the air chamber is preferably 5 to 500 Pa, more preferably 50 to 400 Pa, and still more preferably 100 to 300 Pa. Moreover, it is preferable that the casting drum surface temperature is the range of 10 to 40 degreeC, More preferably, it is the range of 10 to 30 degreeC, More preferably, it is the range of 10 to 20 degreeC. Further, it is preferable to use various filters, for example, a filter made of a material such as sintered metal, porous ceramic, sand, and wire mesh, in order to remove foreign substances and altered polymer in the melt extruder.

  Next, the obtained non-oriented sheet is biaxially stretched and heat-treated by various methods. Stretching is preferably performed in the range of 90 to 120 ° C. and 3.0 to 3.8 times in the longitudinal direction. In the case of this invention, a more preferable draw ratio is 3.0 to 3.7 times, More preferably, it is 3.0 to 3.5 times. In the present invention, when the draw ratio is less than 3.0 times, a polyphenylene sulfide film having sufficient film planarity may not be obtained, and when the draw ratio exceeds 3.8 times, the breaking elongation of the present invention You may not get. Then, it is preferably stretched 2.5 to 3.5 times at 90 to 120 ° C. in the width direction. More preferably, it is 2.7 to 3.3 times, and still more preferably 2.8 to 3.0 times. In the present invention, when the draw ratio is less than 2.5 times, a polyphenylene sulfide film having sufficient film planarity may not be obtained, and when the draw ratio exceeds 3.5 times, the breaking elongation of the invention You may not get.

  The heat treatment is preferably performed in the range of 180 ° C. to (melting point of PPS—15 ° C.) for 1 to 60 seconds under a constant length or a limited shrinkage of 15% or less. In the case of the present invention, in order to make the elongation at break within the range of the present invention, the heat treatment temperature is more preferably 200 ° C. to (PPS melting point−25 ° C.), and 220 ° C. to (PPS melting point−35 ° C.). preferable.

  In the case of the present invention, the polyphenylene sulfide film having the elongation at break of the present invention can be obtained by performing heat treatment in the above temperature range after stretching in the above range of magnification.

(Methods for measuring physical properties and methods for evaluating effects)
The characteristic value measurement method and effect evaluation method used in the present invention are as follows.

(1) Elongation at break Using an Instron type tensile tester (Orientec Co., Ltd. film tensile strength automatic measuring device “Tensilon AMF / RTA-100”) according to the following method defined in ASTM-D882. Measured. A sample film having a width of 10 mm is pulled under conditions of 100 mm between test lengths and a pulling speed of 200 mm / min. The measurement is performed in an atmosphere of 25 ° C. and 65% RH.

(2) Melt crystallization temperature (Tmc), Tmeta
The melt crystallization temperature and Tmeta were measured under the following conditions using a robot DSC manufactured by Seiko Instruments Inc. The melt crystallization temperature measured an exothermic peak in the 2nd run temperature-decreasing process, and Tmeta measured a minute endothermic peak just below the melting point that appeared in the 1st run temperature-raising process.
1st run Temperature rising process 25 ° C → 350 ° C (20 ° C / min) 5 minutes hold, rapid cooling (removal)
2nd run Temperature rising process 25 ℃ → 350 ℃ (20 ℃ / min) 5 minutes hold
Temperature drop process 350 ℃ → 25 ℃ (20 ℃ / min)
(3) Slot workability Using a motor slot machine (Odawara Engineering Co., Ltd.), a 250 μm thick sample was processed into a slot 24 mm wide and 39 mm long at a processing speed of 2 / sec. The defective product was regarded as a defective product, and the defective product occurrence rate was evaluated according to the following criteria. The number of processed samples is 100 for each sample.

A: Defect rate is 0%
○: Defect rate exceeds 0% and 5% or less △: Defect rate exceeds 5% and 20%
X: The defective rate exceeds 20%. (4) Impact strength Measurement was performed in an atmosphere at 25 ° C. according to the method defined in ASTM-D-256.

(Example 1)
Sodium sulfide and p-dichlorobenzene are reacted in N-methyl-2-pyrrolidone (NMP) solvent at high temperature and pressure. Caustic potash was added as a polymerization regulator, and a polymerization reaction was performed at 280 ° C. After the polymerization, the polymer was cooled, and the polymer was filtered through a filter as a water slurry to obtain a granular polymer. This was stirred for 60 minutes in an 80 ° C. aqueous solution of acetate, washed with ion-exchanged water 5 times at 80 ° C., and dried to obtain PPS powder.

