WO2024070972A1

WO2024070972A1 - Biaxially oriented polypropylene film, package for food, and food package

Info

Publication number: WO2024070972A1
Application number: PCT/JP2023/034574
Authority: WO
Inventors: 拓也田村; 裕之若木; 琢巳正本; 正之櫻井
Original assignee: 三井化学東セロ株式会社
Priority date: 2022-09-28
Filing date: 2023-09-22
Publication date: 2024-04-04

Abstract

A biaxially oriented polypropylene film (100) is provided with a biaxially oriented film layer (101) containing a propylene polymer, and has a crystal ratio of at least 38% at 165° C or lower, as determined by differential scanning calorimetry.

Description

Biaxially oriented polypropylene film, food packaging and food packaging

The present invention relates to a biaxially oriented polypropylene film, a food package, and a food package.

Biaxially oriented polypropylene film (hereinafter referred to as OPP film) has an excellent balance of performance, including processability, water vapor barrier properties, transparency, mechanical strength, and rigidity, and is used, for example, as a packaging film for packaging food.

Technologies relating to food packaging films using such OPP films include those described in Patent Document 1 (JP Patent Publication No. 2008-73926) and Patent Document 2 (JP Patent Publication No. 2004-82499).

Patent Document 1 describes a biaxially oriented multilayer polypropylene film comprising a biaxially oriented film made of a propylene polymer composition containing 75 to 90 mass % of a propylene homopolymer (A) and 25 to 10 mass % of a tackifier (D), the biaxially oriented film having a layer made of a propylene-α-olefin random copolymer (C) having a melting point in the range of 125 to 145° C., via a layer made of a propylene polymer (B) having a melting point of 155° C. or higher, on one side thereof, and a layer made of a propylene polymer (E) on the other side thereof.
Patent Document 1 describes that the biaxially oriented multilayer polypropylene film can suppress the seepage of petroleum resins and the like onto the film surface, and has excellent lamination strength and moisture resistance.

Patent Document 2 describes a multilayer resin film having a biaxially oriented polypropylene resin layer containing 10 to 40% by mass of a highly crystallized resin and 6 to 15% by mass of a petroleum resin, and further having a polyvinyl alcohol resin layer via an adhesive layer on at least one surface of the biaxially oriented polypropylene resin layer, the multilayer resin film being characterized in that the oxygen transmission rate at a relative humidity of 85% RH and a temperature of 23°C is 600 mL/ ^m2 day MPa or less, and the water vapor transmission rate at a relative humidity of 90% RH and a temperature of 40°C is 3.5 g/ ^m2 day 20 μm or less.
Patent Document 2 describes that the multilayer resin film has excellent oxygen gas barrier properties and moisture resistance.

JP 2008-73926 A JP 2004-82499 A

In recent years, from the viewpoint of environmental issues, there has been a demand for mono-material packaging materials.
However, conventional biaxially oriented polypropylene films have sometimes been insufficient in thermal dimensional stability from the viewpoint of suppressing thermal wrinkles at the sealed portion during bag making and suppressing thermal expansion during vapor deposition and coating processing. That is, further improvement in thermal dimensional stability is required for biaxially oriented polypropylene films from the viewpoint of suppressing thermal wrinkles at the sealed portion during bag making and suppressing thermal expansion during vapor deposition and coating processing.

The present invention was made in consideration of the above circumstances, and provides a biaxially oriented polypropylene film, food packaging material, and food packaging material with improved thermal dimensional stability.

The inventors conducted extensive research to solve the above problems. As a result, they discovered that the thermal dimensional stability of biaxially oriented polypropylene film can be improved by adjusting the crystallinity ratio at 165°C or less to a specific range, which led to the present invention.

In other words, the present invention provides the biaxially oriented polypropylene film, food packaging material, and food packaging material shown below.

[1]
A biaxially stretched film layer containing a propylene-based polymer is provided,
A biaxially oriented polypropylene film having a crystallinity of 38% or more at 165°C or less as determined by differential scanning calorimetry.
[2]
The biaxially oriented polypropylene film according to [1], wherein the main melting point of the biaxially oriented polypropylene film is 165° C. or higher and 180° C. or lower, as determined by differential scanning calorimetry.
[3]
The biaxially oriented polypropylene film according to [1] or [2], wherein the heat of fusion (ΔH) of the entire biaxially oriented polypropylene film, as determined by differential scanning calorimetry, is 110 J/g or more and 150 J/g or less.
[4]
The biaxially oriented polypropylene film according to any one of [1] to [3] above, wherein the heat of fusion (ΔH) of the biaxially oriented polypropylene film at 165° C. or less is 40 J/g or more, as determined by differential scanning calorimetry.
[5]
The biaxially oriented polypropylene film according to any one of [1] to [4], wherein the amount of crystallinity at 165 ° C. or less of the biaxially oriented polypropylene film is 20% or more as determined by differential scanning calorimetry.
[6]
The biaxially oriented polypropylene film according to any one of [1] to [5], wherein the amount of structural units derived from α-olefins other than propylene contained in the biaxially oriented polypropylene film is 0.05 mol% or more when the total amount of structural units derived from monomers contained in the biaxially oriented polypropylene film is taken as 100 mol%.
[7]
The biaxially oriented polypropylene film according to any one of [1] to [6], wherein the amount of structural units derived from α-olefins other than propylene contained in the biaxially oriented polypropylene film is 0.05 mol% or more and 50.0 mol% or less, when the total amount of structural units derived from monomers contained in the biaxially oriented polypropylene film is taken as 100 mol%.
[8]
The biaxially oriented polypropylene film according to [6] or [7], wherein the α-olefin other than propylene comprises one or two selected from the group consisting of ethylene and 1-butene.
[9]
The biaxially oriented polypropylene film according to any one of [6] to [8], wherein the amount of structural units derived from the α-olefin other than propylene contained in the biaxially oriented polypropylene film is 0.1 mol% or more and 15.0 mol% or less, when the total amount of structural units derived from monomers contained in the biaxially oriented polypropylene film is taken as 100 mol%.
[10]
The biaxially stretched polypropylene film according to any one of [1] to [9], wherein the crystal long period in the TD direction determined by small angle X-ray scattering (SAXS) measurement is 28.0 nm or less.
[11]
The biaxially oriented polypropylene film according to any one of [1] to [10] above, wherein the amorphous thickness in the TD direction determined by SAXS measurement is 15.5 nm or less.
[12]
The biaxially oriented polypropylene film according to any one of [1] to [11], wherein the crystal thickness in the TD direction determined by SAXS measurement is 13.5 nm or less.
[13]
The biaxially stretched polypropylene film according to any one of [1] to [12], which expands in the TD direction when heat-treated at 120 ° C. for 15 minutes in accordance with JIS C2151:2019.
[14]
The biaxially stretched polypropylene film according to any one of [1] to [13], wherein when heat-treated at 120 ° C. for 15 minutes in accordance with JIS C2151:2019, the biaxially stretched polypropylene film expands in the TD direction and shrinks in the MD direction.
[15]
[15] The biaxially stretched polypropylene film according to any one of [1] to [14], wherein the thermal expansion coefficient in the TD direction when heat-treated at 120 ° C. for 15 minutes in accordance with JIS C2151:2019 is 0.1% or more and 2.0% or less.
[16]
The biaxially stretched polypropylene film according to any one of [1] to [15], having a heat shrinkage rate in the MD direction of 5.0% or less when heat-treated at 120 ° C. for 15 minutes in accordance with JIS C2151:2019.
[17]
The biaxially stretched polypropylene film according to any one of [1] to [16], having a heat shrinkage rate in the TD direction of 8.5% or less when heat-treated at 150 ° C. for 15 minutes in accordance with JIS C2151:2019.
[18]
The biaxially stretched polypropylene film according to any one of [1] to [17], having a heat shrinkage rate in the MD direction of 8.0% or less when heat-treated at 150 ° C. for 15 minutes in accordance with JIS C2151:2019.
[19]
The biaxially stretched polypropylene film according to any one of [1] to [18], wherein when the heat shrinkage in the TD direction and the heat shrinkage in the MD direction are X _TD [%] and X _MD [%], respectively, when heat-treated at 150° C. for 15 minutes in accordance with JIS C2151:2019, X _TD +X _MD is less than 7.0%.
[20]
The biaxially oriented polypropylene film according to any one of [1] to [19], wherein the heat fusion strength when the biaxially oriented polypropylene films are heat-sealed to each other at 200°C is 4.0 N/15 mm or less.
[21]
The biaxially oriented polypropylene film according to any one of [1] to [20] above, wherein the heat fusion strength when the biaxially oriented polypropylene films are heat-sealed to each other at 170°C is 1.0 N/15 mm or less.
[22]
The biaxially oriented polypropylene film according to any one of [1] to [21], further comprising a surface resin layer on at least one surface of the biaxially oriented film layer.
[23]
The biaxially oriented polypropylene film according to [22], wherein the surface resin layer contains homopolypropylene (A).
[24]
The content of the homopolypropylene (A) in the surface resin layer is 75% by mass or more and 100% by mass or less, when the entire surface resin layer is 100% by mass. The biaxially oriented polypropylene film according to [23].
[25]
The biaxially oriented polypropylene film according to any one of [22] to [24], wherein the thickness of the surface resin layer is 0.1 μm or more and 10.0 μm or less.
[26]
The biaxially oriented polypropylene film according to any one of [1] to [25], wherein the biaxially oriented film layer has a thickness of 5 μm or more and 100 μm or less.
[27]
The biaxially oriented polypropylene film according to any one of [1] to [26], wherein the sum (T1 + T2) of the tensile modulus _T1 in the MD direction and the tensile modulus T2 in the TD direction of the biaxially oriented polypropylene film, measured in accordance with JIS _K7127 (1999) using a tensile tester under conditions of a measurement temperature of 23± ₂ °C, 50±5 _% RH, and a tensile speed of 5 mm/min, is 3000 MPa or more and 10000 MPa or less.
[28]
The biaxially oriented polypropylene film according to any one of [1] to [27] above, which is a food packaging film.
[29]
A food packaging material using the biaxially oriented polypropylene film according to any one of [1] to [28].
[30]
The food packaging material according to [29] above,
and a food product within the food package.

The present invention provides a biaxially oriented polypropylene film, food packaging material, and food packaging material with improved thermal dimensional stability.

FIG. 1 is a cross-sectional view showing a schematic example of the structure of a biaxially oriented polypropylene film according to the present embodiment. FIG. 1 is a cross-sectional view showing a schematic example of the structure of a biaxially oriented polypropylene film according to the present embodiment. FIG. 1 is a cross-sectional view showing a schematic example of the structure of a biaxially oriented polypropylene film according to the present embodiment.

Below, an embodiment of the present invention will be described with reference to the drawings. Note that the drawings are schematic and do not correspond to the actual dimensional ratios. Note that "~" between numbers in the text indicates "above" to "below" unless otherwise specified.

<Biaxially oriented polypropylene film>
1 to 3 are cross-sectional views each showing a schematic example of the structure of a biaxially oriented polypropylene film 100 according to the present embodiment.
The biaxially oriented polypropylene film 100 of this embodiment includes a biaxially oriented film layer 101 containing a propylene-based polymer, and has a crystal ratio at 165° C. or less of 38% or more as determined by differential scanning calorimetry.

As described above, further improvement in the thermal dimensional stability of biaxially oriented polypropylene films is required from the viewpoint of suppressing thermal wrinkles in the sealed portions during bag making and from the viewpoint of suppressing thermal elongation during vapor deposition and coating processes.
Here, the inventors have found that the amount of crystalline components at 165° C. or less affects the thermal dimensional stability. As a result of further investigation based on the above findings, the inventors have found that the thermal dimensional stability of the biaxially oriented polypropylene film 100 can be improved by making the crystalline ratio at 165° C. or less 38% or more, and have arrived at the present invention.
That is, according to the biaxially oriented polypropylene film 100 of the present embodiment, the thermal dimensional stability can be improved.
In addition, since the biaxially oriented polypropylene film 100 of this embodiment has improved thermal dimensional stability, it is possible to suppress thermal wrinkles in the sealed portions during bag making, thereby improving bag making properties.

The crystal ratio of the biaxially oriented polypropylene film 100 at 165°C or less, as determined by differential scanning calorimetry, is 38% or more, but from the viewpoint of further improving the thermal dimensional stability of the biaxially oriented polypropylene film 100, it is preferably 39% or more, more preferably 40% or more, even more preferably 41% or more, even more preferably 42% or more, and even more preferably 43% or more, and from the viewpoint of further improving the performance balance of the formability and thermal dimensional stability of the biaxially oriented polypropylene film 100, it is preferably 70% or less, more preferably 65% or less, even more preferably 60% or less, even more preferably 55% or less, and even more preferably 50% or less.
The crystal ratio of the biaxially oriented polypropylene film 100 at 165° C. or less can be measured by the method described in the examples.

The main melting point of the biaxially oriented polypropylene film 100, as determined by differential scanning calorimetry, is preferably 165°C or higher, more preferably 168°C or higher, and even more preferably 170°C or higher, from the viewpoint of further improving the thermal dimensional stability of the biaxially oriented polypropylene film 100, and is preferably 180°C or lower, more preferably 178°C or lower, even more preferably 175°C or lower, and even more preferably 173°C or lower, from the viewpoint of further improving the performance balance of the formability and thermal dimensional stability of the biaxially oriented polypropylene film 100.
The main melting point of the biaxially stretched polypropylene film 100 can be measured by the method described in the Examples. Here, in this specification, the peak temperature of the maximum melting peak in the DSC curve is defined as the main melting point.

