JP2024065134A - Sheet or film - Google Patents

Abstract

To provide a sheet or film that is resistant to blocking.SOLUTION: A sheet or film according to the present invention is composed of a composition which contains: (A) polymers that include one or more polymers that are selected from the group consisting of (A1) 4-methyl-1-pentene polymers and (A2) styrene elastomers; and (B) a silylated polyolefin.SELECTED DRAWING: None

Description

The present invention relates to a sheet or film.

Generally, sheets or films formed from polymers are prone to blocking (a phenomenon in which solid surfaces come into close contact with each other, making the materials continuous with each other), which, for example, makes it impossible to unwind a roll of sheet material (a sheet that has been wound into a roll). In addition, when cutting overlapping sheets, blocking occurs between the sheets due to pressure bonding during cutting, and the sheets stick together and cannot be peeled off. This has been a problem for a long time, and various measures have been taken.
As a method for suppressing the above-mentioned blocking, for example, there is a method of mixing an antiblocking agent (anti-adhesive agent) with the olefin copolymer (Patent Documents 1 and 2).

As such a method, Patent Document 1 discloses a polyolefin resin composition for sheets in which silica and zeolite are added to an olefin copolymer.
Patent Document 2 discloses a polyethylene resin composition in which an alkylene bis-saturated higher fatty acid amide is added to an olefin copolymer, and a sheet and a film using the same.

Japanese Patent Application Laid-Open No. 04-220443 Japanese Patent Application Laid-Open No. 08-269268

As a result of the inventor's investigation, it became clear that even the method of adding the above-mentioned antiblocking agent was insufficient in suppressing blocking of the sheet or film.

This embodiment was made in consideration of the above circumstances, and provides a sheet or film in which blocking is suppressed.

The present inventors have conducted extensive research to solve the above problems. As a result, they have discovered that by blending a silylated polyolefin with a specific polymer, a sheet or film in which blocking is suppressed can be obtained, and have completed this embodiment.

That is, according to this embodiment, the following sheets or films are provided:

（前記一般式（１）において、Ａ^１、Ａ^２およびＡ^３は各々独立に、ポリオレフィン鎖または炭素数１～２０の炭化水素基である。Ｒは炭素数１～２０の炭化水素基である。各Ｒは同一でも異なっていてもよい。ｍは１～１０，０００の整数である。Ａ^３が複数存在する場合、各Ａ^３は同一でも異なっていてもよい。ただし、Ａ^１、Ａ^２、Ａ^３のうち、少なくとも１つはポリオレフィン鎖を表す。）
［７］ 前記重合体（Ａ）１００質量部に対し、前記シリル化ポリオレフィン（Ｂ）を０．５～１０質量部の割合で含む、［１］～［６］のいずれかに記載のシートまたはフィルム。
［８］ ［１］～［７］のいずれかに記載のシートまたはフィルム（Ｌ１）と、
熱可塑性エラストマーを含む層からなるシートまたはフィルム（Ｌ２）と、
が積層された、積層体。
［９］ 前記シートまたはフィルム（Ｌ１）は、
４－メチル－１－ペンテンに由来する構成単位（ａ１）と、前記４－メチル－１－ペンテン以外の炭素数２～２０のα－オレフィンに由来する構成単位（ａ２）とが合計で１００モル％である共重合体を含み、
前記共重合体は、構成単位（ａ１）を６０モル％～９９モル％、及び構成単位（ａ２）を１モル％～４０モル％含む、［８］に記載の積層体。
［１０］ 前記シートまたはフィルム（Ｌ１）と前記シートまたはフィルム（Ｌ２）とが合計で３層以上積層されており、
少なくとも一方の外層がシートまたはフィルム（Ｌ１）である、［９］又は［１０］に記載の積層体。
［１１］ 前記シートまたはフィルム（Ｌ１）は、前記重合体（Ａ）として４－メチル－１－ペンテン系重合体（Ａ１）のみを含み、
前記シートまたはフィルム（Ｌ２）は、前記熱可塑性エラストマーとしてスチレン系エラストマーを含む、［８］～［１０］のいずれかに記載の積層体。
［１２］ 最外層に位置する前記シートまたはフィルム（Ｌ１）の動的粘弾性の温度依存性を測定して得られる損失正接ｔａｎδの最大値は、０℃～５０℃の温度範囲において０．６以上である、［８］～［１１］のいずれかに記載の積層体。 [1] A polymer (A) containing one or more polymers selected from the group consisting of a 4-methyl-1-pentene polymer (A1) and a styrene elastomer (A2); and a silylated polyolefin (B);
A sheet or film comprising a composition comprising:
[2] The sheet or film according to [1], wherein the maximum value of loss tangent tan δ obtained by measuring the temperature dependence of dynamic viscoelasticity of the sheet or film is 0.6 or more in a temperature range of 0°C to 50°C.
[3] the 4-methyl-1-pentene polymer (A1) contains 100 mol % in total of the structural units (a1) derived from 4-methyl-1-pentene and the structural units (a2) derived from an α-olefin having 2 to 20 carbon atoms other than 4-methyl-1-pentene,
The sheet or film according to [1] or [2], comprising 60 mol % to 99 mol % of the structural unit (a1) and 1 mol % to 40 mol % of the structural unit (a2).
[4] The styrene-based elastomer (A2) includes a hydrogenated styrene-based elastomer,
The sheet or film according to any one of [1] to [3], wherein a ratio of monomer units derived from styrene in 100% by mass of the hydrogenated styrene-based elastomer is 5% by mass to 80% by mass.
[5] The polymer (A) includes a copolymer in which the structural units (a1) derived from 4-methyl-1-pentene and the structural units (a2) derived from an α-olefin having 2 to 20 carbon atoms other than 4-methyl-1-pentene account for 100 mol % in total,
The copolymer contains 60 mol% to 99 mol% of the structural unit (a1) and 1 mol% to 40 mol% of the structural unit (a2).
[6] The sheet or film according to any one of [1] to [5], wherein the silylated polyolefin (B) contains a silylated polyolefin represented by the following general formula (1):

