JP5046126B2 - Nylon 6 / polypropylene blend oriented film and method for producing the same - Google Patents

Description

  The present invention has an orthogonal orientation structure in which the molecular chain axes of nylon 6 and polypropylene are oriented in directions orthogonal to each other, or a tilted orientation structure in which molecular chain axes are oriented in directions oblique to each other, and has excellent two-dimensional mechanical properties. The present invention relates to a crystallographic film and a method for producing the same.

Various polymers are used as molding materials, but the properties that can be imparted by the polymers alone are limited. By blending multiple polymers, the strength and heat resistance can be improved compared to the case of a single polymer. Various multicomponent resin compositions with improved high impact properties have been developed.
There are two types of polymer blends, a compatible blend in which the constituent components are mutually soluble and an incompatible blend in which the constituent components are not compatible. In many cases, it is used by strengthening the interface.
For example, nylon 6 blended with polypropylene has the properties of nylon 6, such as impact resistance, chemical resistance, and thermal stability, and the low water absorption, chemical stability, and low cost properties of polypropylene. Although it is expected as a material having a good balance, since nylon and polypropylene are incompatible with each other, various compatibilizations have been reported (Patent Documents 1 and 2).

On the other hand, it is well known to create a material reinforced in the stretching direction by stretching a polymer film or rod in one direction, and it is applied to many polymer materials.
The present inventors have repeatedly studied stretched films made of several polymer blends.
For example, in Patent Document 1, when a uniaxially stretched film is produced from a compatible polymer blend composed of crystalline polystyrene and polyphenylene oxide (PPO), the film is stretched by combining orientation control by stretching and crystallization by heat treatment. The orientation degree of the crystalline isotactic polystyrene in the direction is 0.6 to 1, and the molecular chain of PPO is randomly oriented, and the strength in the direction perpendicular to the stretching direction of the film is It has been found that a uniaxially stretched film can be obtained that has the same strength as the unstretched film of crystalline polystyrene constituting the film, and whose strength in the stretching direction of the film exceeds the strength of the unstretched film of crystalline polystyrene constituting the film. .
Patent Document 2 is obtained by dissolving a compatible polymer polyvinylidene fluoride (PVdF) and polybutylene succinate (PBSU) in a solvent, forming a film, heating and melting the film, and then rapidly cooling. The film is uniaxially stretched and then melted at a temperature lower than the melting point of PVdF and higher than that of PBSU, and then kept at 50 to 100 ° C. to crystallize PBSU. A multiaxial crystallographic film in which both the crystal axis (c axis) and the crystallographic axis (b axis) perpendicular to the molecular chain of PBSU are oriented in the stretching direction is obtained, and the film is compared with the strength of the non-oriented blend film. Thus, it has been found to have physical properties that are 4 to 7.5 times stronger in the stretching direction and 1.2 to 1.5 times stronger in the direction perpendicular to the stretching.

  Furthermore, the present inventors have earnestly studied a film composed of an incompatible polymer blend, and a polymer blend composed of polyvinylidene fluoride (PVdF) and nylon 11 (Patent Document 3) or polyvinylidene fluoride (PVdF). A polymer blend consisting of nylon 6 and nylon 6 is kneaded, then formed into a sheet by hot pressing, uniaxially stretched, and then only PVdF is melted at a temperature lower than the melting point of nylon and then slowly cooled to crystallize PVdF. As a result, the crystal axis (c axis) in the molecular chain direction of nylon and the crystal axis (b axis) in the perpendicular direction to the molecular chain of PVdF are both oriented in the stretching direction, and the breaking strength is obtained in two directions of the stretching direction and the perpendicular direction. It has been found that a multiaxial crystal oriented film having an improved elastic modulus can be obtained.

However, a film made of nylon 6 / polypropylene blend, which is an incompatible polymer blend, has not yet been fully studied.
For example, Patent Document 5 describes that a film made of nylon 6 / polypropylene blend is used as a packaging film because it exhibits easy tearability, but for stretching, tearability is not impaired. It is only said that characteristics such as tear strength and breaking strength may be adjusted by uniaxial or biaxial stretching treatment within a range.
In addition, regarding the fiber made of nylon 6 / polypropylene blend, the structure of the blended fiber and the change in the strength and elongation properties due to stretching have been reported (see Non-Patent Document 3), but the film has not been studied. .
Japanese Patent No. 3783052 Japanese Patent No. 3968210 Japanese Patent No. 4035607 JP 2007-302723 A JP-A-7-299858 Ide, F .; Hasegawa, A. Studies on polymer blend of nylon 6 and polypropylene or nylon 6 and polystyrene using the reaction of polymer.J. Appl.Polym. Sci. 1974, 18, 963-974. Gonzalez-Montiel, A .; Keskkula, H .; Paul, DR Impact-modified nylon 6 / polypropylene blends: 1. Morphology-property relationships. Polymer 1995, 36, 4587-4603. Changes in structure and strength properties of polypropylene / polyamide 6 blend fiber due to stretching, Takahashi, Chikita, Shimizu, Journal of Textile Society, 52, 396, (1996)

