JPH08176366A - Polypropylene resin composition and oriented polypropylene film - Google Patents

Abstract

PURPOSE: To obtain a polypropylene resin composition improved in transparency and image clarity, having excellent processability without causing problems such as roughness of sheet in the case of extrusion molding of a raw sheet, cutting of sheet in drawing and unevenness of film in drawing, when the composition is formed into oriented film and obtain an oriented polypropylene film. CONSTITUTION: This polypropylene resin composition comprises a crystalline polypropylene, 0.1-1000ppm fluorine-containing polymer having >=50% degree of crystallinity and 50-4000ppm talc having 0.1-10μm average particle diameter. This oriented polypropylene film is formed of the polypropylene resin composition and obtained by at least monoaxially orienting the resin composition.

Description

Detailed Description of the Invention

[0001]

TECHNICAL FIELD The present invention relates to a polypropylene resin composition and a stretched film comprising the polypropylene resin composition. More specifically, a crystalline polypropylene containing a small amount of a fluorinated polymer and talc, the transparency and image clarity are remarkably improved, and at the time of extrusion of a raw sheet during molding of a uniaxially or biaxially stretched film. Polypropylene suitable for a stretched film having good formability without causing edge roughness of the sheet, breakage of the sheet during longitudinal stretching, deterioration of thickness accuracy due to uneven stretching of the film during horizontal stretching, and stretch tearing. The present invention relates to a resin composition and a stretched film made of the polypropylene resin composition.

[0002]

2. Description of the Related Art Polypropylene stretched films, particularly polypropylene biaxially stretched films, are widely used for packaging materials and the like because of their excellent mechanical and optical properties. The manufacturing method is generally a sequential biaxial stretching method using a tenter method. However, due to the high crystallinity of polypropylene, these polypropylene stretched films are generally inferior in transparency and image clarity to other highly transparent thermoplastic resins such as polystyrene and polyvinyl chloride.

Several proposals have been made so far in an attempt to improve the transparency and image clarity of a stretched polypropylene film. For example, by adding an organic nucleating agent such as a sorbitol derivative, an alkali metal salt of an aromatic carboxylic acid, or an aluminum salt to a polypropylene resin, in the cooling and solidifying process at the time of extrusion molding of a raw sheet during film forming, It is known that the spherulites inside the solidified raw sheet become smaller and uniform, and the transparency and image clarity of the stretched film are improved. However, these organic nucleating agents have a problem that they bleed from polypropylene during extrusion and cause roll stains, and that odor is generated during processing. Further, there is a problem that the nucleating agent bleeds even when the film or the like is stored for a long period of time. Further, in the aromatic carboxylate, there is a problem that the original performance of the additive is deteriorated or the polypropylene resin is colored by reacting with itself or its hydrolyzate with other additives. .

On the other hand, attempts have been made to improve the transparency of polypropylene by using a polymer of a branched olefin having 5 or more carbon atoms (Japanese Patent Publication No. 32430/1985). These branched olefin polymers do not cause problems such as roll fouling during film formation like the organic nucleating agent,
It is excellent in improving the transparency and image clarity of stretched films.

However, when the content of the branched olefin polymer in polypropylene exceeds 0.1 ppm,
At the time of molding a polypropylene stretched film, the raw sheet obtained by extrusion molding suffers from surface roughness, resulting in deterioration of transparency and image clarity. Further, there is a problem that wavy or saw-toothed roughness is generated at the edge portion of the original sheet, which causes a clip error in tenter stretching, and uneven stretching or tearing of the film in transverse stretching occurs.
Further, when the edge portion is roughened in a saw-tooth shape, the stretch breakage of the sheet occurs during the longitudinal stretching, which causes a problem in the formability of the stretched film.