The heat of fusion (ΔH) of the entire biaxially oriented polypropylene film 100, as determined by differential scanning calorimetry, is preferably 100 J/g or more, more preferably 105 J/g or more, even more preferably 110 J/g or more, even more preferably 113 J/g or more, even more preferably 115 J/g or more, and even more preferably 117 J/g or more, from the viewpoint of further improving the thermal dimensional stability of the biaxially oriented polypropylene film 100, and is preferably 150 J/g or less, more preferably 140 J/g or less, even more preferably 130 J/g or less, and even more preferably 128 J/g or less, from the viewpoint of further improving the performance balance of the formability and thermal dimensional stability of the biaxially oriented polypropylene film 100.
The heat of fusion (ΔH) of the entire biaxially stretched polypropylene film 100 can be measured by the method described in the Examples. Herein, when multiple melting peaks appear in the DSC curve, the total area of the multiple melting peaks is defined as the heat of fusion (ΔH).

The heat of fusion (ΔH) of the biaxially oriented polypropylene film 100 at 165° C. or less, as determined by differential scanning calorimetry, is preferably 40 J/g or more, more preferably 42 J/g or more, even more preferably 43 J/g or more, even more preferably 45 J/g or more, even more preferably 48 J/g or more, and even more preferably 50 J/g or more, from the viewpoint of further improving the thermal dimensional stability of the biaxially oriented polypropylene film 100, and is preferably 90 J/g or less, more preferably 85 J/g or less, even more preferably 80 J/g or less, even more preferably 75 J/g or less, even more preferably 70 J/g or less, even more preferably 65 J/g or less, and even more preferably 60 J/g or less, from the viewpoint of further improving the performance balance of the formability and thermal dimensional stability of the biaxially oriented polypropylene film 100.
The heat of fusion (ΔH) of the biaxially oriented polypropylene film 100 at 165° C. or less can be measured by the method described in the examples.

The crystallinity of the biaxially oriented polypropylene film 100, as determined by differential scanning calorimetry, is preferably 40% or more, more preferably 45% or more, even more preferably 50% or more, even more preferably 53% or more, and even more preferably 55% or more, from the viewpoint of further improving the thermal dimensional stability of the biaxially oriented polypropylene film 100, and is preferably 80% or less, more preferably 75% or less, even more preferably 70% or less, even more preferably 65% or less, even more preferably 62% or less, and even more preferably 60% or less, from the viewpoint of further improving the performance balance of the formability and thermal dimensional stability of the biaxially oriented polypropylene film 100.
The crystallinity of the biaxially oriented polypropylene film 100 can be measured by the method described in the Examples.

The crystal content of the biaxially oriented polypropylene film 100 at 165°C or less, as determined by differential scanning calorimetry, is preferably 20% or more, more preferably 22% or more, even more preferably 23% or more, and even more preferably 24% or more, from the viewpoint of further improving the thermal dimensional stability of the biaxially oriented polypropylene film 100, and is preferably 40% or less, more preferably 38% or less, even more preferably 36% or less, preferably 35% or less, and even more preferably 30% or less, from the viewpoint of further improving the performance balance of the formability and thermal dimensional stability of the biaxially oriented polypropylene film 100.
The amount of crystallinity of the biaxially oriented polypropylene film 100 at 165° C. or less can be measured by the method described in the examples.

The above-mentioned characteristics of the biaxially oriented polypropylene film 100, which are determined by differential scanning calorimetry, can be adjusted, for example, by adjusting the type and content of the propylene-based polymer contained in the biaxially oriented film layer 101, the thickness and stretching ratio of the biaxially oriented film layer 101, the constituent material and thickness of the surface resin layer 103, etc.

The crystal long period _S2 in the TD direction of the biaxially oriented polypropylene film 100 determined by small angle X-ray scattering (SAXS) measurement is preferably 28.0 nm or less from the viewpoint of further improving the thermal dimensional stability of the biaxially oriented polypropylene film 100.
As described above, further improvement in the thermal dimensional stability of biaxially oriented polypropylene films is required from the viewpoint of suppressing thermal wrinkles in the sealed portions during bag making and from the viewpoint of suppressing thermal elongation during vapor deposition and coating processes.
Here, according to the study by the present inventors, it was found that the thermal dimensional stability of the biaxially stretched polypropylene film 100 can be improved by setting the crystal long period _S2 in the TD direction determined by SAXS measurement to 28.0 nm or less.
That is, according to the biaxially stretched polypropylene film 100 of this embodiment, in which the crystal long period _S2 in the TD direction determined by SAXS measurement is 28.0 nm or less, the thermal dimensional stability can be further improved.
In addition, since such a biaxially oriented polypropylene film 100 has improved thermal dimensional stability, it is possible to suppress thermal wrinkles in the sealed portions during bag making, thereby further improving bag making properties.

The crystal long period _S2 in the TD direction of the biaxially oriented polypropylene film 100 determined by SAXS measurement is preferably 28.0 nm or less, but from the viewpoint of further improving the thermal dimensional stability of the biaxially oriented polypropylene film 100, it is more preferably 27.8 nm or less, even more preferably 27.6 nm or less, even more preferably 27.0 nm or less, even more preferably 25.0 nm or less, even more preferably 23.0 nm or less, even more preferably 20.0 nm or less, even more preferably 18.0 nm or less, and even more preferably 15.0 nm or less, and from the viewpoint of further improving the performance balance of the transparency and water vapor barrier property of the biaxially oriented polypropylene film 100, it is preferably 5.0 nm or more, more preferably 8.0 nm or more, even more preferably 10.0 nm or more, even more preferably 12.0 nm or more, even more preferably 15.0 nm or more, even more preferably 18.0 nm or more, even more preferably 20.0 nm or more, even more preferably 23.0 nm or more, even more preferably 25.0 nm or more, and even more preferably 27.0 nm or more.

In addition, the crystal long period _S1 in the MD direction of the biaxially oriented polypropylene film 100 determined by SAXS measurement is, from the viewpoint of further improving the thermal dimensional stability of the biaxially oriented polypropylene film 100, preferably 16.5 nm or less, more preferably 16.0 nm or less, even more preferably 15.8 nm or less, and even more preferably 15.5 nm or less, and from the viewpoint of further improving the performance balance of the transparency and water vapor barrier property of the biaxially oriented polypropylene film 100, is preferably 5.0 nm or more, more preferably 8.0 nm or more, even more preferably 10.0 nm or more, even more preferably 12.0 nm or more, and even more preferably 14.0 nm or more.

The sum of the crystal long period _S1 in the MD direction and the crystal long period _S2 in the TD direction of the biaxially oriented polypropylene film 100 obtained by SAXS measurement ( _S1 + _S2 ) is preferably 44.5 nm or less, more preferably 44.0 nm or less, even more preferably 43.5 nm or less, even more preferably 43.0 nm or less, even more preferably 40.0 nm or less, even more preferably 35.0 nm or less, even more preferably 32.0 nm or less, even more preferably 30.0 nm or less, and even more preferably 28.0 nm or less, from the viewpoint of further improving the performance balance of the transparency and water vapor barrier property of the biaxially oriented polypropylene film 100, is preferably 15.0 nm or more, more preferably 20.0 nm or more, even more preferably 25.0 nm or more, even more preferably 28.0 nm or more, even more preferably 30.0 nm or more, even more preferably 32.0 nm or more, even more preferably 35.0 nm or more, even more preferably 38.0 nm or more, even more preferably 40.0 nm or more, and even more preferably 42.0 nm or more.
The crystalline long period _S1 in the MD direction and the crystalline long period _S2 in the TD direction of the biaxially oriented polypropylene film 100, which are obtained by SAXS measurement, can be measured by the method described in the Examples.

The amorphous thickness _S4 in the TD direction of the biaxially oriented polypropylene film 100, as determined by SAXS measurement, is preferably 15.5 nm or less, more preferably 15.2 nm or less, even more preferably 15.0 nm or less, even more preferably 14.5 nm or less, even more preferably 13.0 nm or less, even more preferably 11.0 nm or less, even more preferably 10.0 nm or less, and even more preferably 8.0 nm or less, from the viewpoint of further improving the thermal dimensional stability of the biaxially oriented polypropylene film 100, and is preferably 3.0 nm or more, more preferably 5.0 nm or more, even more preferably 8.0 nm or more, even more preferably 10.0 nm or more, and even more preferably 13.0 nm or more, from the viewpoint of further improving the performance balance of the formability and transparency of the biaxially oriented polypropylene film 100.
When the amorphous thickness _S4 that is prone to movement when heated is equal to or less than the upper limit value, the thermal dimensional stability of the biaxially oriented polypropylene film 100 can be further improved.

In addition, the amorphous thickness _S3 in the MD direction of the biaxially oriented polypropylene film 100 determined by SAXS measurement is, from the viewpoint of further improving the thermal dimensional stability of the biaxially oriented polypropylene film 100, preferably 9.5 nm or less, more preferably 9.0 nm or less, even more preferably 8.8 nm or less, even more preferably 8.6 nm or less, and even more preferably 8.0 nm or less, and from the viewpoint of further improving the performance balance of the formability and transparency of the biaxially oriented polypropylene film 100, is preferably 3.0 nm or more, more preferably 5.0 nm or more, even more preferably 7.0 nm or more, even more preferably 7.5 nm or more, and even more preferably 8.0 nm or more.

The sum ( _S3 + _S4 ) of the amorphous thickness _S3 in the MD direction and the amorphous thickness _S4 in the TD direction of the biaxially oriented polypropylene film 100 obtained by SAXS measurement is preferably 24.5 nm or less, more preferably 24.0 nm or less, even more preferably 23.5 nm or less, even more preferably 23.0 nm or less, even more preferably 20.0 nm or less, even more preferably 18.0 nm or less, even more preferably 16.0 nm or less, and even more preferably 15.0 nm or less, from the viewpoint of further improving the thermal dimensional stability of the biaxially oriented polypropylene film 100, and is preferably 5.0 nm or more, more preferably 8.0 nm or more, even more preferably 10.0 nm or more, even more preferably 13.0 nm or more, even more preferably 15.0 nm or more, even more preferably 17.0 nm or more, even more preferably 20.0 nm or more, even more preferably 22.0 nm or more, and even more preferably 23.0 nm or more, from the viewpoint of further improving the performance balance of the formability and transparency of the biaxially oriented polypropylene film 100.
The amorphous thickness _S3 in the MD direction and the amorphous thickness _S4 in the TD direction of the biaxially oriented polypropylene film 100, which are determined by SAXS measurement, can be measured by the method described in the Examples.

The crystal thickness _S6 in the TD direction of the biaxially oriented polypropylene film 100 determined by SAXS measurement is, from the viewpoint of further improving the performance balance of the formability and thermal dimensional stability of the biaxially oriented polypropylene film 100, preferably 13.5 nm or less, more preferably 13.0 nm or less, even more preferably 12.5 nm or less, even more preferably 12.0 nm or less, even more preferably 10.0 nm or less, and even more preferably 8.0 nm or less, and from the viewpoint of further improving the performance balance of the transparency and water vapor barrier property of the biaxially oriented polypropylene film 100, preferably 3.0 nm or more, more preferably 5.0 nm or more, even more preferably 8.0 nm or more, even more preferably 10.0 nm or more, even more preferably 12.0 nm or more, and even more preferably 12.5 nm or more.

In addition, the crystal thickness _S5 in the MD direction of the biaxially oriented polypropylene film 100 determined by SAXS measurement is preferably 9.0 nm or less, more preferably 8.0 nm or less, and even more preferably 7.5 nm or less, from the viewpoint of further improving the performance balance of the formability and thermal dimensional stability of the biaxially oriented polypropylene film 100, and is preferably 3.0 nm or more, more preferably 5.0 nm or more, and even more preferably 6.5 nm or more, from the viewpoint of further improving the performance balance of the transparency and water vapor barrier property of the biaxially oriented polypropylene film 100.

The sum ( _S5 + _S6 ) of the crystal thickness _S5 in the MD direction and the crystal thickness _S6 in the TD direction of the biaxially oriented polypropylene film 100 obtained by SAXS measurement is, from the viewpoint of further improving the performance balance of the formability and thermal dimensional stability of the biaxially oriented polypropylene film 100, preferably 21.0 nm or less, more preferably 20.5 nm or less, even more preferably 20.0 nm or less, even more preferably 19.0 nm or less, even more preferably 18.0 nm or less, even more preferably 17.0 nm or less, even more preferably 16.0 nm or less, and even more preferably 15.5 nm or less, and from the viewpoint of further improving the performance balance of the transparency and water vapor barrier property of the biaxially oriented polypropylene film 100, is preferably 5.0 nm or more, more preferably 8.0 nm or more, even more preferably 10.0 nm or more, even more preferably 13.0 nm or more, even more preferably 15.0 nm or more, even more preferably 16.0 nm or more, even more preferably 18.0 nm or more, and even more preferably 19.0 nm or more.
The crystal thickness _S5 in the MD direction and the crystal thickness _S6 in the TD direction of the biaxially oriented polypropylene film 100, which are determined by SAXS measurement, can be measured by the method described in the Examples.

The crystalline long period, amorphous thickness, and crystalline thickness of the biaxially stretched polypropylene film 100 can be adjusted, for example, by adjusting the type and content ratio of the propylene-based polymer contained in the biaxially stretched film layer 101, the thickness and stretch ratio of the biaxially stretched film layer 101, the constituent material and thickness of the surface resin layer 103, etc.