(In the general formula (1), A ¹ , A ² and A ³ each independently represent a polyolefin chain or a hydrocarbon group having 1 to 20 carbon atoms. R represents a hydrocarbon group having 1 to 20 carbon atoms. Each R may be the same or different. m represents an integer of 1 to 10,000. When a plurality of A ³ 's are present, each A ³ 's may be the same or different. However, at least one of A ¹ , A ² and A ³ 's represents a polyolefin chain.)
[7] The sheet or film according to any one of [1] to [6], containing the silylated polyolefin (B) in a ratio of 0.5 to 10 parts by mass per 100 parts by mass of the polymer (A).
[8] A sheet or film (L1) according to any one of [1] to [7],
A sheet or film (L2) consisting of a layer containing a thermoplastic elastomer;
A laminate in which the above-mentioned are stacked.
[9] The sheet or film (L1)
a copolymer in which the total amount of the structural unit (a1) derived from 4-methyl-1-pentene and the structural unit (a2) derived from an α-olefin having 2 to 20 carbon atoms other than 4-methyl-1-pentene is 100 mol %,
The laminate according to [8], wherein the copolymer contains 60 mol % to 99 mol % of the structural unit (a1) and 1 mol % to 40 mol % of the structural unit (a2).
[10] The sheet or film (L1) and the sheet or film (L2) are laminated in a total of three or more layers,
The laminate according to [9] or [10], wherein at least one outer layer is a sheet or film (L1).
[11] The sheet or film (L1) contains only a 4-methyl-1-pentene polymer (A1) as the polymer (A),
The laminate according to any one of [8] to [10], wherein the sheet or film (L2) contains a styrene-based elastomer as the thermoplastic elastomer.
[12] The laminate according to any one of [8] to [11], wherein the maximum value of loss tangent tanδ obtained by measuring the temperature dependence of dynamic viscoelasticity of the sheet or film (L1) located in the outermost layer is 0.6 or more in a temperature range of 0° C. to 50° C.

According to this embodiment, it is possible to provide a sheet or film in which blocking is suppressed.

The sheet or film according to this embodiment will be described in detail below, but the present invention is not limited to the following embodiment, and can be modified as appropriate within the scope of the purpose of this embodiment. In this embodiment, a numerical range expressed using "~" means a range in which the numerical values before and after "~" are the lower and upper limits, for example, "1 part by mass to 10 parts by mass" means "1 part by mass or more and 10 parts by mass or less." In the numerical ranges described in stages in this embodiment, the upper or lower limit value described in a certain numerical range may be replaced with the upper or lower limit value of another numerical range described in stages, that is, the upper and lower limits can be arbitrarily combined. In addition, the upper or lower limit value of the numerical range described in this embodiment may be replaced with the value shown in the example.

<Sheet or film>
The sheet or film according to this embodiment (hereinafter, may be simply referred to as a sheet) is made of a composition containing a polymer (A) containing one or more polymers selected from the group consisting of a 4-methyl-1-pentene polymer (A1) and a styrene elastomer (A2), and a silylated polyolefin (B).

Silica, zeolite, etc., which are generally used as antiblocking agents, have low affinity with olefin-based polymers, so that the antiblocking agent located on the surface of the resin composition may be detached from the resin composition over time or may be buried inside the sheet when surface pressure is applied, so that blocking is likely to occur over time, and the transparency of the sheet tends to decrease when added to the polymer (A). In addition, higher fatty acids tend to bleed out to the surface and be lost from the sheet surface over time, so that the blocking effect tends to decrease over time, and it may be necessary to increase the amount added to continue to exhibit the effect. However, in that case, there is a problem that the characteristics and physical properties of other polymers are deteriorated. In addition, if the amount of higher fatty acid added is large, the sheet is likely to become sticky, which may impair the surface quality.
On the other hand, the silylated polyolefin (B) used in the present embodiment has high affinity with the polymer (A) and has a large effect of suppressing the occurrence of blocking, and therefore, by adding an appropriate amount, the occurrence of blocking can be suppressed for a long period of time.

