JP5261563B2 - Method for producing polyimide film having high adhesiveness - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide a non-thermoplastic polyimide film whose precursor solution has high storage stability and which achieves high adhesivity without expensive surface treatment. <P>SOLUTION: The high storage stability of the precursor solution and the high adhesivity, in particular, the high adhesion to a polyimide-based adhesive are achieved by specifying polyimide structure and designing the polyimide film so that the average birefringence thereof is controlled to be equal to or less than a specific value. Particularly, the high adhesivity is achieved without performing surface treatment to enhance adhesion. <P>COPYRIGHT: (C)2012,JPO&amp;INPIT

Description

  The present invention has high storage stability of the precursor solution, high adhesion to the adhesive, particularly high adhesion to the thermoplastic polyimide, and can be suitably used for two-layer CCL. The present invention relates to a plastic polyimide film.

  In recent years, the demand for various printed circuit boards has increased along with the reduction in weight, size and density of electronic products. ing. The flexible laminate has a structure in which a circuit made of a metal foil is formed on an insulating film.

  The flexible laminate is generally formed of various insulating materials, and a flexible insulating film is used as a substrate, and a metal foil is bonded to the surface of the substrate by heating and pressure bonding via various adhesive materials. Manufactured by. A polyimide film or the like is preferably used as the insulating film. As the adhesive material, a thermosetting adhesive such as epoxy or acrylic is generally used (FPC using these thermosetting adhesives is hereinafter also referred to as three-layer FPC).

  Thermosetting adhesives have the advantage that they can be bonded at relatively low temperatures. However, in the future, as required characteristics such as heat resistance, flexibility, and electrical reliability become stricter, it is considered that it is difficult to cope with a three-layer FPC using a thermosetting adhesive. On the other hand, an FPC (hereinafter also referred to as a two-layer FPC) in which a metal layer is directly provided on an insulating film or a thermoplastic polyimide is used for an adhesive layer has been proposed. This two-layer FPC has characteristics superior to those of the three-layer FPC, and demand is expected to increase in the future.

However, in general, polyimide film has low adhesion to thermoplastic polyimide, and in order to obtain high adhesion, surface roughening treatment such as plasma treatment and corona treatment, and treatments such as coupling agents and specific metal components are included. It is necessary and has the problem that the cost increases and the characteristics of the film deteriorate. (Patent Documents 1 to 3)
In recent years, improvements in thermal dimensional stability, water absorption properties, and mechanical properties have been desired. For example, by containing a rigid non-thermoplastic polyimide block component with paraphenylenediamine and pyromellitic dianhydride. Although the properties have been achieved, they have poor storage stability of the polyimide precursor solution, and it has been difficult to stably industrially produce them unless molecular weight control is performed to improve storage stability. (Patent Documents 4 and 5)
On the other hand, a polyimide film manufactured from a quaternary copolymerized polyamic acid composed of 3,3 ′, 4,4′-biphenyltetracarboxylic dianhydride, pyromellitic dianhydride, phenylenediamine, and bisaminophenoxyphenylpropane It is disclosed. (Patent Document 5) However, the polyimide film used here is for the purpose of balancing various properties of a film suitable for a TAB tape, and further, by specifying the birefringence, an adhesive is used. No mention is made that the adhesiveness when laminated with a metal foil can be improved. The non-thermoplastic polyimide film of the present invention is a film different from a film having a birefringence greater than 0.14.

JP-A-5-222219 JP-A-6-32926 Japanese Patent Laid-Open No. 11-158276 JP 2000-80178 A JP 2000-119521 A

  This invention is made | formed in view of said subject, The objective is to provide the polyimide film which has adhesiveness with an adhesive agent, especially adhesiveness with a polyimide-type adhesive agent.

  As a result of intensive studies in view of the above problems, the present inventors have prescribed the polyimide structure and designed the polyimide film so that its average birefringence is kept below a specific value. The inventors have found that a polyimide film having high adhesiveness, particularly high adhesiveness with a polyimide adhesive, can be obtained, and the present invention has been completed.

  That is, the present invention includes the following inventions.