The sum (T1 + T2) of the tensile modulus T1 in the MD direction and the tensile modulus T2 in the TD direction of the biaxially oriented polypropylene film 100, measured in accordance with JIS K7127 (1999) using a tensile tester under conditions of a measurement temperature of ₂₃ ± ₂ ° _C , 50±5% RH, and a tensile speed of 5 mm/min, is preferably 3000 MPa or more, more preferably 3500 MPa or more, even more preferably 4000 MPa or more, even more preferably 5000 MPa _or more, even more preferably 6000 MPa or more, even more preferably 6500 MPa or more, and is preferably 10000 MPa or less, more preferably 8000 MPa or less, and even more preferably 7500 MPa or less.
When the sum ( _T1 + _T2 ) of the tensile modulus _T1 in the MD direction and the tensile modulus _T2 in the TD direction is equal to or greater than the lower limit, the biaxially oriented polypropylene film 100 can have a better balance of performance such as thermal dimensional stability, formability, water vapor barrier property, mechanical properties, transparency, bag formability, and handleability. Furthermore, the stiffness of the biaxially oriented polypropylene film 100 can be improved, and as a result, the film can be prevented from shifting in position during heat sealing, thereby preventing the occurrence of defective sealing.
In other words, when the sum ( _T1 + _T2 ) of the tensile modulus _T1 in the MD direction and the tensile modulus _T2 in the TD direction is equal to or greater than the above-mentioned lower limit, the biaxially oriented polypropylene film 100 can have a better balance of thermal dimensional stability, formability, water vapor barrier properties, mechanical properties, transparency, bag formability, handleability, and packaging suitability.
In addition, when the sum ( _T1 + _T2 ) of the tensile modulus _T1 in the MD direction and the tensile modulus _T2 in the TD direction is equal to or less than the upper limit, problems such as breakage are less likely to occur during molding of the biaxially oriented polypropylene film 100, continuous stretch molding of the film becomes easier, and industrial continuous productivity can be further improved.
Such a tensile modulus is a substitute value for quantitatively measuring the stiffness of a film, and can be adjusted, for example, by adjusting the type and content ratio of the propylene-based polymer contained in the biaxially oriented film layer 101, the thickness and stretching ratio of the biaxially oriented film layer 101, the constituent material and thickness of the surface resin layer 103, etc.

In addition, the tensile modulus _T1 in the MD direction of the biaxially oriented polypropylene film 100 is preferably 1000 MPa or more, more preferably 1200 MPa or more, even more preferably 1300 MPa or more, even more preferably 1400 MPa or more, even more preferably 1500 MPa or more, even more preferably 1800 MPa or more, even more preferably 2000 MPa or more, and even more preferably 2300 MPa or more, from the viewpoint of further improving the performance balance of the biaxially oriented polypropylene film 100, including the thermal dimensional stability, antistatic properties, bag formability, and packaging suitability. In addition, the tensile modulus T1 in the MD direction of the biaxially oriented polypropylene film 100 is preferably 4000 MPa or less, more preferably 3500 MPa or less, even more preferably 3000 MPa or less, even more preferably 2800 MPa or less, and even more preferably 2600 MPa or less, from the viewpoint of further improving the performance balance of the biaxially oriented polypropylene film 100, including the thermal dimensional stability, antistatic properties, bag formability, and packaging suitability.

The biaxially oriented polypropylene film 100 of this embodiment preferably has the property of expanding in the TD direction and shrinking in the MD direction when heat-treated at 120°C for 15 minutes in accordance with JIS C2151:2019, from the viewpoint of further improving the thermal dimensional stability of the biaxially oriented polypropylene film 100.

As described above, further improvement in the thermal dimensional stability of biaxially oriented polypropylene films is required from the viewpoint of suppressing thermal wrinkles in the sealed portions during bag making and from the viewpoint of suppressing thermal elongation during vapor deposition and coating processes.
Here, according to the inventors' investigations, it was found that the thermal dimensional stability of the biaxially oriented polypropylene film 100 can be improved by having the property of expanding in the TD direction and shrinking in the MD direction when heated at 120°C for 15 minutes.
Generally, a roll of biaxially oriented polypropylene film is unwound in the MD direction, and bag making, coating, vapor deposition, etc. are performed while tension is applied. In other words, since there is no tension in the TD direction, the biaxially oriented polypropylene film is susceptible to heat shrinkage when heated, and heat wrinkles are likely to occur in the sealed area. In addition, since there is tension in the MD direction, if the film has low heat resistance, the film is likely to thermally expand in the MD direction when heated.
On the other hand, the biaxially oriented polypropylene film 100 of the present embodiment has the property of expanding in the TD direction and shrinking in the MD direction when heated at 120° C. for 15 minutes, and is therefore considered to be less susceptible to thermal shrinkage in the TD direction and thermal elongation in the MD direction even when the biaxially oriented polypropylene film 100 is heated. Therefore, it is presumed that the biaxially oriented polypropylene film 100 of the present embodiment, which has the property of expanding in the TD direction and shrinking in the MD direction when heated at 120° C. for 15 minutes in accordance with JIS C2151:2019, has improved thermal dimensional stability, and as a result, it is possible to further suppress thermal wrinkles in the sealed portion.
In other words, according to the biaxially oriented polypropylene film 100 of the present embodiment, which has the property of expanding in the TD direction and shrinking in the MD direction when heat-treated at 120°C for 15 minutes in accordance with JIS C2151:2019, the thermal dimensional stability can be further improved.
In addition, since such a biaxially oriented polypropylene film 100 has improved thermal dimensional stability, it is possible to suppress thermal wrinkles in the sealed portions during bag making, thereby further improving bag making properties.

In order to further improve the balance of thermal dimensional stability and bag formability, it is preferable that the biaxially oriented polypropylene film 100 expands in the TD direction when heat-treated at 120°C for 15 minutes in accordance with JIS C2151:2019.
More specifically, the thermal expansion coefficient in the TD direction of the biaxially oriented polypropylene film 100 when heat-treated at 120°C for 15 minutes is, from the viewpoint of further improving the performance balance between thermal dimensional stability and bag formability, and from the viewpoint of further suppressing thermal wrinkles in the sealed portion and obtaining a bag product with good thermal wrinkles in the sealed portion, preferably 0.1% or more, more preferably 0.2% or more, even more preferably 0.3% or more, even more preferably 0.4% or more, and even more preferably 0.5% or more, and from the viewpoint of further improving the performance balance between thermal dimensional stability and bag formability, it is preferably 2.0% or less, more preferably 1.5% or less, even more preferably 1.2% or less, even more preferably 1.0% or less, and even more preferably 0.8% or less.
Generally, a roll of biaxially oriented polypropylene film is unwound in the MD direction, and bag making, coating, deposition, etc. are performed while tension is applied. That is, since no tension is applied in the TD direction, the biaxially oriented polypropylene film is susceptible to heat shrinkage when heated, and heat wrinkles are easily formed in the sealed portion. On the other hand, if the thermal expansion coefficient in the TD direction when heated at 120°C for 15 minutes is within the above range, heat shrinkage is unlikely to occur in the TD direction even when the biaxially oriented polypropylene film 100 is heated, and heat wrinkles in the sealed portion can be further suppressed.
The thermal expansion coefficient in the TD direction of the biaxially oriented polypropylene film 100 when it is heat-treated at 120° C. for 15 minutes is calculated by the following method.
First, a test piece of 10 cm x 10 cm is cut out from the biaxially stretched polypropylene film 100, and this test piece is heat-treated for 15 minutes at 120° C. Next, when the length in the TD direction of the test piece after the heat treatment is TD ₁ [cm], the thermal expansion coefficient in the TD direction [%] is calculated by 100 x (TD ₁ - 10)/10.

Furthermore, the heat shrinkage rate in the MD direction of the biaxially oriented polypropylene film 100 when heated at 120°C for 15 minutes is, from the viewpoint of further improving the performance balance between thermal dimensional stability and bag formability, and from the viewpoint of further suppressing thermal elongation of the film during processing, preferably 5.0% or less, more preferably 4.0% or less, even more preferably 3.0% or less, even more preferably 2.5% or less, even more preferably 2.2% or less, and even more preferably 2.0% or less, and may be 0.1% or more, 0.3% or more, or 0.5% or more.
Generally, a roll of biaxially oriented polypropylene film is unwound in the MD direction, and bag making, coating, deposition, etc. are performed while tension is applied. That is, since tension is applied in the MD direction, if the heat resistance of the film is low, the film is likely to thermally elongate in the MD direction when heated. On the other hand, if the heat shrinkage rate in the MD direction when heated at 120°C for 15 minutes is within the above range, it is possible to further suppress the thermal elongation in the MD direction when the biaxially oriented polypropylene film 100 is heated.
The heat shrinkage rate in the MD direction of the biaxially oriented polypropylene film 100 when it is heat-treated at 120° C. for 15 minutes is calculated by the following method.
First, a test piece of 10 cm x 10 cm is cut out from the biaxially stretched polypropylene film 100, and this test piece is heat-treated for 15 minutes at 120° C. Next, when the length in the MD direction of the test piece after heat treatment is MD ₁ [cm], the heat shrinkage rate [%] in the MD direction is calculated by 100 x (10 - MD ₁ )/10.

Furthermore, the heat shrinkage rate _XTD in the TD direction of the biaxially oriented polypropylene film 100 when heat-treated at 150°C for 15 minutes is, from the viewpoint of further improving the performance balance between thermal dimensional stability and bag formability, preferably 8.5% or less, more preferably 7.0% or less, even more preferably 5.0% or less, even more preferably 3.0% or less, even more preferably 2.0% or less, even more preferably 1.0% or less, even more preferably 0.8% or less, and may be 0.0% or more, 0.1% or more, or 0.2% or more.

Furthermore, the heat shrinkage rate _XMD in the MD direction of the biaxially oriented polypropylene film 100 when heat-treated at 150°C for 15 minutes is, from the viewpoint of further improving the performance balance between thermal dimensional stability and bag formability, preferably 8.0% or less, more preferably 7.0% or less, even more preferably 6.0% or less, even more preferably 5.5% or less, even more preferably 5.0% or less, and even more preferably 4.8% or less, and may be 0.1% or more, 0.5% or more, 1.0% or more, 1.5% or more, 2.0% or more, or 2.5% or more.

In the biaxially stretched polypropylene film 100, when the heat shrinkage rate in the TD direction and the heat shrinkage rate in the MD direction when heated at 150° C. for 15 minutes are X _TD [%] and X _MD [%], respectively, X _TD +X _MD is preferably less than 7.0%, more preferably 6.5% or less, and even more preferably less than 6.0%, from the viewpoint of further improving the performance balance of the thermal dimensional stability and bag formability of the biaxially stretched polypropylene film 100.
Moreover, X _TD [%] and X _MD [%] of the biaxially stretched polypropylene film 100 are calculated by the following method.
First, a test piece of 10 cm x 10 cm is cut out from the biaxially stretched polypropylene film 100, and this test piece is heat-treated for 15 minutes at 150° C. Next, when the length in the TD direction of the test piece after heat treatment is TD ₁ [cm] and the length in the MD direction of the test piece after heat treatment is MD ₁ [cm], X _TD [%] is calculated by 100 x (10 - TD ₁ )/10, and X _MD [%] is calculated by 100 x (10 - MD ₁ )/10.

The thermal expansion coefficient and thermal shrinkage coefficient of the biaxially oriented polypropylene film 100 can be adjusted, for example, by adjusting the type and content ratio of the propylene-based polymer contained in the biaxially oriented film layer 101, the thickness and stretching ratio of the biaxially oriented film layer 101, the constituent material and thickness of the surface resin layer 103, etc.
In addition, the thermal expansion coefficient and thermal shrinkage coefficient of the biaxially oriented polypropylene film 100 can be measured in accordance with JIS C2151:2019.

The heat fusion strength when the biaxially oriented polypropylene films 100 are heat sealed together at 200°C (hereinafter also referred to as "heat fusion strength at 200°C") is preferably 4.0 N/15 mm or less, from the viewpoint of further improving the performance balance between thermal dimensional stability and bag formability.
In this specification, the heat fusion strength is used as an index of the heat fusion resistance of the biaxially oriented polypropylene film surface. It can be determined that the lower the heat fusion strength, the better the heat fusion resistance of the biaxially oriented polypropylene film surface.
Here, the heat fusion strength when heat sealed at 200° C. can be measured by the following method. First, two biaxially oriented polypropylene films 100 are heat fused under the conditions of 200° C., pressure of 2.0 kgf, and sealing time of 1.0 second to obtain a laminated film. Next, the two biaxially oriented polypropylene films 100 are peeled under the conditions of 15 mm width, 90 degree peel, peel speed of 300 mm/min, and tension in the TD direction, and the peel strength at this time is taken as the heat fusion strength.

As described above, further improvement in the thermal dimensional stability of biaxially oriented polypropylene films is required from the viewpoint of suppressing thermal wrinkles in the sealed portions during bag making and from the viewpoint of suppressing thermal elongation during vapor deposition and coating processes.
Here, according to the investigations of the present inventors, it was found that a biaxially oriented polypropylene film having a heat fusion strength of 4.0 N/15 mm or less when heat sealed at 200° C. can have improved thermal dimensional stability.
That is, according to the biaxially oriented polypropylene film 100 of this embodiment, which has a heat fusion strength of 4.0 N/15 mm or less when heat sealed at 200° C., the thermal dimensional stability can be further improved.
In addition, since such a biaxially oriented polypropylene film 100 has improved thermal dimensional stability, it is possible to suppress thermal wrinkles in the sealed portions during bag making, thereby further improving bag making properties.
Furthermore, from the perspective of environmental issues, there is a demand for mono-material packaging materials, and from the perspective of suppressing heat wrinkles in the sealed parts during bag making and suppressing heat fusion of the film to the sealing bar, there is a demand for film surfaces with improved heat resistance compared to conventional biaxially oriented polypropylene films.
The biaxially oriented polypropylene film 100 of this embodiment has a heat fusion strength of 4.0 N/15 mm or less when heat sealed at 200°C, and has an improved performance balance between thermal dimensional stability and heat resistance of the film surface, which can further suppress heat wrinkles in the sealed area during bag making and heat fusion of the film to the seal bar.