As mentioned above, nylon 6 / polypropylene blend balances the properties of nylon 6, such as impact resistance, chemical resistance, and thermal stability, with low water absorption, chemical stability, and low cost properties of polypropylene. Although it is expected as a material having a combination, it is necessary to further improve the mechanical properties, but it has not yet been fully studied.
The present invention has been made in view of such circumstances, and by controlling the crystal orientation of polypropylene by orientation-crystallizing polypropylene in a stretched film of nylon 6 / polypropylene blend, the dynamics of nylon 6 / polypropylene blend are controlled. The purpose is to improve physical properties.

  As a result of intensive studies to achieve the above object, the inventors have achieved excellent physical properties of a polymer blend of nylon 6 and polypropylene by controlling the crystal orientation of polypropylene in the nylon 6 orientation film. It was found that the mechanical properties can be improved by improving the breaking strength and elastic modulus in the stretching direction and the vertical direction while maintaining the same.

The present invention has been completed based on these findings, and is as follows.
[1] A blend film containing nylon 6, isotactic polypropylene, and a compatibilizer, a crystal axis (b axis) in the molecular chain direction of nylon 6 and a crystal axis (c axis) in the molecular chain direction of isotactic polypropylene Crystal oriented films in which the films are oriented in different directions.
[2] The crystal oriented film according to [1], wherein the compatibilizing agent is polypropylene grafted with maleic anhydride.
[3] The crystal orientation according to [1] or [2], wherein the nylon 6 and isotactic polypropylene (PP) are contained at a weight ratio of nylon 6 / PP = 50/50 to 90/10. the film.
[4] The crystal oriented film according to claim 1 or 2, comprising 0.1 to 30% by weight of the compatibilizer.
[5] Nylon 6, astactic polypropylene and a compatibilizing agent are kneaded, then formed into a sheet shape by hot pressing and uniaxially stretched, then lower than the melting point of nylon 6 and higher than the melting point of isotactic polypropylene. A method for producing a crystal orientation film, comprising melting isotactic polypropylene at a temperature and then recrystallizing isotactic polypropylene in a stretched nylon 6 / isotactic polypropylene blend.

  By controlling the crystal orientation of polypropylene in the nylon 6 orientation film according to the present invention, the strength and elastic modulus in the stretching and vertical directions are improved while maintaining the excellent physical properties of the nylon 6 / polypropylene blend. The mechanical properties can be improved.

  The present invention is a blend film containing nylon 6, isotactic polypropylene and a compatibilizing agent, wherein the crystal axis (b axis) in the molecular chain direction of nylon 6 and the crystal axis (c axis) in the molecular chain direction of isotactic polypropylene. ) Are oriented in different directions from each other.

  In the polymer blend constituting the crystal orientation film of the present invention, the composition of nylon-6 (polyundecanamide) and isotactic polypropylene (PP) may be any ratio, but the weight ratio of nylon 6 / Those containing PP = 50/50 to 90/10, more preferably nylon 6 / PP = 60/40 to 80/20. When there is too much quantity of nylon 6, the effect acquired by blending a polypropylene will become small. On the other hand, if the amount of polypropylene is too large, the polypropylene becomes a matrix to form a continuous phase, so that the orientation is disturbed during the crystallization process, and the desired orientation structure cannot be formed.