  (1) Essential diamine, pyromellitic dianhydride and 3,3 ′, 4,4′-biphenyltetracarboxylic dianhydride containing 2,2-bisaminophenoxyphenylpropane and paraphenylenediamine as essential components A non-thermoplastic polyimide film using an acid dianhydride component as a raw material, and having a mean birefringence of less than 0.14, comprising the 2,2-bis (aminophenoxy) A process for producing a polyimide film comprising a step of selectively reacting (phenyl) propane with 3,3 ′, 4,4′-biphenyltetracarboxylic dianhydride.

  (2) The method for producing a polyimide film according to (1), wherein an elastic modulus is 5 to 10 GPa and an average linear expansion coefficient at 100 to 200 ° C. is 5 to 15 ppm.

  (3) The method for producing a polyimide film according to (1) or (2), wherein the average birefringence is less than 0.13.

  (4) The manufacturing method of the polyimide film of any one of (1)-(3) containing oxydianiline as a diamine component.

  (5) 10 to 50 mol% 2,2-bisaminophenoxyphenylpropane, 30 to 60 mol% paraphenylenediamine, and 10 to 30 mol% oxydianiline based on the diamine component are used. The manufacturing method of the polyimide film of any one of Claims 1.

  (6) The method for producing a polyimide film according to (3) or (4), wherein the oxydianiline is 4,4′-oxydianiline.

  (7) 60 to 95 mol% of pyromellitic dianhydride and 5 to 40 mol% of 3,3 ′, 4,4′-biphenyltetracarboxylic dianhydride are used based on the acid dianhydride component (1) The manufacturing method of the polyimide film of any one of-(6).

The polyimide film obtained by this invention can improve the adhesiveness of metal foil and a polyimide film at the time of manufacturing a flexible metal-clad laminate, for example.
Specifically, by realizing high adhesion, it is possible to cope with the miniaturization of wiring patterns accompanying high-density mounting. In particular, since low adhesion when thermoplastic polyimide is used as the adhesive can be improved, it is possible to cope with an increase in reflow temperature accompanying lead-free soldering.

  The polyimide film of the present invention defines the composition and the average birefringence of the film, and is non-thermoplastic, so that the adhesiveness when the composition, for example, a metal foil and a polyimide film are bonded together with an adhesive is excellent. It has become. One embodiment of the present invention will be described below.

(Composition of polyimide film)
In the present invention, the composition of the polyimide film is defined. The monomer used when manufacturing a polyimide film is demonstrated.
In the present invention, the diamine component can exhibit excellent adhesion by using 2,2-bisaminophenoxyphenylpropane and paraphenylenediamine as essential components. As a general tendency, when the amount of paraphenylenediamine used is increased, the elastic modulus described later increases, the linear expansion coefficient decreases, the birefringence increases, and the amount of 2,2-bisaminophenoxyphenylpropane increases. Decrease in rate, increase in linear expansion coefficient, decrease in birefringence, decrease in water absorption, and improve adhesion. If oxydianiline is further used here, the adhesiveness tends to be further improved, so that oxydianiline is also preferably used. In this case, from the viewpoint of easy balance of linear expansion coefficient and birefringence, 10 to 50 mol% 2,2-bisaminophenoxyphenylpropane, 30 to 60 mol% paraphenylenediamine, It is preferable to use 30 mol% oxydianiline.

  Examples of the oxydianiline include 4,4′-oxydianiline, 3,4′-oxydianiline, 3,3′-oxydianiline, 2,4′-oxydianiline, and among these, 4 , 4′-oxydianiline is preferable because the above problem tends to be solved.

  By using pyromellitic dianhydride and 3,3 ′, 4,4′-biphenyltetracarboxylic dianhydride as essential components as the acid component, excellent adhesion can be expressed. . The preferable use ratio of these is 60 to 95 mol% of pyromellitic dianhydride and 5 to 40 mol% of 3,3 ′, 4,4′-biphenyltetracarboxylic dianhydride. If the use ratio of these acid dianhydrides is out of this range, the adhesive strength tends to decrease or the linear expansion coefficient tends to be too large.