Thus, conventionally, attempts have been made to improve the transparency and image clarity of a polypropylene stretched film by the above-mentioned method, but the stretchability of the stretched film is still unsatisfactory. That is, the object of the present invention is to have excellent transparency and image clarity without the above-mentioned drawbacks, and at the time of forming a stretched film, does not cause edge roughness of the sheet at the time of extrusion of the original sheet, and is longitudinal. It is an object of the present invention to provide a polypropylene resin composition and a polypropylene stretched film which have good moldability and do not cause stretch breakage of the sheet during stretching, uneven stretching or tearing of the film during transverse stretching.

[0007]

From these viewpoints, the present inventors have made earnest studies on a polypropylene stretched film having improved transparency, image clarity, and moldability of the stretched film. By a simple method of containing a small amount of a fluorinated polymer and talc in polypropylene, transparency and image clarity of the polypropylene stretched film is significantly improved, and the edges of the sheet during the stretched film molding are not roughened. They have found that they are excellent in moldability and have completed the present invention.

That is, the present invention is a crystalline polypropylene, a fluoropolymer having a degree of crystallinity of 50% or more 0.1 to 1
A polypropylene resin composition comprising 000 ppm and talc having an average particle size of 0.1 to 10 μm of 50 to 4000 ppm, and a polypropylene stretched film comprising the polypropylene resin composition and stretched at least uniaxially. .

Examples of the crystalline polypropylene used in the present invention include a homopolymer of propylene, a random copolymer of propylene and another α-olefin, and a mixture thereof. Examples of the α-olefin include ethylene, 1-butene, 1-pentene,
1-hexene, 1-heptene, 1-octene, 1-nonene, 1-decene, 4-methyl-1-pentene and the like can be mentioned, and the content of these α-olefins is 10 mol% or less. Are preferred for maintaining crystallinity.

Although the melt flow rate of the crystalline polypropylene used in the present invention is not particularly limited, it is usually in the range of 0.01 to 100 g / 10 min in consideration of moldability for various stretched films. What is used is, and it is preferable that it is in the range of 0.1 to 50 g / 10 min.

The crystalline polypropylene used in the present invention is crystalline and has an isotactic pentad fraction of 0.85 or more. The isotactic pentad fraction as used in the present invention means A. Zambilli et al., Macromolecules, 13 , 267.
(1980), which is a fraction in which five propylene units, which are quantified based on the attribution of peaks in a ¹³ C-NMR spectrum, continuously have the same configuration.

The molecular weight distribution (ratio (Mw / Mn) of weight average molecular weight (Mw) to number average molecular weight (Mn)) of the crystalline polypropylene used in the present invention is not particularly limited, but film molding Considering the above case, it is preferably 6 to 20 in order to increase the melt tension and improve the workability. The molecular weight distribution is a value measured by gel permeation chromatography (hereinafter also referred to as GPC) using o-dichlorobenzene as a solvent, and a calibration curve calibrated with standard polystyrene is used.

The fluorine-containing polymer used in the present invention must have a crystallinity of 50% or more. Crystallinity is 5
When it is less than 0%, the transparency-improving effect and the image-improving effect of the fluoropolymer are poor. The transparency and image clarity improving effects of the fluoropolymer in the present invention tend to be more effective as the crystallinity of the fluoropolymer is higher, and therefore the crystallinity is preferably 50% or more. And more preferably 70% or more. The crystallinity of the fluorine-containing polymer was determined by using an X-ray diffractometer JDX3500 manufactured by JEOL Ltd., using a tube voltage-tube current of 40 KV-400 mA, and using a monochromatic Cu-Kα ray with a graphite monochromator. The measurement conditions are reflection method, divergence slit 0.2mm,
Measurement is performed with a light-receiving slit 0.4 mm, a diffraction angle of 11 to 27 °, a step angle of 0.04 °, and a counting time of 1.0 second, and the peak separation of the diffraction intensity curve is performed. The diffraction angles 2θ are 16 ° and 1
The sum of the broad peak areas observed at 7.5 ° is S
_{When the} crystalline peak area observed at _A , 18 ° is S _C , it is represented by the following formula S _C / (S _C + S _A ) × 100 (%).