The compatibilizer used in the crystal orientation material of the present invention is a compound that exhibits reactivity, compatibility, or affinity for an incompatible polymer blend composed of nylon 6 and isotactic polypropylene (PP). There is no particular limitation as long as it is present.
The compatibilizing agent includes, for example, a modified polyolefin having a functional group introduced therein, and examples of the functional group include an epoxy group such as a carboxyl group, an acid anhydride group, an ester group, and a glycidyl group. A combination of a plurality of these functional groups may be introduced into the polyolefin, or two or more of these modified polyolefins may be combined.
In the present invention, propylene is used as a preferred olefin of the modified polyolefin, and as a preferred functional group, an acid anhydride of an ethylenically unsaturated polyvalent carboxylic acid such as an ethylenically unsaturated carboxylic acid and its ester or maleic anhydride. In particular, in the present invention, polypropylene grafted with maleic anhydride (PP-g-MA) is preferably used.

  The proportion of the compatibilizing agent in the polymer blend constituting the crystal orientation film of the present invention may be any proportion as long as the interface is strengthened and the phase structure is refined. What contains 0.1-30%, More preferably, what contains 1-10% is good.

The crystal orientation film of the present invention is produced by combining orientation control by stretching and crystallization by heat treatment when producing a uniaxially stretched film from a polymer blend containing nylon 6, isotactic polypropylene, and a compatibilizer. Can do.
Specifically, for example, isotactic polypropylene (PP) is used as crystalline polypropylene, and nylon 6 and a compatibilizing agent are added thereto and kneaded to form a polymer blend composed of nylon 6, PP and the compatibilizing agent. Make it. Kneading is performed using a kneader in a state where the polymer blend containing nylon 6, isotactic polypropylene, and a compatibilizing agent is melted, but any kneader may be used. The kneading temperature is kneading at a melting temperature of nylon 6 (230 ° C.) or higher, preferably 235 to 340 ° C.

  Subsequently, the obtained kneaded material is melted at 230 to 235 ° C. by hot pressing and formed into a sheet shape, and further 20 to 200 ° C., preferably 80 to 160 ° C., uniaxially more than twice, Preferably it extends 3 times or more.

After stretching, the polypropylene is melted at a temperature lower than the melting temperature of nylon 6 and higher than the melting temperature of polypropylene, preferably at a temperature of 175 ° C. or higher and 210 ° C. or lower.
The crystallization of polypropylene may be isothermal crystallization at a constant temperature or non-isothermal crystallization at a constant cooling rate, and does not depend on the cooling method.

Next, the present invention will be described more specifically based on examples, but the present invention is not limited to the following examples.
Example 1
Nylon 6, isotactic polypropylene (PP), and maleic anhydride grafted polypropylene (PP-g-MA), 35 g, 10 g, and 5 g, were vacuum dried at 80 ° C. for 24 hours, respectively, and then kneaded. A nylon 6 / PP / PP-g-MA = 70/20/10 (weight ratio) blend was produced by kneading at 235 ° C. for 10 minutes. It was melted at 233 ° C. using a hot press and formed into a sheet. Further, the film was stretched 3.7 times at 140 ° C. to prepare an alignment film. The shape of the stretched film was fixed and held at 200 ° C. for 3 minutes to melt PP, and then heat-treated at 130 ° C. for 4 hours under vacuum to cause oriented crystallization of PP.

When the stretched film was observed with an electron microscope, it was observed that PP domains (diameter of about 200 to 500 nm) deformed into a cylindrical shape were distributed in the nylon 6 matrix and oriented in the stretch direction.
FIG. 1 is a wide-angle X-ray diffraction image of a film obtained by orientation-crystallizing PP obtained in Example 1, with the meridian (vertical direction) in the stretching direction and the equator (horizontal direction) in the direction perpendicular to the stretching. Correspond.
FIG. 2 shows the azimuth angle dependence of the diffraction intensity of 110 reflection (-----) and 040 reflection (-------) of polypropylene in a film obtained by orientation-crystallizing PP obtained in Example 1. In the figure, the azimuth angles of 0 degrees and ± 90 degrees correspond to the stretching direction and the vertical direction, respectively.

  In the wide-angle X-ray diffraction image (FIG. 1), 200 reflection and 002 reflection of nylon 6 are observed in the equator direction (perpendicular to the stretching direction), and the molecular chain axis (crystal b axis) of nylon 6 is oriented in the stretching direction. It was confirmed that Furthermore, when examining the azimuth dependence (FIG. 2) of the X-ray diffraction intensity of the 110-angle reflection and the 040 reflection of the wide-angle X-ray diffraction image (FIG. 1), the 040 reflection of PP is observed as a spot in the vertical direction. The crystal b-axis of PP is highly oriented in the direction perpendicular to the stretching. Further, 110 reflection is observed mainly at an angle slightly inclined from the stretching direction (azimuth angle ± 15 °), and from this, the a * axis is oriented in the stretching direction, and the molecular chain axis (crystal c axis) and crystal b axis Were confirmed to be oriented in the vertical direction.