(Average birefringence)
It is important that the polyimide film of the present invention has an average birefringence of less than 0.14. Thereby, the outstanding adhesiveness can be expressed. If the average birefringence exceeds this range, the adhesive strength is reduced, or the adhesive strength after pressure cooker is extremely reduced, making it unsuitable for two-layer CCL applications that require high reliability. Therefore, the polyimide film may be designed using the above composition so that the average birefringence is less than 0.14. The average birefringence of the present invention is determined by determining the extinction angle with a polarizing microscope under a crossed Nicol film piece cut into 2 × 2 cm, and the average value of the birefringence in two directions orthogonal (that is, the maximum birefringence) And the average value of the minimum values). The birefringence referred to in the present invention is the difference between the refractive index in the film plane direction and the refractive index in the thickness direction. The average birefringence is preferably less than 0.13 from the viewpoint of expressing higher adhesion.

(Physical properties of polyimide film)
It is important that the polyimide film of the present invention is non-thermoplastic in addition to the definition of composition and birefringence. Non-thermoplastic refers to a material that melts when the film is heated to about 450 to 500 ° C. and maintains the shape of the film. Therefore, the polyimide film may be designed to be non-thermoplastic using the above composition.

  Furthermore, the polyimide film of the present invention preferably has an elastic modulus of 5 to 10 GPa, more preferably 6 to 9 GPa. If the elastic modulus is below this range, the dimensional stability tends to be poor when applied to a two-layer CCL, and if it exceeds this range, the flexibility of the film tends to be poor and the bending properties of the CCL tend to be reduced.

  The average linear expansion coefficient of the polyimide film of the present invention is preferably 5 to 15 ppm, particularly 7 to 13 ppm. If the value of the average linear expansion coefficient is outside this range, the dimensional stability when the two-layer CCL is used tends to be deteriorated.

(Manufacture of polyimide film)
The polyimide film used in the present invention is manufactured using polyamic acid as a precursor. Any known method can be used as a method for producing the polyamic acid. Usually, the polyamic acid obtained by dissolving a substantially equimolar amount of an aromatic dianhydride and an aromatic diamine in an organic solvent is obtained. The organic solvent solution is produced by stirring under controlled temperature conditions until the polymerization of the acid dianhydride and the diamine is completed. These polyamic acid solutions are usually obtained at a concentration of 5 to 35 wt%, preferably 10 to 30 wt%. When the concentration is in this range, an appropriate molecular weight and solution viscosity are obtained.

As the polymerization method, any known method and a combination thereof can be used. The characteristic of the polymerization method in the polymerization of polyamic acid is the order of addition of the monomers, and the physical properties of the polyimide obtained can be controlled by controlling the order of addition of the monomers. Therefore, in the present invention, any method of adding monomers may be used for the polymerization of polyamic acid. The following method is mentioned as a typical polymerization method. That is,
1) A method in which an aromatic diamine is dissolved in an organic polar solvent and this is reacted with a substantially equimolar amount of an aromatic tetracarboxylic dianhydride for polymerization.
2) An aromatic tetracarboxylic dianhydride is reacted with a small molar amount of an aromatic diamine compound in an organic polar solvent to obtain a prepolymer having acid anhydride groups at both ends. Then, the method of superposing | polymerizing using an aromatic diamine compound so that an aromatic tetracarboxylic dianhydride and an aromatic diamine compound may become substantially equimolar in all the processes.
3) An aromatic tetracarboxylic dianhydride and an excess molar amount of the aromatic diamine compound are reacted in an organic polar solvent to obtain a prepolymer having amino groups at both ends. Subsequently, after adding an aromatic diamine compound here, using the aromatic tetracarboxylic dianhydride so that the aromatic tetracarboxylic dianhydride and the aromatic diamine compound are substantially equimolar in all steps. How to polymerize.
4) A method in which an aromatic tetracarboxylic dianhydride is dissolved and / or dispersed in an organic polar solvent and then polymerized using an aromatic diamine compound so as to be substantially equimolar.
5) A method of polymerizing by reacting a substantially equimolar mixture of aromatic tetracarboxylic dianhydride and aromatic diamine in an organic polar solvent.
And so on. These methods may be used singly or in combination.