In a package produced using the biaxially oriented polypropylene film 100, from the viewpoint of further improving the performance balance between the ability to prevent the film from fusing to the seal bar during bag making processing and the seal appearance, the heat fusion strength (TD tensile direction) of the portion heat-sealed under conditions of 200°C, a pressure of 2.0 kgf, and a sealing time of 1.0 second is preferably 4.0 N/15 mm or less, more preferably 3.5 N/15 mm or less, even more preferably 3.0 N/15 mm or less, even more preferably 2.5 N/15 mm or less, even more preferably 2.0 N/15 mm or less, even more preferably 1.5 N/15 mm or less, and even more preferably 1.3 N/15 mm or less. The lower limit of the heat fusion strength of the biaxially oriented polypropylene film 100 at 200°C is not particularly limited, but may be 0.01 N/15 mm or more, 0.05 N/15 mm or more, 0.1 N/15 mm or more, 0.3 N/15 mm or more, 0.5 N/15 mm or more, or 0.8 N/15 mm or more.
In this specification, the heat fusion strength is used as an index of the heat fusion resistance of the biaxially oriented polypropylene film surface. It can be determined that the lower the heat fusion strength, the better the heat fusion resistance of the biaxially oriented polypropylene film surface.
Here, the heat fusion strength can be measured by the following method. First, two biaxially oriented polypropylene films 100 are heat fused under the conditions of 200° C., pressure of 2.0 kgf, and sealing time of 1.0 second to obtain a laminated film. Next, the two biaxially oriented polypropylene films 100 are peeled under the conditions of 15 mm width, 90 degree peel, peel speed of 300 mm/min, and tension in the TD direction, and the peel strength at that time is taken as the heat fusion strength.
Such heat fusion strength can be adjusted, for example, by adjusting the type and content ratio of the homopolypropylene (A) and polymer (B) contained in the biaxially oriented film layer 101, the thickness and stretching ratio of the biaxially oriented film layer 101, the constituent material and thickness of the surface resin layer 103, etc.

The heat fusion strength when the biaxially oriented polypropylene films 100 are heat-sealed together at 170°C (hereinafter also referred to as "heat fusion strength at 170°C") is preferably 1.0 N/15 mm or less, more preferably 0.8 N/15 mm or less, even more preferably 0.5 N/15 mm or less, even more preferably 0.3 N/15 mm or less, and even more preferably 0.2 N/15 mm or less, from the viewpoint of further improving the performance balance of thermal dimensional stability and bag formability. The lower limit of the heat fusion strength of the biaxially oriented polypropylene film 100 at 170°C is not particularly limited, but may be 0.01 N/15 mm or more, 0.03 N/15 mm or more, or 0.05 N/15 mm or more.
Here, the heat fusion strength when heat sealed at 170° C. can be measured by the following method. First, two biaxially oriented polypropylene films 100 are heat fused under the conditions of 170° C., pressure of 2.0 kgf, and sealing time of 1.0 second to obtain a laminated film. Next, the two biaxially oriented polypropylene films 100 are peeled under the conditions of 15 mm width, 90 degree peel, peel speed of 300 mm/min, and tension in the TD direction, and the peel strength at this time is taken as the heat fusion strength.
The heat fusion strength at 170°C can be adjusted, for example, by adjusting the type and content ratio of the propylene-based polymer contained in the biaxially oriented film layer 101, the thickness and stretching ratio of the biaxially oriented film layer 101, the constituent material and thickness of the surface resin layer 103, etc.

The haze of the biaxially oriented polypropylene film 100, measured using a haze meter in accordance with JIS K7136:2000, is preferably 5.0% or less, more preferably 3.0% or less, even more preferably 2.5% or less, even more preferably 2.0% or less, even more preferably 1.5% or less, and even more preferably 1.0% or less, from the viewpoint of further improving the transparency of the biaxially oriented polypropylene film 100.
Such haze can be adjusted, for example, by adjusting the type and content ratio of the propylene-based polymer contained in the biaxially oriented film layer 101, the thickness and stretching ratio of the biaxially oriented film layer 101, the constituent material and thickness of the surface resin layer 103, etc.

Here, the food packaging produced using the biaxially oriented polypropylene film 100 exhibits sufficient performance in terms of water vapor barrier properties. Therefore, the biaxially oriented polypropylene film 100 can be particularly suitably used as a food packaging film for packaging foods that require water vapor barrier properties.

From the viewpoint of stably obtaining food packaging with improved water vapor barrier properties, the water vapor permeability of the biaxially oriented polypropylene film 100, measured by the method described below, is preferably 20.0 g/( ^m2 ·24 h) or less, more preferably 15.0 g/( ^m2 ·24 h) or less, even more preferably 12.0 g/( ^m2 ·24 h) or less, even more preferably 10.0 g/( ^m2 ·24 h) or less, and even more preferably 8.0 g/( ^m2 ·24 h) or less.
(Measuring method)
The biaxially oriented polypropylene film 100 is folded and two sides are heat sealed to form a bag. Calcium chloride is then placed in the bag as the content. The other side is then heat sealed to create a bag with a surface area of 0.01 ^m2 . The resulting bag is then stored for 72 hours under conditions of 40°C and 90% RH. The mass of calcium chloride before and after storage is measured, and the water vapor transmission rate (g/( ^m2 ·24h)) is calculated from the difference.
Such water vapor permeability can be adjusted, for example, by adjusting the type and content ratio of the propylene-based polymer contained in the biaxially oriented film layer 101, the thickness and stretching ratio of the biaxially oriented film layer 101, the constituent material and thickness of the surface resin layer 103, etc.

As described above, further improvement in the thermal dimensional stability of biaxially oriented polypropylene films is required from the viewpoint of suppressing thermal wrinkles in the sealed portions during bag making and from the viewpoint of suppressing thermal elongation during vapor deposition and coating processes.
On the other hand, when a highly crystalline homopolypropylene is used from the viewpoint of improving thermal dimensional stability, the high crystallinity results in a high yield stress during molding and an unstable stretch point, so that the effect of improving thermal dimensional stability is not sufficiently obtained.
Here, according to the research of the present inventors, it has been found that by setting the amount of structural units derived from α-olefins other than propylene contained in a biaxially oriented polypropylene film to a specific range, the residual stress in the film can be efficiently alleviated and the thermal dimensional stability of the biaxially oriented polypropylene film can be further improved.
That is, by setting the amount of structural units derived from α-olefins other than propylene within a specific range, the biaxially oriented polypropylene film 100 of this embodiment can improve the thermal dimensional stability.
In addition, since such a biaxially oriented polypropylene film 100 has improved thermal dimensional stability, it is possible to more effectively suppress thermal wrinkles in the sealed portions during bag making, thereby further improving bag making properties.

The amount of structural units derived from α-olefins other than propylene contained in the biaxially oriented polypropylene film 100, when the total amount of structural units derived from monomers contained in the biaxially oriented polypropylene film 100 is taken as 100 mol%, is preferably 0.05 mol% or more, more preferably 0.1 mol% or more, even more preferably 0.3 mol% or more, and even more preferably 0.5 mol% or more, from the viewpoint of further improving the performance balance of the formability, thermal dimensional stability, and bag formability of the biaxially oriented polypropylene film 100; and from the viewpoint of further improving the performance balance of the thermal dimensional stability, water vapor barrier property, bag formability, and transparency of the biaxially oriented polypropylene film 100, is preferably 50.0 mol% or less, more preferably 30.0 mol% or less, even more preferably 25.0 mol% or less, even more preferably 20.0 mol% or less, even more preferably 15.0 mol% or less, even more preferably 12.0 mol% or less, even more preferably 10.0 mol% or less, even more preferably 8.0 mol% or less, even more preferably 5.0 mol% or less, even more preferably 2.0 mol% or less, and even more preferably 1.0 mol% or less.
When the amount of structural units derived from α-olefins other than propylene contained in the biaxially stretched polypropylene film 100 is within the above range, the softening effect of the structural units derived from α-olefins exerts an effect of suppressing the yield point stress at the start of stretching in the stretching process, improving ease of formability. In addition, the low melting point effect of the structural units derived from α-olefins more efficiently relieves residual stress in the heat setting process during film molding, improving formability and suppressing thickness unevenness. As a result, the thermal dimensional stability of the biaxially stretched polypropylene film 100 can be further improved.
The amount of structural units derived from α-olefins other than propylene in the biaxially oriented polypropylene film 100 can be measured by the method described in the Examples.

The α-olefin in the structural units derived from α-olefins other than propylene contained in the biaxially stretched polypropylene film 100 includes, for example, one or more selected from the group consisting of ethylene and α-olefins having 4 to 10 carbon atoms, preferably one or more selected from the group consisting of ethylene and α-olefins having 4 to 8 carbon atoms, more preferably one or more selected from the group consisting of ethylene, 1-butene, and 1-octene, and even more preferably one or two selected from the group consisting of ethylene and 1-butene.

The thickness of the biaxially oriented polypropylene film 100 is preferably 5 μm or more, more preferably 10 μm or more, even more preferably 12 μm or more, and even more preferably 15 μm or more, from the viewpoint of further improving the balance of performance such as thermal dimensional stability, formability, water vapor barrier properties, cost, mechanical properties, transparency, bag formability, ease of handling, appearance, and light weight, and is preferably 100 μm or less, more preferably 50 μm or less, even more preferably 40 μm or less, even more preferably 30 μm or less, and even more preferably 25 μm or less.

The layers that make up the biaxially oriented polypropylene film 100 are described below.

[Biaxially oriented film layer]
The biaxially oriented film layer 101 (also called a biaxially oriented polypropylene-based film layer) contains a propylene-based polymer.
The biaxially stretched film layer 101 is formed, for example, by biaxially stretching a film made of a propylene-based polymer composition containing a propylene-based polymer.

The biaxially stretched film layer 101 may be a single layer or may be a laminate of multiple layers made of a propylene-based polymer composition, but it is necessary that it is biaxially stretched.

The thickness of the biaxially oriented film layer 101 is preferably 5 μm or more, more preferably 10 μm or more, even more preferably 12 μm or more, and even more preferably 15 μm or more, from the viewpoint of further improving the performance balance of the biaxially oriented polypropylene film 100, such as thermal dimensional stability, formability, water vapor barrier properties, cost, mechanical properties, transparency, bag formability, handleability, appearance, and light weight, and is preferably 100 μm or less, more preferably 50 μm or less, even more preferably 40 μm or less, even more preferably 30 μm or less, and even more preferably 20 μm or less.

In the biaxially oriented polypropylene film 100, the ratio of the thickness of the biaxially oriented film layer 101 to the total thickness of the biaxially oriented polypropylene film 100 is preferably 50% or more, more preferably 60% or more, even more preferably 70% or more, even more preferably 75% or more, and preferably 100% or less, more preferably 99% or less, even more preferably 95% or less, even more preferably 90% or less.

(Propylene-Based Polymer Composition)
The propylene-based polymer composition of the present embodiment contains a propylene-based polymer.
From the viewpoint of further improving the balance of performances of the biaxially stretched polypropylene film 100, such as thermal dimensional stability, environmental compatibility, heat resistance, water vapor barrier property, transparency, cost, mechanical properties, rigidity, bag formability, fluidity, moldability, handleability, appearance, and lightness, the propylene polymer content in the propylene polymer composition of the present embodiment, i.e., the biaxially stretched film layer 101, is preferably 60% by mass or more, more preferably 70% by mass or more, even more preferably 80% by mass or more, even more preferably 90% by mass or more, even more preferably 95% by mass or more, even more preferably 98% by mass or more, and for example, 100% by mass or less, when the entire propylene polymer composition is taken as 100% by mass.

(Propylene-based polymer)
The propylene-based polymer of the present embodiment is a polymer containing a structural unit derived from propylene, and examples thereof include homopolypropylene (A); at least one polymer (B) selected from the group consisting of random polypropylene (B1) and α-olefin copolymer (B2); and the like.

(Homopolypropylene (A))
Examples of the homopolypropylene (A) include propylene homopolymers and propylene copolymers having a content of structural units derived from α-olefins other than propylene of 2.0 mol % or less.
When the total content of the structural units constituting the homopolypropylene (A) is taken as 100 mol %, the content of structural units derived from propylene in the homopolypropylene (A) is 98.0 mol % or more, preferably 98.5 mol % or more, more preferably 98.7 mol % or more, even more preferably 99.0 mol % or more, even more preferably 99.5 mol % or more, even more preferably 99.8 mol % or more, and is, for example, 100.0 mol % or less.

The α-olefin other than propylene includes, for example, one or more selected from the group consisting of ethylene and α-olefins having 4 to 20 carbon atoms, preferably one or more selected from the group consisting of ethylene and α-olefins having 4 to 6 carbon atoms, more preferably at least one selected from the group consisting of ethylene and 1-butene, and even more preferably ethylene.
The content of structural units derived from α-olefins other than propylene, when the entire homopolypropylene (A) is taken as 100 mol %, is preferably 2.0 mol % or less, more preferably 1.5 mol % or less, even more preferably 1.3 mol % or less, even more preferably 1.0 mol % or less, even more preferably 0.5 mol % or less, and even more preferably 0.2 mol % or less.
The homopolypropylene (A) in the biaxially oriented film layer 101 may be used alone or in combination of two or more kinds.