FIG. 3 is a diagram showing a stress-strain curve of a film obtained by orientation-crystallizing PP obtained in Example 1, in which (-----) indicates that the orientation-crystallized sample was tested in the stretching direction. (-----) indicates that when the oriented crystallized sample is tested in the vertical direction, (---------) indicates that nylon 6 / PP / PP / PP-g-MA = Fig. 7 represents a stress-strain curve of an unstretched sample of a 70/20/10 (weight ratio) blend.
As is clear from FIG. 3, when the tensile test was performed, the strength and elastic modulus in the stretching direction were 180 MPa and 1.72 GPa, respectively. In addition, the strength and elastic modulus in the stretched and vertical directions were 35.0 MPa and 1.22 GPa, respectively, and excellent mechanical properties were exhibited in two directions compared to the unstretched film.

(Example 2)
A stretched film was produced in the same manner as in Example 1 for the nylon 6 / PP / PP-g-MA = 70/20/10 (weight ratio) blend. The shape of the stretched film was fixed and PP was melted at 200 ° C. for 3 minutes, then dropped in ice water and rapidly cooled to cause oriented crystallisation of PP.
FIG. 4 is a wide-angle X-ray diffraction image of a film obtained by orientation-crystallizing PP obtained in Example 2, with the meridian (vertical direction) in the stretching direction and the equator (horizontal direction) in the direction perpendicular to the stretching. Correspond.
FIG. 5 shows the azimuth angle dependence of the diffraction intensity of 110 reflection (-----) and 040 reflection (-------) of polypropylene in a film obtained by orientation crystallizing PP obtained in Example 2. In the figure, the azimuth angles of 0 degrees and ± 90 degrees correspond to the stretching direction and the vertical direction, respectively.

  From the wide-angle X-ray diffraction image (FIG. 4), it was confirmed that the molecular chain axis (b axis) of nylon 6 was oriented in the stretching direction, as in Example 1. According to the wide-angle X-ray diffraction image (FIG. 4) and the azimuth angle dependence of the X-ray diffraction intensity of 110 reflection and 040 reflection (FIG. 5), the 040 reflection of PP is observed as a spot in the vertical direction, and the crystal b axis is vertical. Highly oriented in the direction. On the other hand, the 110 reflection of PP showed a complicated azimuth angle dependency, and showed spot-like reflection at ± 15 ° and ± 90 ° from the stretching direction. The 110 reflection with an azimuth angle of ± 15 ° is due to the orientation of the PP crystal in the stretching direction of the a * axis. The 110 reflection at azimuth ± 42 ° increases with the appearance of the 111 reflection on the meridian (stretching direction), indicating that a tilted orientation of the crystal c axis of PP has been formed. From the above, it was confirmed that in the quenched film, unlike the heat-treated sample of Example 1, a * axis orientation (vertical orientation of crystal c axis) and tilt orientation of crystal c axis coexist.

FIG. 6 is a diagram showing a stress-strain curve of a film obtained by orientation-crystallizing PP obtained in Example 2, in which (-----) indicates a test of the orientation-crystallized sample in the stretching direction. (-----) indicates that when the oriented crystallized sample is tested in the vertical direction, (---------) indicates that nylon 6 / PP / PP / PP-g-MA = Fig. 7 represents a stress-strain curve of an unstretched sample of a 70/20/10 (weight ratio) blend.
As is apparent from FIG. 6, when the tensile test was performed, the strength and elastic modulus in the stretching direction were 161.5 MPa and 1.35 GPa, respectively. In addition, the strength and elastic modulus in the stretched and perpendicular directions were 37.6 MPa and 1.10 GPa, respectively, and excellent mechanical properties were exhibited in two directions compared to the unstretched film.