  A conventionally well-known method can be used about the method of manufacturing a polyimide film from these polyamic acid solutions. This method includes a thermal imidization method and a chemical imidization method, and either method may be used to produce a film, but the imidization by the chemical imidation method is more preferably used in the present invention. It tends to be easy to obtain a polyimide film having various characteristics.

In addition, the production process of the polyimide film particularly preferable in the present invention is as follows.
a) reacting an aromatic diamine with an aromatic tetracarboxylic dianhydride in an organic solvent to obtain a polyamic acid solution;
b) casting a film-forming dope containing the polyamic acid solution on a support;
c) a step of peeling the gel film from the support after heating on the support;
d) further heating to imidize and dry the remaining amic acid,
It is preferable to contain.

  In the above step, a curing agent containing a dehydrating agent typified by an acid anhydride such as acetic anhydride and an imidation catalyst typified by a tertiary amine such as isoquinoline, β-picoline or pyridine may be used. .

  In the following, a preferred embodiment of the present invention, the chemical imide method, is taken as an example to describe the process for producing a polyimide film. However, the present invention is not limited to the following examples, and the film forming conditions and heating conditions may vary depending on the type of polyamic acid, the thickness of the film, and the like.

For example, a film forming dope is obtained by mixing a dehydrating agent and an imidization catalyst in a polyamic acid solution at a low temperature. Subsequently, this film-forming dope is cast into a film on a support such as a glass plate, an aluminum foil, an endless stainless steel belt, or a stainless drum, and the temperature on the support is 80 ° C. to 200 ° C., preferably 100 ° C. to 180 ° C. After partially curing and / or drying by activating the dehydrating agent and imidization catalyst by heating in the region, the polyamic acid film (hereinafter referred to as gel film) is obtained by peeling from the support.
The gel film is in the intermediate stage of curing from polyamic acid to polyimide and has self-supporting properties,
(AB) × 100 / B (1)
In formula (1), A and B represent the following.
A: Weight of gel film B: The volatile content calculated from the weight after heating the gel film at 450 ° C. for 20 minutes is in the range of 5 to 500% by weight, preferably 5 to 200% by weight, more preferably 5 to 5%. It is in the range of 150% by weight. It is preferable to use a film in this range, and problems such as film breakage, uneven film color due to drying unevenness, and characteristic variations may occur during the baking process.
The preferable amount of the dehydrating agent is 0.5 to 5 mol, preferably 1.0 to 4 mol, relative to 1 mol of the amic acid unit in the polyamic acid.
Moreover, the preferable quantity of an imidation catalyst is 0.05-3 mol with respect to 1 mol of amic acid units in a polyamic acid, Preferably it is 0.2-2 mol.
If the dehydrating agent and the imidization catalyst are below the above ranges, chemical imidization may be insufficient, and may break during firing or mechanical strength may decrease. Moreover, when these amounts exceed the above range, the progress of imidization becomes too fast, and it may be difficult to cast into a film, which is not preferable.

  The end of the gel film is fixed to avoid shrinkage during curing, water, residual solvent, residual conversion agent and catalyst are removed, and the remaining amic acid is completely imidized to obtain the present invention. A polyimide film is obtained.

  At this time, it is preferable to finally heat at a temperature of 400 to 650 ° C. for 5 to 400 seconds. Above this temperature and / or for a long time, the film may suffer from thermal degradation and may cause problems. Conversely, if the temperature is lower than this temperature and / or the time is shorter, the predetermined effect may not be exhibited.

  Moreover, in order to relieve the internal stress remaining in the film, heat treatment can be performed under the minimum tension necessary for transporting the film. This heat treatment may be performed in the film manufacturing process, or may be provided separately. The heating conditions vary depending on the characteristics of the film and the apparatus used, and therefore cannot be determined in general. The internal stress can be relaxed by heat treatment at a temperature of 450 ° C. or lower for 1 to 300 seconds, preferably 2 to 250 seconds, particularly preferably 5 to 200 seconds.