The particle size of the fluoropolymer is not particularly limited, but in order to obtain a film having good transparency and image clarity, the average primary particle size is preferably 2 μm or less, and more preferably 0.01 μm to 1 μm. Is preferred.

The fluorine-containing polymer which can be used in the present invention includes homopolymers of fluorine-containing monomers, copolymers of fluorine-containing monomers with each other, copolymers of fluorine-containing monomers with hydrocarbon monomers, especially α-olefins. You can use this. Specific examples of the fluoropolymer that can be used in the present invention include, for example, a tetrafluoroethylene polymer,
1-fluoroethylene polymer, 1,1-difluoroethylene polymer, trifluoroethylene polymer, 1-chloro-2,2-difluoroethylene polymer, chlorotrifluoroethylene polymer, hexafluoropropylene polymer, hexafluoro Propylene oxide polymer, tetrafluoroethylene-methyl vinyl ether copolymer, trifluoroethylene-methyl vinyl ether copolymer, tetrafluoroethylene-perfluorovinyl ether copolymer, tetrafluoroethylene-hexafluoropropylene copolymer, etc. You can

The content of the fluoropolymer used in the present invention must be in the range of 0.1 to 1000 ppm,
It is preferably 1 to 500 ppm, more preferably 10
More preferably, it is 200 ppm. When the content of the fluorinated polymer is less than 0.1 ppm, the effect of improving the transparency and image clarity is not observed. Conversely, 1000 ppm
If it exceeds, the surface of the sheet is roughened and edge roughening occurs in the extrusion process of the raw sheet, and the transparency and image clarity of the stretched film deteriorates, and there is a problem such as stretching unevenness and stretching tearing. . When a copolymer of a fluorine-containing α-olefin monomer and another α-olefin is used as the fluorine-containing polymer, the weight of the polymerization component based on the fluorine-containing α-olefin monomer needs to be within the above range. . In the present invention, ppm is based on weight.

The average particle size (primary particle size) of talc used in the present invention must be in the range of 0.1 to 10 μm, preferably 0.5 to 8.0 μm, and more preferably 1.0. More preferably, it is about 7.0 μm. If the average particle size of talc is less than 0.1 μm, talc undergoes secondary agglomeration to increase the agglomerated particle size, resulting in a decrease in transparency and fish eyes, which deteriorates the appearance of the film, which is not preferable. . On the contrary, when the average particle size exceeds 10 μm, many voids are generated in stretching the film,
It is not preferable because the transparency of the film is lowered. The method for measuring the average particle size of talc used in the present invention is not particularly limited, but a method using a Coulter counter, an electron microscope or the like is exemplified. As the talc used in the present invention, known products such as crushed products of natural products or synthetic products are used without limitation, and talc having high crystallinity and high crystallinity for polypropylene is preferred.

The content of talc in the crystalline polypropylene used in the present invention must be in the range of 50 to 4000 ppm, preferably 80 to 2000 ppm, and more preferably 100 to 1000 ppm. If the talc content is less than 50 ppm,
The sufficient nucleation effect of talc cannot be obtained, and the edge of the raw sheet is roughened. On the other hand, when it exceeds 4000 ppm, the transparency of the film is lowered and the appearance is deteriorated due to the generation of voids.

The method of incorporating the fluorine-containing polymer and talc into the crystalline polypropylene is not particularly limited, and various mixing methods can be adopted. Specifically, a fluorinated polymer and talc are simultaneously added to the crystalline polypropylene, a single screw extruder, a screw extrusion kneader such as a twin screw extruder, a Banbury mixer, a continuous mixer,
Examples thereof include a method of mixing using a mixing roll and the like, a method of separately mixing the fluoropolymer and talc with crystalline polypropylene, and then mixing both.