  The powder polymer is washed in NMP at an oxygen partial pressure of 1 Torr or less, then washed 5 times with ion exchange water at 80 ° C., and dried under a reduced pressure of 1 Torr or less. The polymer thus obtained was a substantially washed PPS polymer and the melt crystallization temperature Tmc was 170 ° C.

  The obtained PPS polymer was dried at 180 ° C. for 3 hours under reduced pressure of 1 mmHg, and after adding 0.1 wt% of silica fine particle powder having an average particle diameter of 0.7 μm and 0.05 wt% of calcium stearate, it was added to the extruder. Feed raw materials and melt at 310 ° C. Subsequently, the molten sheet was extruded from a crow mouth type die having a lip width of 1,200 mm and a lip gap of 2.7 mm by filtering with a 95% cut hole diameter 10 μm filter using metal fibers. A casting drum (diameter 1,500 mm) in which an electrostatic charge is applied to the molten film thus obtained and the surface temperature is maintained at 15 ° C., and an air chamber having an internal pressure of 300 Pa is installed on the non-drum surface side. And solidified by cooling.

  The cast film thus obtained was an amorphous and non-oriented film. The film is supplied to a longitudinal stretching machine consisting of a heated roll group, stretched 3.5 times at a film temperature of 102 ° C., then stretched 3.0 times at 103 ° C. in the width direction using a tenter, and further 245 A 250 μm biaxially oriented polyphenylene sulfide film was obtained by heat treatment at 10 ° C. for 10 seconds.

  The measurement and evaluation results on the configuration and properties of the obtained biaxially oriented polyphenylene sulfide film are as shown in Table 1. This film was free from film cracking in slot processing.

(Example 2)
A biaxially oriented polyphenylene sulfide film was prepared in the same manner as in Example 1 except that the stretching ratio of the biaxially oriented polyphenylene sulfide film used in Example 1 was changed to 3.5 × 3.3 times (longitudinal direction × width direction). Created.

  The measurement and evaluation results on the configuration and properties of the obtained biaxially oriented polyphenylene sulfide film are as shown in Table 1. This film was free from film cracking in slot processing.

(Example 3)
A biaxially oriented polyphenylene sulfide film was prepared in the same manner as in Example 1 except that the stretching ratio of the biaxially oriented polyphenylene sulfide film used in Example 1 was changed to 3.5 × 3.5 times (longitudinal direction × width direction). Created.

  The measurement and evaluation results on the configuration and properties of the obtained biaxially oriented polyphenylene sulfide film are as shown in Table 1. This film was free from film cracking in slot processing.

(Example 4)
A biaxially oriented polyphenylene sulfide film was prepared in the same manner as in Example 1 except that the stretch ratio of the biaxially oriented polyphenylene sulfide film used in Example 1 was changed to 3.7 × 3.0 times (longitudinal direction × width direction). Created.

  The measurement and evaluation results on the configuration and properties of the obtained biaxially oriented polyphenylene sulfide film are as shown in Table 1. This film was free from film cracking in slot processing.

(Example 5)
A biaxially oriented polyphenylene sulfide film was prepared in the same manner as in Example 1 except that the stretch ratio of the biaxially oriented polyphenylene sulfide film used in Example 1 was changed to 3.8 × 3.0 times (longitudinal direction × width direction). Created.

  The measurement and evaluation results on the configuration and properties of the obtained biaxially oriented polyphenylene sulfide film are as shown in Table 1. This film was free from film cracking in slot processing.

(Example 6)
A biaxially oriented polyphenylene sulfide film was prepared in the same manner as in Example 1 except that the stretch ratio of the biaxially oriented polyphenylene sulfide film used in Example 1 was changed to 3.5 × 3.7 times (longitudinal direction × width direction). Created.

  The measurement and evaluation results on the configuration and properties of the obtained biaxially oriented polyphenylene sulfide film are as shown in Table 1. This film was free from film cracking in slot processing.

(Example 7)
A biaxially oriented polyphenylene sulfide film was prepared in the same manner as in Example 1 except that the heat setting temperature of the biaxially oriented polyphenylene sulfide film used in Example 1 was changed to 255 ° C.

  The measurement and evaluation results on the configuration and properties of the obtained biaxially oriented polyphenylene sulfide film are as shown in Table 1. This film was free from film cracking in slot processing.

(Example 8)
A biaxially oriented polyphenylene sulfide film was prepared in the same manner as in Example 1 except that the heat setting temperature of the biaxially oriented polyphenylene sulfide film used in Example 1 was changed to 265 ° C.