  Further, the film can be stretched before and after fixing the gel film. At this time, the preferable volatile content is 100 to 500% by weight, preferably 150 to 500% by weight. If the volatile content is below this range, stretching tends to be difficult, and if it exceeds this range, the self-supporting property of the film is poor and the stretching operation itself tends to be difficult.

  For stretching, any known method such as a method using a differential roll or a method of widening the fixing interval of the tenter may be used.

Furthermore, the average birefringence of the polyimide film of the present invention is 0.14 or less, preferably 0.13 or less. In the present invention, any method may be used as a method for controlling the average birefringence of the polyimide film. For example, the birefringence can be controlled by the following method.
1) Increased by changing the mixing ratio of the monomers used (more paraphenylenedidiamine and less 2,2-bis (aminophenoxyphenyl) propane) 3,3 ', 4,4'-biphenyltetracarboxylic acid (Increased dianhydride tends to decrease)
2) Change the order of monomer addition during polymerization (selecting the order of addition such that paraphenylenediamine and pyromellitic dianhydride react selectively increases the amount of 2,2-bis (aminophenoxyphenyl) propane and (It tends to be smaller when the order of addition is selected so that 3,3 ′, 4,4′-biphenyltetracarboxylic dianhydride reacts selectively)
3) Change the film forming conditions (they tend to decrease when the volatile content is lowered and the temperature of the first stage of the heating process is set low)
4) Various amounts of dehydrating agent and imidation catalyst are changed (they tend to decrease if the amount of dehydrating agent and / or imidization catalyst is reduced).
5) Stretching operation during film formation (increases when the stretching ratio is increased, and conversely tends to decrease when the operation is contracted)
6) As a preferred solvent for synthesizing a polyimide precursor (hereinafter referred to as polyamic acid) appropriately combining the above methods, any solvent that dissolves polyamic acid can be used. N-dimethylformamide, N, N-dimethylacetamide, N-methyl-2-pyrrolidone and the like, and N, N-dimethylformamide and N, N-dimethylacetamide can be particularly preferably used.

  In addition, a filler can be added for the purpose of improving various film properties such as slidability, thermal conductivity, conductivity, corona resistance, and loop stiffness. Any filler may be used, but preferred examples include silica, titanium oxide, alumina, silicon nitride, boron nitride, calcium hydrogen phosphate, calcium phosphate, mica and the like.

The particle size of the filler is not particularly limited because it is determined by the film characteristics to be modified and the kind of filler to be added, but generally the average particle size is 0.05 to 100 μm, preferably 0.1. It is -75 micrometers, More preferably, it is 0.1-50 micrometers, Most preferably, it is 0.1-25 micrometers. If the particle size is below this range, the modification effect is less likely to appear. If the particle size is above this range, the surface properties may be greatly impaired or the mechanical properties may be greatly deteriorated. Further, the number of added parts of the filler is not particularly limited because it is determined by the film properties to be modified, the filler particle diameter, and the like. Generally, the addition amount of the filler is 0.01 to 100 parts by weight, preferably 0.01 to 90 parts by weight, and more preferably 0.02 to 80 parts by weight with respect to 100 parts by weight of the polyimide. If the amount of filler added is less than this range, the effect of modification by the filler hardly appears, and if it exceeds this range, the mechanical properties of the film may be greatly impaired. Addition of filler
1. 1. A method of adding to a polymerization reaction solution before or during polymerization 2. A method of kneading fillers using three rolls after the completion of polymerization. Any method such as preparing a dispersion containing filler and mixing it with a polyamic acid organic solvent solution may be used, but a method of mixing a dispersion containing filler with a polyamic acid solution, particularly immediately before film formation. This method is preferable because the contamination by the filler in the production line is minimized. When preparing a dispersion containing a filler, it is preferable to use the same solvent as the polymerization solvent for the polyamic acid. Further, in order to disperse the filler satisfactorily and stabilize the dispersion state, a dispersant, a thickener and the like can be used within a range not affecting the film physical properties.