Further, after obtaining a crystalline polypropylene composition containing a high concentration of a fluoropolymer by the above-mentioned method, the composition is used as a masterbatch with another crystalline polypropylene, and a dilution ratio of 2 is obtained. The desired fluoropolymer content can be obtained by diluting in the range of 1000 times (diluting the fluoropolymer content to 0.5 to 0.001 times). Dilution ratio of masterbatch is generally 2
Although it is about 0 times, in the present invention, the transparency and image clarity of the stretched film can be sufficiently improved even at a considerably large dilution ratio depending on the masterbatch concentration.

The thickness of the polypropylene stretched film of the present invention is not particularly limited, but it is usually 3 to 150 μm in the case of a biaxially stretched film and 10 to 25 in the case of a uniaxially stretched film.
It is preferably 4 μm. The polypropylene stretched film of the present invention is stretched in at least a uniaxial direction. Of course, it may be biaxially stretched. Although the stretching ratio is not particularly limited, it is generally 4 to 10 times in the uniaxial direction, and in the case of biaxial stretching, it is generally stretched in the range of 4 to 15 times in the direction perpendicular thereto. Is.

In the polypropylene stretched film of the present invention, if necessary, an antioxidant, a chlorine scavenger, a heat stabilizer, an antistatic agent, an antifogging agent, an ultraviolet absorber, a lubricant, an antiblocking agent, a pigment, etc. Additives such as resins and fillers may be added as long as the effects are not impaired.

If necessary, one or both surfaces of the polypropylene stretched film of the present invention may be subjected to surface treatment such as corona discharge treatment. Further, for the purpose of imparting a function such as heat sealability, a layer made of another resin having a lower melting point than the crystalline polypropylene of the present invention may be laminated on one side or both sides. The method for laminating other resins is not particularly limited, but a coextrusion method, a laminating method, etc. are preferable.

As the method for producing the polypropylene stretched film of the present invention, known methods can be adopted without any limitation. For example, as a method for producing a stretched film by a sequential biaxial stretching method by a tenter method, the polypropylene resin composition is molded into a sheet or film by a T-die method, an inflation method or the like, and then supplied to a longitudinal stretching device, Longitudinal stretching 4 to 10 times at a heating roll temperature of 120 to 170 ° C., and then using a tenter, a tenter temperature of 13
A method of transversely stretching 4 to 15 times at 0 to 180 ° C. is preferable, and a method of heat treatment at 80 to 180 ° C. while allowing a relaxation of 0 to 25% in the transverse direction as needed can be mentioned. Of course, the stretching may be performed again after these stretchings, and in the longitudinal stretching, stretching methods such as multi-stage stretching and rolling can be combined. Also, a stretched film can be obtained by stretching only uniaxially.

[0025]

According to the present invention, the transparency and image clarity of a polypropylene stretched film are improved, and the surface of the sheet is not roughened or the edges are roughened in the process of forming a raw sheet when molding the stretched film. It is possible to obtain a polypropylene stretched film having excellent processability without problems such as breakage of stretching of the sheet, deterioration of thickness accuracy due to uneven stretching of the film, and breakage of stretching.

In the polypropylene resin composition and the polypropylene stretched film of the present invention, it is not clear why the inclusion of a small amount of talc improves the moldability of the crystalline polypropylene containing the fluoropolymer into the stretched film. However, the present inventors consider as follows from the following analysis results.

When the orientation mode of the polypropylene crystals of the crystalline polypropylene raw sheet containing the fluoropolymer is analyzed in detail by the wide-angle X-ray diffraction method, the growth axis of the polypropylene crystals, that is, the a * axis is perpendicular to the sheet surface ( It was found that the orientation was strong in the sheet thickness direction). That is, when the original sheet was rotated at high speed about an axis perpendicular to the sheet surface and X-rays were made incident from a direction perpendicular to the sheet surface to measure the diffraction intensity, 040 reflection from the polypropylene crystal (2θ = 17 .1 °) is strongly observed. The peak intensity ratio I (040) / I (111) of 040 reflection and 111 reflection (2θ = 21.4 °) was calculated by performing peak separation of the measured X-ray diffraction profile and found to be 2 to 5. The peak intensity ratio increases with an increase in the content of. Z. Mencik (Z. Menc
ik, Journal of Macromolecule
ler Science, Physics B6 , 1
01 (1972)), when the polypropylene crystals are perfectly randomly oriented, the peak intensity ratio is I (0
40) / I (111) = 1.52. From this, it is understood that in the crystalline polypropylene raw sheet containing the fluoropolymer, the (040) plane of the polypropylene crystal is perpendicular to the sheet surface, that is, the b axis of the crystal is strongly oriented parallel to the sheet surface. . Also, since the crystal c-axis (polypropylene molecular chain axis) is oriented in the extrusion direction (parallel to the sheet surface), the a * axis, which is the crystal growth direction, is oriented perpendicular to the sheet surface (sheet thickness direction). It turned out.