The isotactic mesopentad fraction (mmmm) of the homopolypropylene (A) is preferably 96.0% or more, more preferably 96.5% or more, even more preferably 97.0% or more, even more preferably 97.3% or more, even more preferably 97.5% or more, even more preferably 97.8% or more, and even more preferably 98.0% or more, from the viewpoint of further improving the balance of performance such as thermal dimensional stability, heat resistance, water vapor barrier property, mechanical properties, rigidity, and bag formability of the biaxially stretched polypropylene film 100. The upper limit of the isotactic mesopentad fraction (mmmm) of the homopolypropylene (A) is not particularly limited, but from the viewpoint of ease of production, it is 99.5% or less, more preferably 99.3% or less, and even more preferably 99.0% or less.
The isotactic mesopentad fraction (mmmm) is an index of stereoregularity and can be determined by a known method from ¹³ C-nuclear magnetic resonance (NMR) spectrum.
When two or more types of homopolypropylenes are used as the homopolypropylene (A), the isotactic mesopentad fraction of the homopolypropylene (A) can be the isotactic mesopentad fraction of a mixture obtained by melt blending two or more types of homopolypropylene (A) by a known method.

The melt flow rate (MFR) of the homopolypropylene (A), measured in accordance with ASTM D1238 under conditions of 230°C and a load of 2.16 kg, is preferably 0.5 g/10 min or more, more preferably 1.0 g/10 min or more, and even more preferably 2.0 g/10 min or more, from the viewpoint of further improving the balance of performance between fluidity and moldability, and is preferably 20.0 g/10 min or less, more preferably 10.0 g/10 min or less, and even more preferably 7.0 g/10 min or less, from the viewpoint of further stabilizing moldability.
When two or more types of homopolypropylenes are used as the homopolypropylene (A), the MFR of the homopolypropylene (A) can be the MFR of a mixture obtained by melt blending two or more types of homopolypropylene (A) by a known method.

From the viewpoint of further improving the balance of performance of the biaxially oriented polypropylene film 100, such as thermal dimensional stability, heat resistance, water vapor barrier property, mechanical properties, rigidity, bag formability, fluidity, and moldability, the melting point of the homopolypropylene (A) is preferably 150°C or higher, more preferably 155°C or higher, even more preferably 160°C or higher, and even more preferably 163°C or higher, and is preferably 180°C or lower, more preferably 175°C or lower, even more preferably 170°C or lower, and even more preferably 168°C or lower.
When two or more kinds of homopolypropylenes are used as the homopolypropylene (A), the melting point of the homopolypropylene (A) is the peak temperature of the maximum melting peak.

Homopolypropylene (A) can be produced by various methods. For example, it can be produced using known catalysts such as Ziegler-Natta catalysts and metallocene catalysts.

(Polymer (B))
The polymer (B) contains at least one selected from the group consisting of random polypropylene (B1) and α-olefin copolymer (B2), and preferably contains random polypropylene (B1).

The melt flow rate (MFR) of the polymer (B), measured in accordance with ASTM D1238 under conditions of 230°C and a load of 2.16 kg, is, from the viewpoint of further improving the performance balance of the moldability and thermal dimensional stability of the biaxially oriented polypropylene film 100, preferably 0.01 g/10 min or more, more preferably 0.1 g/10 min or more, even more preferably 0.5 g/10 min or more, even more preferably 1.0 g/10 min or more, even more preferably 2.0 g/10 min or more, and is preferably 30.0 g/10 min or less, more preferably 20.0 g/10 min or less, even more preferably 15.0 g/10 min or less, even more preferably 12.0 g/10 min or less, and even more preferably 10.0 g/10 min or less.
When two or more kinds of polymers are used as the polymer (B), the MFR of a mixture obtained by melt blending two or more kinds of the polymer (B) by a known method can be adopted.

From the viewpoint of further improving the balance of performance of the biaxially oriented polypropylene film 100, such as thermal dimensional stability, heat resistance, water vapor barrier property, mechanical properties, rigidity, bag formability, fluidity, and moldability, the melting point of the polymer (B) is preferably 50°C or higher, more preferably 60°C or higher, even more preferably 70°C or higher, even more preferably 80°C or higher, and even more preferably 90°C or higher, and is preferably 155°C or lower, more preferably 150°C or lower, even more preferably 148°C or lower, and even more preferably 145°C or lower.
When two or more kinds of polymers are used as polymer (B), the melting point of polymer (B) is the peak temperature of the maximum melting peak.

The weight average molecular weight (Mw) of the polymer (B) is preferably 100,000 or more, more preferably 150,000 or more, even more preferably 200,000 or more, and even more preferably 220,000 or more, from the viewpoint of further improving the performance balance of the formability, thermal dimensional stability, blocking resistance, and sheet payout property of the biaxially oriented polypropylene film 100, and is preferably 1,000,000 or less, more preferably 800,000 or less, more preferably 600,000 or less, even more preferably 500,000 or less, and even more preferably 450,000 or less, from the viewpoint of further improving the thermal dimensional stability.

The weight average molecular weight (Mw)/number average molecular weight (Mn) of the polymer (B) is preferably 1.5 or more, more preferably 1.8 or more, from the viewpoint of further improving the performance balance of the formability, thermal dimensional stability, blocking resistance, and sheet payout ability of the biaxially oriented polypropylene film 100, and is preferably 8.0 or less, more preferably 7.5 or less, even more preferably 7.0 or less, and even more preferably 6.8 or less, from the viewpoint of further improving the performance balance of the formability, thermal dimensional stability, blocking resistance, and sheet payout ability of the biaxially oriented polypropylene film 100.
When two or more kinds of polymers are used as the polymer (B), the weight average molecular weight (Mw) and number average molecular weight (Mn) of the polymer (B) can be the weight average molecular weight (Mw) and number average molecular weight (Mn) of a mixture obtained by melt blending two or more kinds of the polymer (B) by a known method. The weight average molecular weight (Mw) and number average molecular weight (Mn) of the polymer (B) can be measured by the method described in the examples.

The content of polymer (B) is preferably 1% by mass or more, more preferably 2% by mass or more, and even more preferably 3% by mass or more, when the entire biaxially oriented film layer 101 is taken as 100% by mass, from the viewpoint of further improving the performance balance of the formability and thermal dimensional stability of the biaxially oriented polypropylene film 100. From the viewpoint of further improving the performance balance of the thermal dimensional stability, water vapor barrier properties, transparency, mechanical properties, rigidity, bag formability, fluidity, formability, etc. of the biaxially oriented polypropylene film 100, the content is preferably 50% by mass or less, more preferably 40% by mass or less, even more preferably 30% by mass or less, even more preferably 25% by mass or less, even more preferably 22% by mass or less, and even more preferably 20% by mass or less.

(Random polypropylene (B1))
The random polypropylene (B1) includes a random copolymer of propylene and an α-olefin other than propylene, in which the content of structural units derived from an α-olefin other than propylene is more than 2.0 mol % and not more than 15.0 mol %.
The α-olefin other than propylene includes, for example, one or more selected from the group consisting of ethylene and α-olefins having 4 to 20 carbon atoms, preferably one or more selected from the group consisting of ethylene and α-olefins having 4 to 6 carbon atoms, more preferably at least one selected from ethylene and 1-butene, and even more preferably ethylene.

The content of structural units derived from α-olefins other than propylene in the random polypropylene (B1), when the entire random polypropylene (B1) is taken as 100 mol%, is preferably more than 2.0 mol%, more preferably 2.5 mol% or more, even more preferably 3.0 mol% or more, even more preferably 3.5 mol% or more, and even more preferably 4.0 mol% or more, from the viewpoint of further improving the performance balance of the formability, thermal dimensional stability, and bag formability of the biaxially oriented polypropylene film 100, and is preferably 15.0 mol% or less, more preferably 12.0 mol% or less, even more preferably 10.0 mol% or less, even more preferably 8.0 mol% or less, and even more preferably 6.5 mol% or less, from the viewpoint of further improving the performance balance of the thermal dimensional stability, water vapor barrier property, bag formability, and transparency of the biaxially oriented polypropylene film 100.
The amount of constituent units derived from an α-olefin other than propylene can be measured by the method described in the Examples.

The random polypropylene (B1) preferably contains one or more selected from the group consisting of a propylene-ethylene random copolymer, a propylene-ethylene-1-butene random copolymer, and a propylene-1-butene random copolymer, more preferably contains one or more selected from the group consisting of a propylene-ethylene random copolymer, and a propylene-1-butene random copolymer, and even more preferably contains a propylene-ethylene random copolymer.
The random polypropylene (B1) in the biaxially oriented film layer 101 may be used alone or in combination of two or more kinds.

(α-Olefin Copolymer (B2))
The α-olefin copolymer (B2) is a copolymer of two or more kinds of α-olefins, and includes, for example, an α-olefin copolymer in which the content of structural units derived from an α-olefin other than propylene exceeds 15.0 mol %.
The α-olefin copolymer (B2) includes a random copolymer of propylene and an α-olefin other than propylene, in which the content of structural units derived from an α-olefin other than propylene exceeds 15.0 mol %.
The α-olefin other than propylene includes, for example, one or more selected from the group consisting of ethylene and α-olefins having 4 to 10 carbon atoms, preferably one or more selected from the group consisting of α-olefins having 4 to 8 carbon atoms, more preferably at least one selected from 1-butene and 1-octene, and even more preferably 1-butene.

The content of structural units derived from an α-olefin other than propylene in the α-olefin copolymer (B2), when the entire α-olefin copolymer (B2) is taken as 100 mol%, is preferably more than 15.0 mol%, more preferably 20.0 mol% or more, even more preferably 30.0 mol% or more, even more preferably 50.0 mol% or more, even more preferably 70.0 mol% or more, and even more preferably 80.0 mol% or more, from the viewpoint of further improving the performance balance of the formability, thermal dimensional stability, and bag formability of the biaxially oriented polypropylene film 100, and is preferably 99.0 mol% or less, more preferably 98.0 mol% or less, even more preferably 95.0 mol% or less, even more preferably 92.0 mol% or less, and even more preferably 90.0 mol% or less, from the viewpoint of further improving the performance balance of the thermal dimensional stability, water vapor barrier property, bag formability, and transparency of the biaxially oriented polypropylene film 100.
The amount of constituent units derived from an α-olefin other than propylene in the α-olefin copolymer (B2) can be measured by the method described in the Examples.

The α-olefin copolymer (B2) preferably comprises a random copolymer of propylene and one or more α-olefins selected from the group consisting of ethylene and α-olefins having 4 to 10 carbon atoms, more preferably a random copolymer of propylene and one or two α-olefins selected from the group consisting of 1-butene and 1-octene, and even more preferably a random copolymer of propylene and 1-butene.
The α-olefin copolymer (B2) in the biaxially stretched film layer 101 may be used alone or in combination of two or more kinds.

Polymer (B) can be produced by various methods. For example, it can be produced using known catalysts such as Ziegler-Natta catalysts and metallocene catalysts.

(Other ingredients)
To the propylene polymer composition of the present embodiment, various additives such as a tackifier, a heat stabilizer, a weather stabilizer, an antioxidant, an ultraviolet absorber, a lubricant, a slipping agent, a nucleating agent, an antiblocking agent, an antistatic agent, an antifogging agent, a pigment, a dye, and an inorganic or organic filler may be added as necessary within a range that does not impair the object of the present embodiment.

(Method for preparing propylene polymer composition)
The propylene polymer composition of the present embodiment can be prepared by mixing or melt-kneading the components using a dry blend, a tumbler mixer, a Banbury mixer, a single-screw extruder, a twin-screw extruder, a high-speed twin-screw extruder, a heated roll, or the like.

[Surface resin layer]
It is preferable that the biaxially oriented polypropylene film 100 further comprises a surface resin layer 103 on at least one side of the biaxially oriented film layer 101 in order to impart functions such as heat resistance, heat sealability, antistatic properties, blocking resistance, printability, and slip properties to the film surface depending on the purpose.
The surface resin layer 103 may be provided on both sides of the biaxially stretched film layer 101. By providing the surface resin layer 103 on both sides of the biaxially stretched film layer 101, different functions can be imparted to each surface of the film.
In addition, the surface resin layer 103 is preferably provided on the outermost layer of the biaxially oriented polypropylene film 100 in order to further improve the functions of the biaxially oriented polypropylene film 100, such as heat resistance, heat sealability, antistatic properties, blocking resistance, printability, slip properties, etc., depending on the purpose.

The surface resin layer 103 is preferably provided so as to be in direct contact with the surface of the biaxially oriented film layer 101. This simplifies the manufacturing process of the biaxially oriented polypropylene film 100.

In the biaxially oriented polypropylene film 100, the thickness of the surface resin layer 103 is preferably 0.1 μm or more, more preferably 0.2 μm or more, even more preferably 0.5 μm or more, even more preferably 1.0 μm or more, and even more preferably 1.5 μm or more, from the viewpoint of further improving the functions of the biaxially oriented polypropylene film 100, such as heat fusion resistance, antistatic properties, blocking resistance, printability, and slip properties, and is preferably 10.0 μm or less, more preferably 8.0 μm or less, even more preferably 6.0 μm or less, even more preferably 5.0 μm or less, and even more preferably 3.0 μm or less, from the viewpoint of further improving the performance balance of the biaxially oriented polypropylene film 100, such as heat fusion resistance, thermal dimensional stability, formability, cost, mechanical properties, transparency, environmental compatibility, and light weight.
Here, the thickness of the surface resin layer 103 refers to the thickness of the surface resin layer 103 provided on one side of the biaxially stretched film layer 101. That is, in this embodiment, when the surface resin layer 103 is provided on both sides of the biaxially stretched film layer 101, the above-mentioned thickness of the surface resin layer 103 indicates the thickness of the surface resin layer 103 provided on one side of the biaxially stretched film layer 101.

In the biaxially oriented polypropylene film 100, it is preferable that the surface resin layer 103 is a single layer. This makes it possible to further simplify the manufacturing process of the biaxially oriented polypropylene film 100.

The surface resin layer 103 is preferably formed by biaxial stretching at the same time as the biaxially stretched film layer 101 in a state before biaxial stretching. This allows the biaxially stretched polypropylene film 100 to be produced using a molding method such as co-extrusion molding, i.e., a laminated film produced in a single molding operation, thereby further simplifying the manufacturing process of the biaxially stretched polypropylene film 100. Therefore, it is preferable that the surface resin layer 103 is biaxially stretched.