(Example 3)
A stretched film was prepared in the same manner as in Example 1 for a nylon 6 / PP / PP-g-MA = 70/29/1 (weight ratio) blend having a composition ratio different from that in Example 1 and Example 2. The shape of the stretched film was fixed and PP was melted at 200 ° C. for 3 minutes, and then heat-treated at 130 ° C. for 4 hours under vacuum to cause oriented crystallization of PP.
When the stretched film was observed with an electron microscope, it was observed that PP domains (diameter of about 1 to 2 microns) deformed into a cylindrical shape were distributed in the nylon 6 matrix and oriented in the stretching direction.
FIG. 7 is a wide-angle X-ray diffraction image of a film obtained by orientation-crystallizing PP obtained in Example 3, with the meridian (vertical direction) in the stretching direction and the equator (horizontal direction) in the direction perpendicular to the stretching. Correspond.
FIG. 8 shows the azimuth angle dependency of the diffraction intensity of 110 reflection (------) and 040 reflection (-------) of polypropylene in a film obtained by orientation crystallizing PP obtained in Example 3. In the figure, the azimuth angles of 0 degrees and ± 90 degrees correspond to the stretching direction and the vertical direction, respectively.

  According to the wide-angle X-ray diffraction image (FIG. 7), it was confirmed that the molecular chain axis (crystal b-axis) of nylon 6 was oriented in the stretching direction as in the case of Example 1 and Example 2. Furthermore, when examining the azimuth angle dependence (FIG. 8) of the X-ray diffraction intensity of the 110-angle reflection and the 040-reflection of the PP (FIG. 7), the PP 040 reflection is observed in the vertical direction. The crystal b-axis is highly oriented in the direction perpendicular to the stretch. Further, 110 reflection is mainly observed at an azimuth angle of ± 15 °. From this, as in Example 1, the a * axis is oriented in the stretching direction, and the molecular chain axis (crystal c axis) and the crystal b axis are perpendicular. It was confirmed that they were oriented.

FIG. 9 is a diagram showing a stress-strain curve of a film obtained by orientation-crystallizing PP obtained in Example 3, in which (-----) indicates a test of the orientation-crystallized sample in the stretching direction. (-----) indicates that when the oriented crystallized sample is tested in the vertical direction, (---------) indicates that nylon 6 / PP / PP-g-MA = 70 / Fig. 4 represents a stress-strain curve of an unstretched sample of a 29/1 (weight ratio) blend.
As is clear from FIG. 9, when the tensile test was performed, the strength and elastic modulus in the stretching direction were 148.8 MPa and 1.30 GPa, respectively. Further, the strength and elastic modulus in the direction perpendicular to the stretching were 30.7 MPa and 1.27 GPa, respectively, and excellent mechanical properties were exhibited in two directions.

(Comparative Example 1)
The mechanical properties of the unstretched film of nylon 6 / PP / PP-g-MA = 70/20/10 (weight ratio) blend were evaluated. It has a yield strength of 26.2 MPa and an elastic modulus of 0.47 Gpa. The mechanical properties of the unstretched film in the low strain region are the mechanical properties of the oriented films of Example 1 (see FIG. 3) and Example 2 (see FIG. 6). Inferior.

(Comparative Example 2)
The mechanical properties of the unstretched film of nylon 6 / PP / PP-g-MA = 70/29/1 (weight ratio) blend were evaluated. The yield strength was 26.4 MPa, the elastic modulus was 0.44 GPa, and the mechanical properties of the unstretched film in the low strain region were inferior to those of the oriented film of Example 3 (see FIG. 9).

(Comparative Example 3)
Nylon 6 / PP / PP-g-MA = 70/20/10 (weight ratio) blend was stretched at 140 ° C. in the same manner as in Example 1, and wide-angle X-ray diffraction was measured without heat treatment.
FIG. 10 is a wide-angle X-ray diffraction image of a stretched film stretched at 140 ° C., in which a is the case of nylon 6, b is the case of polypropylene, and c is nylon 6 / PP / PP−. The cases of g-MA = 70/20/10 (weight ratio) blend are shown. In both cases, the meridian (up and down direction) corresponds to the stretching direction, and the equator (left and right direction) corresponds to the stretching and vertical direction.
The wide-angle X-ray diffraction image (FIG. 10c) of the stretched film of the blend is a superposition of the wide-angle X-ray diffraction image of the nylon 6 stretched film (FIG. 10a) and the wide-angle X-ray diffraction image of the stretched PP film (FIG. 10b). In the stretched blend film, both the molecular axis of nylon 6 and the molecular axis of PP were oriented in the stretching direction.

  When a tensile test was performed, the strength and elastic modulus in the stretching direction were 218 MPa and 1.90 Gpa, respectively. The strength and elastic modulus in the vertical direction were 29.0 Mpa and 1.02 GPa, respectively, and high mechanical properties were exhibited in the stretching direction. However, the mechanical properties in the vertical direction were similar to those of the heat-treated samples of Example 1 and Example 2. It stayed at a low value.