From the above, when the fluorine-containing polymer is contained in the crystalline polypropylene, when the raw sheet is formed,
During cooling and solidification of the molten resin, polypropylene crystals grow in the thickness direction of the sheet from the chill roll side, and at this time, the shrinkage ratio between the chill roll side and the opposite surface side, the difference in internal stress, etc. become large. It is considered that the adhesion between the sheet and the cooling roll deteriorates, uneven cooling and roll separation occur, the surface of the original sheet is roughened, and the edge state deteriorates.

On the other hand, when talc known as an inorganic nucleating agent for polypropylene is contained, on the contrary, 040
The peak intensity ratio I (040) / I (111) between reflection and 111 reflection is 1
Below, the peak intensity ratio decreases with increasing talc content. It can be seen that in the crystalline polypropylene original sheet containing talc, the (040) plane of the polypropylene crystal is parallel to the sheet surface, that is, the b axis of the crystal is strongly oriented perpendicular to the sheet surface. Therefore, it was found that the a * axis, which is the crystal growth direction, is oriented in the direction parallel to the sheet surface (in the sheet surface). Talc is also known to have a nucleating effect on polypropylene, but in the case of talc-containing crystalline polypropylene, even if a nucleating effect such as a crystallization temperature rise similar to that of a fluoropolymer is observed, Roughness does not occur at the edge of the original sheet. This is
In the talc-containing system, polypropylene crystals grow in the plane of the sheet when the molten resin is cooled and solidified when forming the original sheet, so shrinkage and changes in stress in the thickness direction are small, so the original sheet and the cooling roll It is considered that the adhesion between the two becomes good and the condition of the edge portion does not deteriorate.

Therefore, when the fluorine-containing polymer and talc are contained in the crystalline polypropylene, it is possible to control the orientation of the polypropylene crystals in the sheet, that is, the crystal growth direction, by the content and the ratio of both. all right.

Based on the above analysis results, the present inventors have made talc contained in crystalline polypropylene containing a fluoropolymer so that polypropylene crystals grow in the sheet thickness direction when forming a raw sheet. It has been found that the suppression suppresses the edge roughness of the original sheet and enables stable sheet formation. Furthermore, it is believed that the spherulites inside the raw sheet are made smaller and uniform by the nucleating effect of both the fluoropolymer and talc, and the transparency and image clarity of the obtained stretched film are further improved.

[0032]

EXAMPLES In order to describe the present invention more specifically, examples and comparative examples will be described below, but the present invention is not limited to these examples. The polypropylene stretched films obtained in the following examples and comparative examples were evaluated by the following methods.

(1) Haze Measured according to JIS K 6714.

(2) Image value An optical comb of 0.1 was used using an image measuring device manufactured by Suga Test Instruments Co., Ltd.
Using 25 mm, the comb direction was made parallel to the transverse stretching method of the biaxially stretched film, and the image value was measured.

Example 1 (Granulation) Homopolypropylene powder 1 shown in Table 1
A tetrafluoroethylene polymer (Asahi ICI Co. Made, product name "Fluon Lubricant L-171J", crystallinity 78.7%,
After adding 100 ppm of an average primary particle diameter of 0.2 μm) and 300 ppm of talc having an average particle diameter of 4.2 μm and mixing with a Henschel mixer for 5 minutes, a screw diameter of 65 mmφ
Was extruded at 230 ° C. to pelletize the raw material pellets.