  The polyimide film of the present invention obtained as described above has not only excellent adhesion in a normal state when a metal foil is laminated through an adhesive, for example, but also excellent adhesion after a PCT test. ing. In particular, the adhesiveness with the polyimide-based adhesive can be improved, but the polyimide film of the present invention can also use an adhesive other than the polyimide-based adhesive, and can be directly provided with a metal. It may be used.

  The present invention may also include the following aspects.

  (1) 2,2-bisaminophenoxyphenylpropane and paraphenylenediamine as diamine components, pyromellitic dianhydride and 3,3 ′, 4,4′-biphenyltetracarboxylic dianhydride as acid dianhydride components A polyimide film characterized by having an elastic modulus of 5 to 10 GPa, an average coefficient of linear expansion at 100 to 200 ° C. of 5 to 15 ppm, and an average birefringence of less than 0.14. .

  (2) The polyimide film according to the invention is characterized in that an average birefringence is less than 0.13.

  (3) Still further, the present invention is characterized in that the polyimide film contains oxydianiline as a diamine component.

  (4) Further, the present invention is characterized by using 10 to 50 mol% 2,2-bisaminophenoxyphenylpropane, 30 to 60 mol% paraphenylenediamine and 10 to 30 mol% oxydianiline based on the diamine component. The polyimide film.

  (5) The polyimide film according to the invention, wherein the oxydianiline is 4,4'-oxydianiline.

  (6) The present invention further comprises 60 to 95 mol% of pyromellitic dianhydride and 5 to 40 mol% of 3,3 ′, 4,4′-biphenyltetracarboxylic dianhydride based on the acid dianhydride component. The polyimide film characterized by being used.

  EXAMPLES Hereinafter, although an Example demonstrates this invention concretely, this invention is not limited only to these Examples.

The average birefringence, elastic modulus, linear expansion coefficient, and adhesion evaluation method in the synthesis examples, examples, and comparative examples are as follows.
(Average birefringence)
An extinction angle is determined with a polarizing microscope (OPTOPHOT / POL, manufactured by Nihon Kogyo Co., Ltd.) under a crossed Nicol film piece cut into 2 × 2 cm, and the average value of birefringence in two orthogonal directions (that is, the maximum value of the birefringence) And the average value of the minimum values). The birefringence referred to in the present invention is the difference between the refractive index in the film plane direction and the refractive index in the thickness direction.

The birefringence was measured using a refractometer (manufactured by Atago Co., Ltd., 4T type) equipped with an eyepiece with a polarizing plate and using a Na lamp as a light source.
(Adhesion evaluation)
As a pretreatment, the polyimide film was surface-treated at a corona density of 200 W · min / m 2.