The surface resin layer 103 may be subjected to a surface treatment in order to further improve the balance of printability and blocking resistance of the biaxially oriented polypropylene film 100. Specifically, a surface activation treatment such as corona treatment, flame treatment, plasma treatment, primer coat treatment, or ozone treatment may be performed.

The surface resin layer 103 is composed of, for example, a polyolefin-based resin composition (A) containing a polyolefin. The polyolefin constituting the surface resin layer 103 includes, for example, one or more selected from the group consisting of homopolymers or copolymers of α-olefins such as ethylene, propylene, 1-butene, hexene-1, 4-methyl-pentene-1, and 1-octene; high-pressure low-density polyethylene; linear low-density polyethylene (LLDPE); high-density polyethylene; homopolypropylene; random copolymers of propylene and α-olefins having 2 to 10 carbon atoms; ethylene-vinyl acetate copolymers (EVA); and ionomer resins.
Among these, homopolypropylene is preferred as the polyolefin constituting the surface resin layer 103 from the viewpoint of further improving the balance of performance such as heat fusion resistance, thermal dimensional stability, heat resistance, water vapor barrier property, transparency, mechanical properties, rigidity, bag formability, fluidity, and moldability of the biaxially oriented polypropylene film 100. Here, the preferred embodiment of the homopolypropylene constituting the surface resin layer 103 is the same as the homopolypropylene (A) described above. That is, the homopolypropylene constituting the surface resin layer 103 preferably contains the homopolypropylene (A) described above.

From the viewpoint of further improving the balance of performance such as heat resistance, thermal dimensional stability, heat resistance, water vapor barrier property, transparency, mechanical properties, rigidity, bag formability, fluidity and moldability of the biaxially oriented polypropylene film 100, the content of polyolefin in the polyolefin resin composition (A), i.e., the surface resin layer 103, is preferably 75% by mass or more, more preferably 80% by mass or more, even more preferably 90% by mass or more, even more preferably 95% by mass or more, even more preferably 98% by mass or more, even more preferably 99% by mass or more, and preferably 100% by mass or less, when the entire polyolefin resin composition (A), i.e., the entire surface resin layer 103, is taken as 100% by mass.
From the viewpoint of further improving the balance of performance such as heat resistance, thermal dimensional stability, heat resistance, water vapor barrier property, transparency, mechanical properties, rigidity, bag formability, fluidity and moldability of the biaxially oriented polypropylene film 100, the content of homopolypropylene (A) in the polyolefin resin composition (A), i.e., the surface resin layer 103, is preferably 75% by mass or more, more preferably 80% by mass or more, even more preferably 90% by mass or more, even more preferably 95% by mass or more, even more preferably 98% by mass or more, even more preferably 99% by mass or more, and preferably 100% by mass or less, when the entire polyolefin resin composition (A), i.e., the entire surface resin layer 103, is taken as 100% by mass.

(Other ingredients)
If necessary, various additives such as tackifiers, heat stabilizers, weather stabilizers, antioxidants, UV absorbers, lubricants, slipping agents, nucleating agents, antiblocking agents, antistatic agents, antifogging agents, pigments, dyes, and inorganic or organic fillers may be added to the polyolefin resin composition (A) constituting the surface resin layer 103, within a range that does not impair the object of this embodiment.

(Method for preparing polyolefin resin composition (A))
The polyolefin resin composition (A) can be prepared, for example, by mixing or melt-kneading the components using a dry blend, a tumbler mixer, a Banbury mixer, a single-screw extruder, a twin-screw extruder, a high-speed twin-screw extruder, a heated roll, or the like.

<Method of manufacturing biaxially oriented polypropylene film>
The biaxially oriented polypropylene film 100 can be obtained, for example, by co-extrusion molding a propylene-based polymer composition for forming the biaxially oriented film layer 101 and, if necessary, a polyolefin-based resin composition (A) for forming the surface resin layer 103 into a film, and then biaxially stretching the film obtained by the co-extrusion molding using a known biaxially oriented film production method such as a simultaneous biaxial stretching method, a sequential biaxial stretching method, or an inflation biaxial stretching method.
The molding device and molding conditions are not particularly limited, and conventionally known molding devices and molding conditions can be adopted. As the molding device, a T-die extruder, a multi-layer T-die extruder, an inflation molding machine, a multi-layer inflation molding machine, or the like can be used. As the biaxial stretching conditions, for example, known OPP film manufacturing conditions can be adopted. More specifically, in the sequential biaxial stretching method, for example, the stretching temperature in the MD direction may be set to 100°C to 145°C, the stretching ratio in the MD direction may be set to a range of 4.5 to 6 times, the stretching temperature in the TD direction may be set to 130°C to 190°C, and the stretching ratio in the TD direction may be set to a range of 9 to 11 times.
The biaxially oriented polypropylene film 100 can also be obtained by separately molding the biaxially oriented film layer 101 and, if necessary, the surface resin layer 103, laminating them together and molding them under heat.

<Applications of biaxially oriented polypropylene film>
The biaxially oriented polypropylene film 100 can also be suitably used as a food packaging film that constitutes a food package.

The food packaging of this embodiment is a packaging that uses a biaxially oriented polypropylene film 100, and is, for example, a packaging bag used for the purpose of containing food. Furthermore, the food packaging of this embodiment may use the biaxially oriented polypropylene film 100 in only a portion thereof depending on the application, or the biaxially oriented polypropylene film 100 may be used for the entire food packaging.

The food packaging of this embodiment includes the food packaging of this embodiment and food inside the food packaging. In other words, the food packaging of this embodiment is the food packaging of this embodiment that contains food.

Although the embodiments of the present invention have been described above with reference to the drawings, these are merely examples of the present invention, and various configurations other than those described above can also be adopted.
The biaxially oriented polypropylene film 100 may further include one or more layers selected from the group consisting of a sealant layer and a coating layer.
The biaxially oriented polypropylene film 100 can also be used as a raw material for coating.

The present embodiment will be described in detail below with reference to examples and comparative examples. Note that the present embodiment is not limited in any way to the descriptions of these examples.

1. Raw Materials Raw materials used in the Examples and Comparative Examples are shown below.
(1) Homopolypropylene (A)
h-PP1: homopolypropylene (MFR: 3.0 g/10 min, melting point: 165° C., isotactic mesopentad fraction (mmmm): 98.0%, Mw: 370,000, Mn: 68,000, Mw/Mn: 5.4, content of propylene-derived structural units: 100 mol%)
h-PP2: homopolypropylene (MFR: 3.0 g/10 min, melting point: 159°C, isotactic mesopentad fraction (mmmm): 97.5%, Mw: 469,000, Mn: 56,300, Mw/Mn: 8.3, content of ethylene-derived structural units: 1.2 mol%, content of propylene-derived structural units: 98.8 mol%)
(2) Polymer (B)
r-PP1: Random polypropylene (MFR: 7.0 g/10 min, melting point: 139°C, Mw: 322,000, Mn: 50,700, Mw/Mn: 6.4, content of ethylene-derived structural units: 3.2 mol%, content of 1-butene-derived structural units: 2.9 mol%, content of propylene-derived structural units: 93.9 mol%)
r-PP2: Random polypropylene (MFR: 2.4 g/10 min, melting point: 143° C., Mw: 436,000, Mn: 66,000, Mw/Mn: 6.6, content of ethylene-derived structural units: 4.4 mol%, content of propylene-derived structural units: 95.6 mol%)

2. Measurement and Evaluation Methods (1) Isotactic mesopentad fraction (mmmm) of homopolypropylene (A)
The isotactic mesopentad fraction (mesopentad fraction, (mmmm)) was measured by ¹³ C-NMR using a nuclear magnetic resonance apparatus (AVANCE III cryo-500 model, manufactured by Bruker Biospin). The sample was dissolved in the following measurement solvent and measured, and the evaluation was made from the integrated intensity of each signal.
[Measurement condition]
Measurement nucleus: ^13C (125MHz)
Measurement mode: Single pulse proton broadband decoupling Pulse width: 45°
Number of points: 64k
Repeat time: 5.5 seconds Measurement solvent: orthodichlorobenzene/heavy benzene (4:1)
Sample concentration: 50 mg/0.6 mL
Measurement temperature: 120°C
Window function: exponential (BF: 0.5 Hz)
Chemical shift reference: mmmm (CH ₃ ): 21.59 ppm

(2) MFR of homopolypropylene (A) and polymer (B)
The measurement was performed in accordance with ASTM D1238 at 230° C. and under a load of 2.16 kg.

(3) Melting points of homopolypropylene (A) and polymer (B) Using a differential scanning calorimeter (product name: Q200DSC manufactured by TA Instruments), homopolypropylene (A) and polymer (B) were subjected to a first differential scanning calorimeter measurement (1st Run) consisting of a process of increasing the temperature from -30°C to 250°C at a temperature increase rate of 10°C/min and a process of decreasing the temperature from 250°C to -30°C at a temperature decrease rate of 10°C/min under a nitrogen stream, and a second differential scanning calorimeter measurement (2nd Run) consisting of a process of increasing the temperature from -30°C to 250°C at a temperature increase rate of 10°C/min. were successively performed.
The peak temperature of the maximum melting peak in the DSC curve in the second run was taken as the melting point.

(4) Weight average molecular weight (Mw) and number average molecular weight (Mn) of homopolypropylene (A) and polymer (B)
The weight average molecular weight (Mw) and number average molecular weight (Mn) of the homopolypropylene (A) and the polymer (B) were measured by gel permeation chromatography (GPC).
The GPC method was performed using a gel permeation chromatograph (Tosoh Corporation, HLC-8321 GPC/HT type) as follows. The separation columns were two TSKgel GNH6-HT and two TSKgel GNH6-HTL, each with a diameter of 7.5 mm and a length of 300 mm, the column temperature was 145° C., the mobile phase was o-dichlorobenzene and 0.025 mass% BHT as an antioxidant, and the flow rate was 1.0 mL/min, the sample concentration was 0.1% (w/v), the sample injection amount was 400 μL, and a differential refractometer was used as a detector. The molecular weight was calculated as polypropylene equivalent molecular weight using monodisperse polystyrene as a standard.

(5) Measurement of the content of structural units derived from α-olefins other than propylene in homopolypropylene (A) and polymer (B), and the content of structural units derived from α-olefins other than propylene contained in biaxially stretched polypropylene film The content of structural units derived from α-olefins other than propylene in homopolypropylene (A) and polymer (B), and the content of structural units derived from α-olefins other than propylene contained in biaxially stretched polypropylene film were measured by ¹³ C-NMR using a nuclear magnetic resonance device (AVANCE III cryo-500 model, manufactured by Bruker Biospin). The sample was dissolved in the following measurement solvent and measured, and the evaluation was performed based on the integrated intensity of each signal. The obtained ¹³ C-NMR spectrum confirmed the results of the studies in Macromolecules (1982) Ethylene-1-Butene Copolymers. 1. Commoner Sequence Distribution and Macromolecules (1977) Carbon-13 Nuclear Magnetic Resonance Determination of Monomer Composition and Sequence Distributions in Ethylene-Propylene Copolymers Prepared with a Stereoregular Catalyst. Signals were assigned with reference to the FT-IR System and the like, and the content (mol %) of ethylene-derived structural units, the content (mol %) of propylene-derived structural units, and the content (mol %) of 1-butene-derived structural units in each polymer were quantified.
[Measurement condition]
Measurement nucleus: ^13C (125MHz)
Measurement mode: Single pulse proton broadband decoupling Pulse width: 45°
Number of points: 64k
Repeat time: 5.5 seconds Measurement solvent: orthodichlorobenzene/heavy benzene (4:1)
Sample concentration: 50 mg/0.6 mL
Measurement temperature: 120°C
Window function: exponential (BF: 0.5 Hz)
In addition, the content of structural units derived from α-olefins other than propylene contained in the biaxially oriented polypropylene film was measured using the biaxially oriented polypropylene film as a sample.

(6) Tensile modulus A test piece of 15 mm x 15 cm was cut out from the biaxially stretched polypropylene film. The tensile modulus of elasticity in the MD direction T1 and the tensile modulus of elasticity in the TD direction T2 of the test piece were measured using a tensile tester manufactured by Orientec Co., Ltd. in accordance with JIS K7127 (1999) under the conditions of a measurement temperature of ₂₃ ± ₂ °C, 50±5% RH, and a tensile speed of 5 mm/min.

(7) Differential Scanning Calorimetry of Biaxially Stretched Polypropylene Film A test piece of about 5.0 mg was cut out from the biaxially oriented polypropylene film. Next, the sample was subjected to a first differential scanning calorimetry (1st Run) using a differential scanning calorimeter (product name: Q200DSC, manufactured by TA Instruments) under a nitrogen gas flow, which consisted of a process of increasing the temperature from -50°C to 250°C at a temperature increase rate of 5°C/min and a process of decreasing the temperature from 250°C to -50°C at a temperature decrease rate of 5°C/min.
From the obtained DSC curve, the main melting point (° C.), the heat of fusion ΔH (J/g) of the entire film, and the heat of fusion ΔH (J/g) at 165° C. or less were determined. Here, the peak temperature of the maximum melting peak in the DSC curve was taken as the main melting point.
The heat of fusion ΔH (J/g) of the entire film was calculated from the melting peak area of the DSC curve in accordance with JIS K 7122:1987 (with the exception that the heating rate was 5° C./min). When multiple melting peaks appear in the DSC curve, the total area of the multiple melting peaks was used as the heat of fusion (ΔH) of the entire film.
The heat of fusion ΔH (J/g) at 165° C. or less is the heat of fusion ΔH (J/g) in the range of 165° C. or less out of the heat of fusion ΔH (J/g) of the entire film.