(Molding of Biaxially Stretched Film) A molding experiment of a biaxially stretched film was carried out by the following method using the obtained raw material pellets. Raw material pellets, screw diameter 90m
An mφ T die sheet extruder was used to extrude at 280 ° C., and a sheet having a thickness of 2 mm was formed with a cooling roll at 30 ° C. Next, this raw sheet is longitudinally stretched 4.6 times in the longitudinal direction at 150 ° C. by using a tenter type sequential biaxial stretching device, and subsequently in the tenter at 165 ° C. in the transverse direction at a mechanical magnification of 10 times. After stretching, the film was relaxed by 8% and heat-treated to form a 50 μm-thick biaxially stretched polypropylene film at a speed of 16 m / min.

The state of edge roughness of the original sheet during film formation was visually evaluated according to the following criteria.

⊚: When the edge portion of the sheet is in close contact with the cooling roll and is linear and extremely good ○: A little away from the cooling roll but no problem in film forming Δ: When wavy and rough ×: In saw blade shape In the case of rough surface In addition, the influence of uneven drawing on the thickness accuracy is the infrared thickness measuring machine W made by Yokogawa Electric Co., Ltd. installed between the tenter and the winder.
The film thickness pattern measured using EB GAGE was evaluated according to the following criteria.

⊚: less than ± 1 μm ○: ± 1 μm or more and less than 1.5 μm Δ: ± 1.5 μm or more and less than 2 μm ×: ± 2 μm or more Further, continuous operation was performed for 5 hours, and the stretch cut in the longitudinal stretching of the sheet, the tenter The number of stretch breakages of the film was evaluated. Also, the obtained film is
After the lapse of time, the haze and the mapping value were measured. The results are shown in Table 1.
It was shown to.

Examples 2-5 Using the same homopolypropylene and talc as in Example 1,
Example 1 was repeated except that the amount of the tetrafluoroethylene polymer of Example 1 was changed as shown in Table 1. The results are shown in Table 1.

Examples 6 to 8 The same homopolypropylene as in Example 1 was used, and Example 1 was used.
Table 1 shows the tetrafluoroethylene polymer and talc used in
The same procedure as in Example 1 was carried out except that the compounding amount was changed. The results are shown in Table 1.

Examples 9 and 10 Example 1 except that talc having an average particle size of 1.2 μm was used (Example 9) and talc having an average particle size of 6.1 μm was used (Example 10). The results are shown in Table 1.

Comparative Example 1 The same procedure as in Example 1 was carried out without adding the tetrafluoroethylene polymer and talc, and the results are shown in Table 1.

Comparative Example 2 The same procedure as in Example 1 was carried out without adding the tetrafluoroethylene polymer, and the results are shown in Table 1.

Comparative Example 3 The same procedure as in Example 1 was carried out without adding talc, and the results are shown in Table 1.

Comparative Examples 4 and 5 Using the same homopolypropylene and talc as in Example 1,
The tetrafluoroethylene polymer used in Example 1 is shown in Table 1.
The same procedure as in Example 1 was carried out except that the compounding amount was changed. The results are shown in Table 1.

Comparative Examples 6 and 7 The same homopolypropylene as in Example 1 was used, and Example 1 was used.
Table 1 shows the tetrafluoroethylene polymer and talc used in
The same procedure as in Example 1 was carried out except that the compounding amount was changed. The results are shown in Table 1.

Example 11 Example 1 except that a propylene-ethylene random copolymer powder having a melt flow rate of 1.8 g / 10 min and an ethylene content of 0.5 mol% was used, and the tetrafluoroethylene polymer was 10 ppm. The results are shown in Table 1.