  The measurement and evaluation results on the configuration and properties of the obtained biaxially oriented polyphenylene sulfide film are as shown in Table 1. This film was free from film cracking in slot processing.

Example 9
A biaxially oriented polyphenylene sulfide film was prepared in the same manner as in Example 1 except that the thickness of the biaxially oriented polyphenylene sulfide film used in Example 1 was changed to 350 μm.

  The measurement and evaluation results on the configuration and properties of the obtained biaxially oriented polyphenylene sulfide film are as shown in Table 1. This film was free from film cracking in slot processing.

(Example 10)
A biaxially oriented polyphenylene sulfide film was prepared in the same manner as in Example 1 except that the thickness of the biaxially oriented polyphenylene sulfide film used in Example 1 was changed to 125 μm.

  The measurement and evaluation results on the configuration and properties of the obtained biaxially oriented polyphenylene sulfide film are as shown in Table 1. This film was free from film cracking in slot processing.

(Example 11)
A biaxially oriented polyphenylene sulfide film was prepared in the same manner as in Example 1 except that the internal pressure of the air chamber was changed to 50 Pa in Example 1.

  The measurement and evaluation results on the configuration and properties of the obtained biaxially oriented polyphenylene sulfide film are as shown in Table 1. This film was free from film cracking in slot processing.

(Comparative Example 1)
A biaxially oriented polyphenylene sulfide film was prepared in the same manner as in Example 1 except that the stretching ratio of the biaxially oriented polyphenylene sulfide film used in Example 1 was changed to 4.0 × 3.7 times (longitudinal direction × width direction). Created.

  The measurement and evaluation results for the structure and properties of the obtained biaxially oriented polyphenylene sulfide film are as shown in Table 1. This film has a low elongation at break in the film longitudinal direction and the width direction, and the film is formed in slot processing. Many cracks occurred.

(Comparative Example 2)
A biaxially oriented polyphenylene sulfide film was prepared in the same manner as in Example 1 except that the stretching ratio of the biaxially oriented polyphenylene sulfide film used in Example 1 was changed to 4.0 × 3.5 times (longitudinal direction × width direction). Created.

  The measurement and evaluation results for the structure and properties of the obtained biaxially oriented polyphenylene sulfide film are as shown in Table 1. This film has a low elongation at break in the film longitudinal direction and the width direction, and the film is formed in slot processing. Many cracks occurred.

(Comparative Example 3)
A biaxially oriented polyphenylene sulfide film was prepared in the same manner as in Example 3 except that the heat setting temperature of the biaxially oriented polyphenylene sulfide film used in Example 3 was changed to 270 ° C.

  The measurement and evaluation results for the structure and properties of the obtained biaxially oriented polyphenylene sulfide film are as shown in Table 1. This film has a low elongation at break in the film longitudinal direction and the width direction, and the film is formed in slot processing. Many cracks occurred.

(Comparative Example 4)
A biaxially oriented polyphenylene sulfide film was prepared in the same manner as in Example 1 except that the air chamber was not installed on the casting drum in Example 1. However, the cast sheet crystallized, and film tearing occurred frequently in the tenter. An axially oriented polyphenylene sulfide film could not be obtained.

(Comparative Example 5)
A biaxially oriented polyphenylene sulfide film was prepared in the same manner as in Example 1 except that the thickness of the biaxially oriented polyphenylene sulfide film used in Example 1 was changed to 500 μm. However, the cast sheet crystallized, and the film was formed with a tenter. Many tears occurred, and a biaxially oriented polyphenylene sulfide film could not be obtained.

(Comparative Example 6)
A biaxially oriented polyphenylene sulfide film was prepared in the same manner as in Example 1 except that the thickness of the biaxially oriented polyphenylene sulfide film used in Example 1 was changed to 100 μm. However, the film thickness was thin, and the slot and wedge were processed. I couldn't.

Claims (5)

A polyarylene sulfide film having a thickness of 125 μm or more and 450 μm or less and a breaking elongation in at least one direction of 100% or more and 200% or less. The polyarylene sulfide film according to claim 1, wherein the polyarylene sulfide is polyphenylene sulfide. The polyarylene sulfide film according to claim 1 or 2, which is biaxially oriented. The polyarylene sulfide film according to any one of claims 1 to 3, wherein a minute endothermic peak (Tmeta) immediately below the melting point is 200 ° C or higher and 260 ° C or lower. The polyarylene sulfide film according to any one of claims 1 to 4, wherein a melt crystallization temperature (Tmc) of the polyarylene sulfide resin is 140 ° C or higher and 220 ° C or lower.