Next, the crystal ratio (%) at 165° C. or less, the degree of crystallinity (%), the amorphous amount (%), and the crystal amount at 165° C. or less were calculated from the following formulas.
The heat of fusion of perfect crystals of polypropylene used in the calculation was 209 J/g as described in Macromolecular Chemie, Rapid Communication, Vol. 9, Page 75 (1988).
Crystallinity (%) at 165° C. or less = 100 × heat of fusion ΔH (J/g) at 165° C. or less / heat of fusion ΔH (J/g) of the entire film
Crystallinity (%)=100×heat of fusion of entire film ΔH (J/g)/heat of fusion of completely crystalline polypropylene (209 J/g)
Amorphous amount (%) = 100 - crystallinity (%)
Amount of crystals at 165°C or less (%) = Degree of crystallinity (%) x Crystal ratio at 165°C or less (%) / 100

(8) Small angle X-ray scattering (SAXS) measurement of biaxially stretched polypropylene film For the biaxially stretched polypropylene film of each example, the MD direction of the film was set to the top and bottom, the TD direction was set to the left and right, and the measurement film was set in the following device so that the angle between the X-ray source direction and the film surface was perpendicular. For the TD direction, the TD direction was set to the top and bottom, and the MD direction was set to the left and right, and small angle X-ray scattering (SAXS) measurement was performed with the following device and conditions.
Device: RIGAKU Corporation, product name: Ultima IV (small angle scattering attachment system)
X-ray incidence direction: normal to the film X-ray wavelength: 0.15418 nm
Optical unit specifications:
1. Optical system selection slit: 0.03 mm for small angle scattering (= 1st slit)
2. DS: Anti-scattering slit 1.00 mm (= 2nd slit)
3. Soller slit on the entrance side: 5° flexible optical system used 4. Distance between 1st and 2nd slits: 70 mm
5. 2nd. ~ Sample distance: 98 mm
6. Vacuum path length: 100 mm (installed on a dedicated stand in front of the receiving slit box)
7. RS, SS: scattering slit 0.20 mm, receiving slit 0.10 mm
8. Camera length: 285mm
9. Solar slit on the receiving side: 5° flexible optical system used 10. Monochromatization: None (monochromatization on the incident side by multilayer mirror)
11. Detector: RIGAKU scintillation detector (HV: 762V) (one-dimensional)
X-ray irradiation conditions:
A. Scan axis: 2theta
B. Measurement method: Continuous C. Scan start angle: 0.1°
D. Scan end angle: 1.0°
E. Sampling width: 0.02°
F. Scan speed: 0.5°/min
G. Voltage and current: 40kV-40mA
H. Number of sample stacks: In order to obtain sufficient scattering intensity, the samples were stacked to a thickness of about 0.5 mm with the sample orientation aligned.
The X-ray scattering pattern obtained under the above measurement conditions was subjected to detector background correction and air scattering correction to obtain SAXS profile I(q). The Bragg angle θ was calculated from the magnitude of the scattering vector of the peak derived from the crystal long period in the SAXS profile using the following formula (1), and this was substituted into the following Bragg formula (2) to calculate the crystal long period (d).
q = 4π sin θ / λ (1)
θ: Bragg angle q: magnitude of scattering vector λ: X-ray wavelength 2d sin θ = λ (2)
d: Crystal long period θ: Bragg angle λ: X-ray wavelength Also, referring to the structural analysis of crystalline polymer materials by scattering method in Nichias Technical Times (2014) No. 2 No. 365, the electron density correlation function γ(r) was calculated by Fourier transforming the scattering intensity profile I(q) using the following formula (3). γ(r) has a special property that can be directly used for structural characterization, and the amorphous thickness (da) of the biaxially stretched polypropylene film obtained as structural information was calculated. Also, r indicates distance (nm).

The crystal thickness (dc) was calculated by subtracting the amorphous thickness (da) from the crystal long period (d).

(9) Water vapor permeability The biaxially oriented polypropylene film was folded so that the surface resin layer 1 was on the inner surface, and the two sides were heat-sealed to form a bag. Then, calcium chloride was placed in the bag as the content. Next, the other side was heat-sealed to make a bag with a surface area of 0.01 ^m2 . The obtained bag was then stored for 72 hours under conditions of 40°C and humidity of 90% RH. The mass of calcium chloride was measured before and after storage, and the water vapor permeability (g/( ^m2 ·24h)) was calculated from the difference.

(10) Thermal expansion coefficient and thermal shrinkage coefficient of biaxially oriented polypropylene film at 120 ° C. The thermal expansion coefficient and thermal shrinkage coefficient of the biaxially oriented polypropylene film at 120 ° C. were measured in accordance with JIS C2151:2019.
First, a test piece of 10 cm x 10 cm was cut out from the biaxially oriented polypropylene film. Then, the test piece was heat-treated at 120 ° C for 15 minutes. At this time, the test piece was heated in a hot air circulation type thermostatic chamber (manufactured by ADVANTEC, product name: DRM620DE) while hanging without applying force. Then, the test piece was cooled to room temperature, and the length of the test piece was measured. Next, the length of the test piece in the TD direction after the heat treatment was taken as TD ₁ [cm], and the thermal expansion coefficient [%] in the TD direction was calculated by 100 × (TD ₁ -10) / 10. In addition, the length of the test piece in the MD direction after the heat treatment was taken as MD ₁ [cm], and the thermal shrinkage coefficient [%] in the MD direction was calculated by 100 × (10 - MD ₁ ) / 10. The above measurement was performed three times, and the average values of the obtained measurements were adopted as the thermal expansion coefficient and thermal shrinkage coefficient of the biaxially oriented polypropylene film at 120 ° C., respectively.

(11) Heat shrinkage rate of biaxially oriented polypropylene film at 150°C The heat shrinkage rate of a biaxially oriented polypropylene film at 150°C was measured in accordance with JIS C2151:2019.
First, a test piece of 10 cm x 10 cm was cut out from the biaxially stretched polypropylene film. Then, the test piece was heat-treated at 150 ° C for 15 minutes. At this time, the test piece was heated in a hot air circulation type thermostatic chamber (manufactured by ADVANTEC, product name: DRM620DE) while hanging without applying force. Then, the test piece was cooled to room temperature, and the length of the test piece was measured. Next, when the length of the test piece in the TD direction after the heat treatment was TD ₁ [cm] and the length of the test piece in the MD direction after the heat treatment was MD ₁ [cm], X _TD [%] was calculated by 100 × (10-TD ₁ ) / 10, and X _MD [%] was calculated by 100 × (10-MD ₁ ) / 10. The above measurement was performed three times, and the average value of the obtained measured values was adopted as the heat shrinkage rate of the biaxially stretched polypropylene film at 150 ° C.

(12) Haze The haze of the biaxially stretched polypropylene film was measured in accordance with JIS K7136:2000 using a haze meter (manufactured by Nippon Denshoku Industries Co., Ltd., NDH5000).

(13) Heat fusion strength at 170°C or 200°C Two biaxially oriented polypropylene films cut to a width of 15 mm were heat fused together at the surface resin layer 1 (heat resistant fusion layer) under the conditions of 170°C or 200°C, pressure of 2.0 kgf, and sealing time of 1.0 second to obtain laminated films. Next, the two biaxially oriented polypropylene films were peeled off under the conditions of 15 mm width, 90° peeling, peeling speed of 300 mm/min, and tension in the TD direction, and the peel strength at this time was taken as the heat fusion strength at 170°C or 200°C, respectively.

(14) Bag-making properties (wrinkles when heat-sealed at 180° C.)
Two pieces of biaxially oriented polypropylene film cut to a width of 15 mm were heat-sealed together at the surface resin layer 1 (heat-resistant adhesive layer) at 180° C., pressure of 2.0 kgf, and sealing time of 1.0 second to obtain a laminated film. The presence or absence of heat wrinkles in the sealed portion was then visually observed.

(15) Thermal Dimensional Stability The thermal dimensional stability of the biaxially oriented polypropylene film was evaluated according to the following criteria.
AA (very good): Heat shrinkage rate ( _XMD + _XTD ) at 150°C is less than 6.0%. A (good): Heat shrinkage rate ( _XMD + _XTD ) at 150°C is 6.0% or more and less than 7.0%. B (poor): Heat shrinkage rate ( _XMD + _XTD ) at 150°C is 7.0% or more and less than 10.0%. C (very bad): Heat shrinkage rate ( _XMD + _XTD ) at 150°C is 10.0% or more.

[Examples 1 to 4 and Comparative Example 1]
Polypropylene films having the compositions shown in Table 1 were extruded and then biaxially stretched to produce biaxially stretched polypropylene films, which were then evaluated. The extrusion conditions and biaxial stretching conditions were as follows. The surface of the surface resin layer 2 in Table 1 was subjected to corona treatment.
Extrusion molding machine: 60 mmφ multi-layer T-die extrusion molding machine (screw: L/D=27, manufactured by Screw Seiki Co., Ltd.)
Extrusion temperature setting: 230 to 250°C, processing speed: 20 m/min (winding speed)
Stretching temperature in MD direction [°C]: See Table 1. Stretching ratio in MD direction [times]: See Table 1. Stretching temperature in TD direction [°C]: See Table 1. Stretching ratio in TD direction [times]: See Table 1. Relaxation rate [%]: See Table 1. Here, the relaxation rate refers to the maximum stretching ratio width in the device settings divided by the tenter exit width.
In addition, the notation "A/B/C" for the stretching temperature in Table 1 means "preheating temperature (temperature for heating the original film before stretching)/stretching temperature (temperature during stretching)/heat setting temperature (temperature during heat setting (annealing) after stretching)".

The biaxially oriented polypropylene film of the embodiment had improved thermal dimensional stability compared to the biaxially oriented polypropylene film of the comparative example.

This application claims priority based on Japanese Patent Application Nos. 2022-155359, 2022-155372, 2022-155360, 2022-155365 and 2022-155368, filed on September 28, 2022, the entire disclosures of which are incorporated herein by reference.

The present invention can also take the following forms:

[1a]
A biaxially stretched film layer containing a propylene-based polymer is provided,
A biaxially oriented polypropylene film having a crystal long period in the TD direction of 28.0 nm or less as determined by small angle X-ray scattering (SAXS) measurement.
[2a]
The biaxially oriented polypropylene film according to [1a], wherein the amorphous thickness in the TD direction determined by SAXS measurement is 15.5 nm or less.
[3a]
The biaxially oriented polypropylene film according to [1a] or [2a], wherein the crystal thickness in the TD direction determined by SAXS measurement is 13.5 nm or less.
[4a]
The biaxially oriented polypropylene film according to any one of [1a] to [3a], wherein the amount of structural units derived from α-olefins other than propylene contained in the biaxially oriented polypropylene film is 0.05 mol% or more when the total amount of structural units derived from monomers contained in the biaxially oriented polypropylene film is taken as 100 mol%.
[5a]
The biaxially oriented polypropylene film according to any one of [1a] to [4a], further comprising a surface resin layer on at least one surface of the biaxially oriented film layer.
[6a]
The biaxially oriented polypropylene film according to [5a], wherein the surface resin layer contains homopolypropylene (A).
[7a]
The content of the homopolypropylene (A) in the surface resin layer is 75% by mass or more and 100% by mass or less, when the entire surface resin layer is 100% by mass. The biaxially oriented polypropylene film according to [6a].
[8a]
The biaxially oriented polypropylene film according to any one of [5a] to [7a], wherein the thickness of the surface resin layer is 0.1 μm or more and 10.0 μm or less.
[9a]
The biaxially oriented polypropylene film according to any one of [1a] to [8a], wherein the thickness of the biaxially oriented film layer is 5 μm or more and 100 μm or less.
[10a]
The biaxially oriented polypropylene film according to any one of [1a] to [9a], wherein the sum (T1 + T2) of the tensile modulus _T1 in the MD direction and the tensile modulus T2 in the TD direction of the biaxially oriented polypropylene film, measured in accordance with JIS _K7127 (1999) using a tensile tester under conditions of a measurement temperature of 23± ₂ °C, 50± ₅ % RH, and a tensile speed of 5 mm/min, is 3000 MPa or more and 10000 MPa or less.
[11a]
The biaxially stretched polypropylene film according to any one of [1a] to [10a], which expands in the TD direction when heat-treated at 120 ° C. for 15 minutes in accordance with JIS C2151:2019.
[12a]
The biaxially oriented polypropylene film according to any one of [1a] to [11a], which is a food packaging film.
[13a]
A food packaging material using the biaxially oriented polypropylene film according to any one of [1a] to [12a].
[14a]
The food packaging material according to [13a] above,
and a food product within the food package.