Examples 12, 13 Melt flow rate 1.2 g / 10 min, powder of propylene-ethylene random copolymer having ethylene content of 1.0 mol% was used (Example 12), and melt flow rate 2. Propylene-butene-1 with 0 g / 10 min and a butene-1 component content of 0.5 mol%
A random copolymer powder was used (Example 1
Except for the point 3), the same procedure as in Example 11 was performed, and the results are shown in Table 1.

Examples 14 and 15 Using the same crystalline polypropylene as in Example 11, the content of the tetrafluoroethylene polymer was 100 ppm, the average particle size of talc was 2.0 μm, and the content was 500 ppm (Examples). 14), the content of the tetrafluoroethylene polymer is 1 ppm, and the average particle diameter of talc is 2.
Example 1 was repeated except that the content was 0 μm and the content was 100 ppm (Example 15), and the results are shown in Table 1.

Comparative Example 8 The crystalline polypropylene of Example 11 was subjected to the same procedure as in Example 1 without adding the tetrafluoroethylene polymer and talc, and the results are shown in Table 1.

Comparative Examples 9 and 10 The content of tetrafluoroethylene polymer was 0.01 pp.
m (Comparative Example 9), and the tetrafluoroethylene polymer content was 5000 ppm (Comparative Example 1).
The same procedure as in Example 15 was carried out except that 0), and the results are shown in Table 1.

Comparative Examples 11 and 12 Talc having an average particle size of 13.6 μm was used (Comparative Example 1
The same procedure as in Example 11 was performed except that 1) and talc having an average particle size of 0.08 μm was used (Comparative Example 12), and the results are shown in Table 1.

Example 16 A polypropylene composition prepared in the same manner as in Example 1 except that the tetrafluoroethylene polymer was 2000 ppm and the talc was 6000 ppm was used. The melt flow rate used in Example 11 was 1.8 g / 10 min. Was diluted 20 times with a powder of propylene-ethylene random copolymer having an ethylene content of 0.5 mol%, and the results are shown in Table 1.

[0055]

[Table 1]

Example 17 Using homopolypropylene and talc shown in Table 2, a tetrafluoroethylene polymer (Asahi ICI, trade name "Fluon Lubricant L-173", crystallinity 87.6) was used.
%, Average primary particle diameter 0.2 μm) and the blending amount shown in Table 2 was used, and the same procedure as in Example 1 was performed. The results are shown in Table 2.

Examples 18 and 19 Using the homopolypropylene and talc shown in Table 2, the tetrafluoroethylene polymer used in Example 17 is shown in Table 2.
The same procedure as in Example 1 was carried out except that the compounding amount was changed. The results are shown in Table 2.

Comparative Examples 13 and 14 The procedure of Example 1 was repeated except that the homopolypropylene and talc shown in Table 2 were used and the amount of the tetrafluoroethylene polymer obtained in Example 17 was changed to that shown in Table 2. The results are shown in Table 2.

Examples 20 and 21 The same procedure as in Example 19 was carried out except that the same homopolypropylene and tetrafluoroethylene polymer as in Example 19 were used and the talc used in Example 19 was changed to the blending amount shown in Table 2. . The results are shown in Table 2.

Example 22 The same procedure as in Example 17 was carried out except that a difluoroethylene homopolymer (crystallinity: 71.2%, average primary particle size: 0.1 μm) was used as the fluorine-containing polymer. The results are shown in Table 2.

Example 23 Tetrafluoroethylene-perfluoroalkylvinylether copolymer (crystallinity 7
The same procedure as in Example 17 was performed except that 4.0% was used and the average primary particle size was 0.3 μm. The results are shown in Table 2.

[0062]

[Table 2]

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Claims (2)

[Claims] 1. A crystalline polypropylene, a fluoropolymer having a crystallinity of 50% or more, 0.1 to 1000 ppm, and
Talc with an average particle size of 0.1 to 10 μm 50 to 4000 p
A polypropylene resin composition comprising pm. 2. A polypropylene stretched film comprising the polypropylene resin composition according to claim 1 and stretched at least uniaxially.