After diluting the polyamic acid solution obtained in Reference Example 1 with DMF to a solid content concentration of 10% by weight, the final single-sided thickness of the thermoplastic polyimide layer (adhesive layer) is 4 μm on both sides of the surface-treated polyimide film. After applying the polyamic acid, heating was performed at 140 ° C. for 1 minute. Subsequently, heat imidization was performed by passing through a far infrared heater furnace having an atmospheric temperature of 390 ° C. for 20 seconds to obtain a heat resistant adhesive film. By using 18 μm rolled copper foil (BHY-22B-T, manufactured by Japan Energy Co., Ltd.) on both sides of the obtained adhesive film, and further using a protective material (Apical 125 NPI; manufactured by Kaneka Chemical Co., Ltd.) on both sides of the copper foil, FCCL was manufactured by performing thermal lamination under conditions of a lamination temperature of 360 ° C., a lamination pressure of 196 N / cm (20 kgf / cm), and a lamination speed of 1.5 m / min. From this FCCL, a sample was prepared according to “6.5 peel strength” of JIS C6471, and a 5 mm wide metal foil part was peeled off at a peeling angle of 180 degrees and 50 mm / min, and the load was measured. .
The pressure cooker test (PCT) measured the adhesive strength after treating at 121 ° C. and 100% RH for 96 hours.
(Elastic modulus)
The elastic modulus was measured according to ASTM D882.
(Linear expansion coefficient)
The linear expansion coefficient at 50 to 200 ° C. was measured by using TMA120C manufactured by Seiko Electronics Co., Ltd. (sample size: 3 mm width, 10 mm length), and the temperature was temporarily increased from 10 ° C. to 400 ° C. at a load of 3 g at 10 ° C./min. After heating, the temperature was cooled to 10 ° C., the temperature was further increased at 10 ° C./min, and the average value was calculated from the thermal expansion coefficients at 50 ° C. and 200 ° C. during the second temperature increase.
(Judgment of plasticity)
The plasticity is determined by fixing the obtained film 20 × 20 cm to a square SUS frame (outer diameter 20 × 20 cm, inner diameter 18 × 18 cm), heat-treating at 450 ° C. for 3 minutes, and maintaining the form. Things were non-thermoplastic, and wrinkled or stretched were made thermoplastic.
(Reference Example 1: Synthesis of thermoplastic polyimide precursor)
780 g of DMF and 115.6 g of 2,2-bis [4- (4-aminophenoxy) phenyl] propane (BAPP) were added to a glass flask having a capacity of 2000 ml, and 3,3′4 while stirring under a nitrogen atmosphere. , 4′-Biphenyltetracarboxylic dianhydride (BPDA) was gradually added. Subsequently, 3.8 g of ethylenebis (trimellitic acid monoester acid anhydride) (TMEG) was added and stirred for 30 minutes in an ice bath. A solution in which 2.0 g of TMEG was dissolved in 20 g of DMF was separately prepared, and this was gradually added to the reaction solution while being careful of the viscosity and stirred. When the viscosity reached 3000 poise, addition and stirring were stopped to obtain a polyamic acid solution.
This polyamic acid solution was cast on a 25 μm PET film (Therapy HP, manufactured by Toyo Metallizing Co., Ltd.) so as to have a final thickness of 20 μm, and dried at 120 ° C. for 5 minutes. After peeling off the dried self-supporting film from PET, it is fixed to a metal pin frame and dried at 150 ° C. for 5 minutes, 200 ° C. for 5 minutes, 250 ° C. for 5 minutes, 350 ° C. for 5 minutes, A single layer sheet was obtained. The glass transition temperature of this thermoplastic polyimide was 240 ° C.

(Examples 1 and 2)
2,2-bis (4-aminophenoxyphenyl) propane (BAPP) and 4,4′-oxydianiline (4,4′ODA) were dissolved in N, N-dimethylformamide (DMF) cooled to 10 ° C. . After 3,3 ′, 4,4′-biphenyltetracarboxylic dianhydride (BPDA) was added and dissolved therein, pyromellitic dianhydride (PMDA) was added and stirred for 30 minutes. A polymer was formed. The mixing ratio of each monomer is as shown in Table 1.
After p-phenylenediamine (p-PDA) was dissolved in this solution, PMDA was added and stirred for 1 hour to dissolve. Further, a DMF solution of PMDA (PMDA 1.85 g / DMF 24.6 g) prepared separately was carefully added to this solution, and the addition was stopped when the viscosity reached about 3000 poise. Stirring was performed for 1 hour to obtain a polyamic acid solution having a solid content of about 19% by weight and a rotational viscosity at 23 ° C. of 3400 poise.
To 100 g of this polyamic acid solution, 50 g of a curing agent composed of acetic anhydride / isoquinoline / DMF (weight ratio 18.90 / 7.17 / 18.93) was added, and the mixture was stirred and degassed at a temperature of 0 ° C. or less. Using a coater, it was cast on aluminum foil. This resin film is heated at 130 ° C. for 100 seconds, and then the self-supporting gel film is peeled off from the aluminum foil (volatile content 45% by weight) and fixed on a metal frame, 300 ° C. × 20 seconds, 450 ° C. × 20 Second and 500 ° C. × 20 seconds to dry and imidize to obtain a polyimide film having a thickness of 18 μm. The obtained film properties and adhesive properties are shown in Table 1.