The present invention can also take the following forms:

[1b]
A biaxially stretched film layer containing a propylene-based polymer is provided,
A biaxially oriented polypropylene film that expands in the TD direction and shrinks in the MD direction when heat-treated at 120°C for 15 minutes in accordance with JIS C2151:2019.
[2b]
The biaxially stretched polypropylene film according to [1b], having a thermal expansion coefficient in the TD direction of 0.1% or more and 2.0% or less when heat-treated at 120 ° C. for 15 minutes in accordance with JIS C2151:2019.
[3b]
The biaxially oriented polypropylene film according to [1b] or [2b], having a heat shrinkage rate in the MD direction of 5.0% or less when heat-treated at 120 ° C. for 15 minutes in accordance with JIS C2151:2019.
[4b]
The biaxially stretched polypropylene film according to any one of [1b] to [3b], having a heat shrinkage rate in the TD direction of 8.5% or less when heat-treated at 150 ° C. for 15 minutes in accordance with JIS C2151:2019.
[5b]
The biaxially stretched polypropylene film according to any one of [1b] to [4b], having a heat shrinkage rate in the MD direction of 8.0% or less when heat-treated at 150 ° C. for 15 minutes in accordance with JIS C2151:2019.
[6b]
The biaxially stretched polypropylene film according to any one of [1b] to [5b], wherein when the heat shrinkage in the TD direction and the heat shrinkage in the MD direction are X _TD [%] and X _MD [%], respectively, when heat-treated at 150° C. for 15 minutes in accordance with JIS C2151:2019, X _TD +X _MD is less than 16.0%.
[7b]
The biaxially oriented polypropylene film according to any one of [1b] to [6b], wherein the amount of structural units derived from α-olefins other than propylene contained in the biaxially oriented polypropylene film is 0.05 mol% or more when the total amount of structural units derived from monomers contained in the biaxially oriented polypropylene film is taken as 100 mol%.
[8b]
The biaxially oriented polypropylene film according to any one of [1b] to [7b], further comprising a surface resin layer on at least one surface of the biaxially oriented film layer.
[9b]
The biaxially oriented polypropylene film according to [8b], wherein the surface resin layer contains homopolypropylene (A).
[10b]
The content of the homopolypropylene (A) in the surface resin layer is 75% by mass or more and 100% by mass or less, when the entire surface resin layer is 100% by mass. The biaxially oriented polypropylene film according to [9b].
[11b]
The biaxially oriented polypropylene film according to any one of [8b] to [10b], wherein the thickness of the surface resin layer is 0.1 μm or more and 10.0 μm or less.
[12b]
The biaxially oriented polypropylene film according to any one of [1b] to [11b], wherein the thickness of the biaxially oriented film layer is 5 μm or more and 100 μm or less.
[13b]
The biaxially oriented polypropylene film according to any one of [1b] to [12b], wherein the sum (T1 + T2) of the tensile modulus _T1 in the MD direction and the tensile modulus T2 in the TD direction of the biaxially oriented polypropylene film, measured in accordance with JIS _K7127 (1999) using a tensile tester under conditions of a measurement temperature of 23± ₂ °C, 50± ₅ % RH, and a tensile speed of 5 mm/min, is 3000 MPa or more and 10000 MPa or less.
[14b]
The biaxially oriented polypropylene film according to any one of [1b] to [13b], which is a food packaging film.
[15b]
A food packaging material using the biaxially oriented polypropylene film according to any one of [1b] to [14b] above.
[16b]
The food packaging material according to [15b] above,
and a food product within the food package.

The present invention can also take the following forms:

[1c]
A biaxially oriented polypropylene film having a biaxially oriented film layer containing a propylene-based polymer,
The biaxially oriented polypropylene film has a heat fusion strength of 4.0 N/15 mm or less when the biaxially oriented polypropylene film is heat sealed to itself at 200°C.
[2c]
The biaxially oriented polypropylene film according to [1c], wherein the heat fusion strength when the biaxially oriented polypropylene films are heat-sealed to each other at 170°C is 1.0 N/15 mm or less.
[3c]
The biaxially oriented polypropylene film according to [1c] or [2c], wherein the amount of structural units derived from α-olefins other than propylene contained in the biaxially oriented polypropylene film is 0.05 mol% or more when the total amount of structural units derived from monomers contained in the biaxially oriented polypropylene film is 100 mol%.
[4c]
The biaxially oriented polypropylene film according to any one of [1c] to [3c], further comprising a surface resin layer on at least one surface of the biaxially oriented film layer.
[5c]
The biaxially oriented polypropylene film according to [4c], wherein the surface resin layer contains homopolypropylene (A).
[6c]
The content of the homopolypropylene (A) in the surface resin layer is 75% by mass or more and 100% by mass or less, when the entire surface resin layer is 100% by mass. The biaxially oriented polypropylene film according to [5c].
[7c]
The biaxially oriented polypropylene film according to any one of [4c] to [6c], wherein the thickness of the surface resin layer is 0.1 μm or more and 10.0 μm or less.
[8c]
The biaxially oriented polypropylene film according to any one of [1c] to [7c], wherein the thickness of the biaxially oriented film layer is 5 μm or more and 100 μm or less.
[9c]
The biaxially stretched polypropylene film according to any one of [1c] to [8c], wherein the sum (T1 + T2) of the tensile modulus _T1 in the MD direction and the tensile modulus T2 in the TD direction of the biaxially stretched polypropylene film, measured in accordance with JIS _K7127 (1999) using a tensile tester under conditions of a measurement temperature of 23± ₂ °C, 50± ₅ % RH, and a tensile speed of 5 mm/min, is 3000 MPa or more and 10000 MPa or less.
[10c]
The biaxially oriented polypropylene film according to any one of [1c] to [9c] above, which is a food packaging film.
[11c]
A food packaging material using the biaxially oriented polypropylene film according to any one of [1c] to [10c].
[12c]
The food packaging material according to [11c] above,
and a food product within the food package.

The present invention can also take the following forms:

[1d]
A biaxially oriented polypropylene film having a biaxially oriented film layer containing a propylene-based polymer,
A biaxially oriented polypropylene film, in which the amount of structural units derived from α-olefins other than propylene contained in the biaxially oriented polypropylene film is 0.05 mol % or more and 50.0 mol % or less, when the total amount of structural units derived from monomers contained in the biaxially oriented polypropylene film is taken as 100 mol %.
[2d]
The biaxially oriented polypropylene film according to [1d], wherein the α-olefin other than propylene comprises one or two selected from the group consisting of ethylene and 1-butene.
[3d]
The biaxially oriented polypropylene film according to [1d] or [2d], wherein the amount of structural units derived from α-olefins other than propylene contained in the biaxially oriented polypropylene film is 0.1 mol% or more and 15.0 mol% or less, when the total amount of structural units derived from monomers contained in the biaxially oriented polypropylene film is 100 mol%.
[4d]
The biaxially oriented polypropylene film according to any one of [1d] to [3d], further comprising a surface resin layer on at least one surface of the biaxially oriented film layer.
[5d]
The biaxially oriented polypropylene film according to [4d], wherein the surface resin layer contains homopolypropylene (A).
[6d]
The content of the homopolypropylene (A) in the surface resin layer is 75% by mass or more and 100% by mass or less, when the entire surface resin layer is 100% by mass. The biaxially oriented polypropylene film according to [5d].
[7d]
The biaxially oriented polypropylene film according to any one of [4d] to [6d], wherein the thickness of the surface resin layer is 0.1 μm or more and 10.0 μm or less.
[8d]
The biaxially oriented polypropylene film according to any one of [1d] to [7d], wherein the thickness of the biaxially oriented film layer is 5 μm or more and 100 μm or less.
[9d]
The biaxially oriented polypropylene film according to any one of [1d] to [8d], wherein the sum (T1 + T2) of the tensile modulus _T1 in the MD direction and the tensile modulus T2 in the TD direction of the biaxially oriented polypropylene film, measured in accordance with JIS _K7127 (1999) using a tensile tester under conditions of a measurement temperature of 23± ₂ °C, 50± ₅ % RH, and a tensile speed of 5 mm/min, is 3000 MPa or more and 10000 MPa or less.
[10d]
The biaxially stretched polypropylene film according to any one of [1d] to [9d], which expands in the TD direction when heat-treated at 120 ° C. for 15 minutes in accordance with JIS C2151:2019.
[11d]
The biaxially oriented polypropylene film according to any one of [1d] to [10d] above, which is a food packaging film.
[12d]
A food packaging material using the biaxially oriented polypropylene film according to any one of [1d] to [11d].
[13d]
The food packaging material according to [12d] above,
and a food product within the food package.

100 Biaxially oriented polypropylene film 101 Biaxially oriented film layer 103 Surface resin layer

Claims

A biaxially stretched film layer containing a propylene-based polymer is provided,
A biaxially oriented polypropylene film having a crystallinity of 38% or more at 165°C or less as determined by differential scanning calorimetry.
The biaxially oriented polypropylene film according to claim 1, wherein the main melting point of the biaxially oriented polypropylene film is 165°C or higher and 180°C or lower, as determined by differential scanning calorimetry.
The biaxially oriented polypropylene film according to claim 1 or 2, wherein the heat of fusion (ΔH) of the entire biaxially oriented polypropylene film, as determined by differential scanning calorimetry, is 100 J/g or more and 150 J/g or less.
The biaxially oriented polypropylene film according to any one of claims 1 to 3, wherein the heat of fusion (ΔH) of the biaxially oriented polypropylene film at 165°C or less, as determined by differential scanning calorimetry, is 40 J/g or more.
The biaxially oriented polypropylene film according to any one of claims 1 to 4, wherein the amount of crystals of the biaxially oriented polypropylene film at 165°C or less is 20% or more.
The biaxially oriented polypropylene film according to any one of claims 1 to 5, wherein the amount of structural units derived from α-olefins other than propylene contained in the biaxially oriented polypropylene film is 0.05 mol% or more when the total amount of structural units derived from monomers contained in the biaxially oriented polypropylene film is taken as 100 mol%.
The biaxially oriented polypropylene film according to any one of claims 1 to 6, wherein the amount of structural units derived from α-olefins other than propylene contained in the biaxially oriented polypropylene film is 0.05 mol% or more and 50.0 mol% or less when the total amount of structural units derived from monomers contained in the biaxially oriented polypropylene film is taken as 100 mol%.
The biaxially oriented polypropylene film according to claim 6 or 7, wherein the α-olefin other than propylene includes one or two selected from the group consisting of ethylene and 1-butene.
The biaxially stretched polypropylene film according to any one of claims 6 to 8, wherein the amount of structural units derived from α-olefins other than propylene contained in the biaxially stretched polypropylene film is 0.1 mol% or more and 15.0 mol% or less when the total amount of structural units derived from monomers contained in the biaxially stretched polypropylene film is taken as 100 mol%.
A biaxially oriented polypropylene film according to any one of claims 1 to 9, in which the crystal long period in the TD direction determined by small angle X-ray scattering (SAXS) measurement is 28.0 nm or less.
The biaxially oriented polypropylene film according to any one of claims 1 to 10, in which the amorphous thickness in the TD direction determined by SAXS measurement is 15.5 nm or less.
A biaxially oriented polypropylene film according to any one of claims 1 to 11, in which the crystal thickness in the TD direction determined by SAXS measurement is 13.5 nm or less.
A biaxially oriented polypropylene film according to any one of claims 1 to 12, which expands in the TD direction when heat-treated at 120°C for 15 minutes in accordance with JIS C2151:2019.
The biaxially oriented polypropylene film according to any one of claims 1 to 13, which expands in the TD direction and shrinks in the MD direction when heat-treated at 120°C for 15 minutes in accordance with JIS C2151:2019.
A biaxially oriented polypropylene film according to any one of claims 1 to 14, which has a thermal expansion coefficient in the TD direction of 0.1% or more and 2.0% or less when heat-treated at 120°C for 15 minutes in accordance with JIS C2151:2019.
A biaxially oriented polypropylene film according to any one of claims 1 to 15, which has a thermal shrinkage rate in the MD direction of 5.0% or less when heat-treated at 120°C for 15 minutes in accordance with JIS C2151:2019.
A biaxially oriented polypropylene film according to any one of claims 1 to 16, which has a thermal shrinkage rate in the TD direction of 8.5% or less when heat-treated at 150°C for 15 minutes in accordance with JIS C2151:2019.
A biaxially oriented polypropylene film according to any one of claims 1 to 17, which has a thermal shrinkage rate in the MD direction of 8.0% or less when heat-treated at 150°C for 15 minutes in accordance with JIS C2151:2019.
The biaxially stretched polypropylene film according to any one of claims 1 to 18, wherein the heat shrinkage in the TD direction and the heat shrinkage in the MD direction when heat-treated at 150°C for 15 minutes in accordance with JIS C2151:2019 are XTD [%] and XMD [%], respectively, and XTD + XMD is less than 7.0%.
The biaxially oriented polypropylene film according to any one of claims 1 to 19, wherein the heat fusion strength when the biaxially oriented polypropylene films are heat sealed together at 200°C is 4.0 N/15 mm or less.
The biaxially oriented polypropylene film according to any one of claims 1 to 20, wherein the heat fusion strength when the biaxially oriented polypropylene films are heat sealed together at 170°C is 1.0 N/15 mm or less.
The biaxially oriented polypropylene film according to any one of claims 1 to 21, further comprising a surface resin layer on at least one side of the biaxially oriented film layer.
The biaxially oriented polypropylene film according to claim 22, wherein the surface resin layer contains homopolypropylene (A).
The biaxially oriented polypropylene film according to claim 23, wherein the content of the homopolypropylene (A) in the surface resin layer is 75% by mass or more and 100% by mass or less, when the entire surface resin layer is taken as 100% by mass.
The biaxially oriented polypropylene film according to any one of claims 22 to 24, wherein the thickness of the surface resin layer is 0.1 μm or more and 10.0 μm or less.
The biaxially oriented polypropylene film according to any one of claims 1 to 25, wherein the thickness of the biaxially oriented film layer is 5 μm or more and 100 μm or less.
The biaxially oriented polypropylene film according to any one of claims 1 to 26, wherein the sum (T1 + T2) of the tensile modulus T1 in the MD direction and the tensile modulus T2 in the TD direction of the biaxially oriented polypropylene film, measured in accordance with JIS K7127 (1999) using a tensile tester under conditions of a measurement temperature of 23± 2 °C, 50± 5 % RH, and a tensile speed of 5 mm/min, is 3000 MPa or more and 10000 MPa or less.
The biaxially oriented polypropylene film according to any one of claims 1 to 27, which is a food packaging film.
Food packaging using the biaxially oriented polypropylene film according to any one of claims 1 to 28.
The food packaging body according to claim 29,
and a food product within the food package.