(Comparative Example 4)
The same experiment as in Example 1 was performed using an ethylene-methacrylic acid copolymer instead of PP. That is, a stretched film of nylon 6 / ethylene-methacrylic acid copolymer blend was prepared, the ethylene methacrylic acid copolymer was melted at 120 ° C., and heat-treated at 80 ° C. to crystallize the ethylene-methacrylic acid copolymer. .
FIG. 11 is a wide-angle X-ray diffraction image, in which the meridian (vertical direction) corresponds to the stretching direction, and the equator (horizontal direction) corresponds to the stretching and vertical direction. In the figure, a is a wide-angle X-ray diffraction image of a nylon 6 / ethylene-methacrylic acid copolymer blend stretched film, and b is a film of Comparative Example 4 that has been heat-treated to crystallize a polyethylene-methacrylic acid copolymer. It is a wide-angle X-ray diffraction image.
When the wide-angle X-ray diffraction image (a) of the unheated stretched film was compared with the wide-angle X-ray diffraction image (b) of the stretched film after the heat treatment, no significant difference was observed. That is, according to Comparative Example 4, when an ethylene-methacrylic acid copolymer was used instead of PP, the crystal orientation of the ethylene-methacrylic acid copolymer was not changed by the heat treatment, and the ethylene-methacrylic acid was not changed. It was confirmed that the molecular chain axis of the acid copolymer was oriented in the stretching direction.

  The present invention can be applied to a wide range of uses as a high-strength plastic film.

2 is a wide-angle X-ray diffraction image of a film obtained by orientation crystallizing PP obtained in Example 1. FIG. The figure which shows the azimuth angle dependence of the 110 reflection of a polypropylene and the diffraction intensity of 040 reflection in the film which carried out the orientation crystallization of PP obtained in Example 1. FIG. The figure which shows the stress-strain curve of the film which oriented-crystallized PP obtained in Example 1. FIG. A wide-angle X-ray diffraction image of a film obtained by orientation crystallizing PP obtained in Example 2. The figure which shows the azimuth angle dependence of the diffraction intensity of 110 reflection of polypropylene and 040 reflection in the film which oriented-crystallized PP obtained in Example 2. FIG. The figure which shows the stress-strain curve of the film which oriented-crystallized PP obtained in Example 2. FIG. 4 is a wide-angle X-ray diffraction image of a film obtained by orientation-crystallization of polypropylene obtained in Example 3. FIG. The figure which shows the azimuth angle dependence of the diffraction intensity of 110 reflection of polypropylene and 040 reflection in the film which oriented-crystallized the polypropylene obtained in Example 3. FIG. The figure which shows the stress-strain curve of the film which obtained the oriented crystallization of the polypropylene obtained in Example 3. FIG. It is a wide-angle X-ray-diffraction image of the stretched film extended | stretched at 140 degreeC, a: Nylon, b: Polypropylene, c: Comparative example 3. FIG. Wide angle X-ray diffraction image (a) of nylon 6 / ethylene-methacrylic acid copolymer blend stretched film, and wide angle X-ray diffraction image of a film obtained by heat-treating the blend stretched film to crystallize a polyethylene-methacrylic acid copolymer (B).

Claims (5)

  A blend film containing nylon 6, isotactic polypropylene and a compatibilizing agent, and the crystal axis (b axis) in the molecular chain direction of nylon 6 and the crystal axis (c axis) in the molecular chain direction of isotactic polypropylene are different from each other. Crystal orientation film oriented in the direction.   The crystal orientation film according to claim 1, wherein the compatibilizing agent is polypropylene grafted with maleic anhydride.   The crystal orientation film according to claim 1 or 2, wherein the nylon 6 and isotactic polypropylene (PP) are contained in a weight ratio of nylon 6 / PP = 50/50 to 90/10.   The crystal orientation film according to claim 1 or 2, comprising 0.1 to 30% by weight of the compatibilizer.   Nylon 6, astactic polypropylene and a compatibilizing agent are kneaded, then formed into a sheet by hot pressing, uniaxially stretched, and then isolated at a temperature lower than the melting point of nylon 6 and higher than the melting point of isotactic polypropylene. A method for producing a crystallographically oriented film, comprising melting tactic polypropylene and then recrystallizing isotactic polypropylene in a stretched nylon 6 / isotactic polypropylene blend.