(Comparative Example 1)
After p-PDA was dissolved in DMF cooled to 10 ° C., PMDA was added and stirred for 1 hour to dissolve. BAPP was added and dissolved therein, and then PMDA was added to obtain a polyamic acid solution having a solid content concentration of about 19% by weight. Using this solution, a polyimide film having a thickness of 18 μm was obtained in the same manner as in Example 1. The obtained film properties and adhesive properties are shown in Table 1.

(Comparative Example 2)
A film was prepared and evaluated according to Example 1 of JP-A-2000-119521.
That is, after putting 150 ml of DMAc into a 500 cc glass flask, p-PDA was dissolved, then BAPP, BPDA and PMDA were sequentially added and stirred at room temperature for about 1 hour. Subsequently, 0.5 mol% of phthalic anhydride with respect to the diamine component was added and stirred for about 1 hour, and the polyamic acid concentration of p-PDA / BAPP / BPDA / PMDA = 70/30/30/70 was 20 A weight percent solution was obtained. 60 g of this copolymerized polyamic acid solution was added with 25.4 ml of DMAc, 7.2 ml of acetic anhydride and 7.2 ml of β-picoline, stirred and degassed at a temperature of 0 ° C. or lower, and then using a comma coater. It was cast on a glass plate. The glass plate was heated on a hot plate heated to 150 ° C. for about 4 minutes to form a self-supporting gel film, which was peeled from the glass plate. This gel film (volatile content 30% by weight) is fixed to a metal frame and heated for 30 minutes while raising the temperature from 250 ° C. to 330 ° C., and then heated at 400 ° C. for about 5 minutes to obtain a polyimide film having a thickness of about 25 μm. It was. The obtained film properties and adhesive properties are shown in Table 1.

(Comparative Example 3)
A film was prepared and evaluated according to Example 2 of JP-A-2000-119521.
That is, after putting 150 ml of DMAc into a 500 cc glass flask, p-PDA was dissolved, then PMDA was added, and the mixture was stirred at room temperature for about 1 hour. After BAPP was added to this solution and completely dissolved, BPDA was further added and stirred at room temperature for about 1 hour. Subsequently, 0.25 mol% acetic anhydride with respect to the diamine component was added, and the mixture was further stirred for about 1 hour, and the polyamic acid concentration of p-PDA / BAPP / BPDA / PMDA = 50/50/50/50 was 20 A weight percent solution was obtained. Using this solution, a polyimide film having a thickness of about 25 μm was obtained in the same manner as in Comparative Example 3. The obtained film characteristics are shown in Table 1.

Claims (6)

Acids containing 2,2-bisaminophenoxyphenylpropane and paraphenylenediamine as essential components, pyromellitic dianhydride and 3,3 ′, 4,4′-biphenyltetracarboxylic dianhydride as essential components A non-thermoplastic polyimide film using a dianhydride component as a raw material, and a method for producing a polyimide film having an average birefringence of less than 0.14,
Have a step of selectively reacting the 2,2-bis aminophenoxy phenyl propane and 3,3 ', 4,4'-biphenyl tetracarboxylic acid dianhydride,
A method for producing a polyimide film comprising oxydianiline as a diamine component .   The method for producing a polyimide film according to claim 1, wherein an elastic modulus is 5 to 10 GPa and an average linear expansion coefficient at 100 to 200 ° C. is 5 to 15 ppm.   The method for producing a polyimide film according to claim 1 or 2, wherein the average birefringence is less than 0.13.   The use of 10 to 50 mol% 2,2-bisaminophenoxyphenylpropane, 30 to 60 mol% paraphenylenediamine, and 10 to 30 mol% oxydianiline based on the diamine component The manufacturing method of the polyimide film of any one of Claims 1. The method for producing a polyimide film according to claim 1 , wherein the oxydianiline is 4,4'-oxydianiline. 60 to 95 mol% of pyromellitic dianhydride and 5 to 40 mol% of 3,3 ′, 4,4′-biphenyltetracarboxylic dianhydride are used based on the acid dianhydride component. the process for producing a polyimide film as described in any one of clauses 1-5.