The present inventors presume that the olefin resin composition containing the polymer (A) and the silylated polyolefin (B) has a high surface silicon concentration and suppresses the surface free energy, thereby suppressing the occurrence of blocking.
The highly polar silyl groups have low affinity with the polymer (A) and are therefore arranged outward on the surface of the sheet or film, and the olefin moiety of the silylated polyolefin (B) has high affinity with the polymer (A), so that the olefin moiety interacts with the polymer (A), which makes it difficult for the silylated polyolefin (B) to fall off from the surface of the sheet or film, and as a result, the present inventors presume that this suppresses the occurrence of blocking in the sheet or film containing the polymer (A).
Furthermore, compared with conventional antiblocking agents, the silylated polyolefin (B) is more likely to be present uniformly on the surface of the sheet or film, and the inventors presume that this suppresses the occurrence of blocking over the entire surface of the sheet or film.

In the sheet or film according to the present embodiment, from the viewpoint of further suppressing occurrence of blocking, the amount of the silylated polyolefin (B) is preferably 0.5 parts by mass or more, more preferably 1 part by mass or more, and even more preferably 1.5 parts by mass or more, relative to 100 parts by mass of the polymer (A). Also, from the viewpoint of maintaining moldability, compatibility with other polymers, strength, and transparency, the amount is preferably 10 parts by mass or less, more preferably 7 parts by mass or less, and even more preferably 5 parts by mass or less.
That is, in this embodiment, the amount of the silylated polyolefin (B) can be preferably 0.5 parts by mass to 10 parts by mass, more preferably 1 part by mass to 7 parts by mass, and even more preferably 1.5 parts by mass to 5 parts by mass, per 100 parts by mass of the polymer (A). By setting the amount of the silylated polyolefin added within the above range, the tensile strength at break, tensile elongation at break, and transparency can be improved.

In the sheet or film according to this embodiment, the total content of the polymer (A) and the silylated polyolefin (B) is, from the viewpoint of the effect of this embodiment, preferably 0.1% by mass or more, more preferably 0.5% by mass or more, and even more preferably 1% by mass or more, when the entire sheet is taken as 100% by mass.

The thickness of the sheet or film according to this embodiment is preferably 0.01 mm to 5 mm, more preferably 0.03 mm to 2 mm, even more preferably 0.05 mm to 1.5 mm, particularly preferably 0.1 mm to 1.0 mm, and extremely preferably 0.1 mm to 0.8 mm.
When the thickness is equal to or greater than the lower limit, the strength of the sheet or film can be improved. When the thickness is equal to or less than the upper limit, the flexibility of the sheet or film can be easily maintained. That is, when the thickness of the sheet or film is within the above range, the balance between the strength and flexibility of the sheet or film is excellent.

The components that make up the sheet or film according to this embodiment are described below.

<Polymer (A)>
The polymer (A) according to this embodiment is at least one polymer selected from the group consisting of a 4-methyl-1-pentene polymer (A1) and a styrene elastomer (A2).

<4-Methyl-1-pentene Polymer (A1)>
The 4-methyl-1-pentene polymer (A1) according to this embodiment contains a structural unit (a1) derived from 4-methyl-1-pentene (hereinafter, may be referred to as "4MP1 unit (a1)").

When the 4-methyl-1-pentene polymer (A1) contains 60 mol % or more of 4MP1 units (a1), the polymer can be made into a sheet or film in which occurrence of blocking is effectively suppressed by adding the silylated polyolefin (B). When the 4-methyl-1-pentene polymer (A1) contains 99 mol % or less of 4MP1 units (a1), the polymer can be made into a sheet or film having good mechanical properties such as elongation.
That is, the 4-methyl-1-pentene polymer (A1) can have 4MP1 units (a1) in an amount of preferably 60 mol% to 99 mol%, more preferably 65 mol% to 98 mol%, and even more preferably 65 mol% to 97 mol%. By containing 4MP1 units (a1) in the above-mentioned numerical range, occurrence of blocking is effectively suppressed, and a sheet or film having good mechanical properties such as elongation can be obtained, in other words, a sheet or film having a good balance of these effects can be obtained.

The 4-methyl-1-pentene polymer (A1) further contains a structural unit (a2) (hereinafter sometimes referred to as "AO unit (a2)") derived from an α-olefin having 2 to 20 carbon atoms other than 4-methyl-1-pentene.
The 4-methyl-1-pentene polymer (A1) may contain the structural unit (a2) in an amount of preferably 1 mol % to 40 mol %, more preferably 2 mol % to 35 mol %, and further preferably 3 mol % to 35 mol %. When the AO unit (a2) contained in the 4-methyl-1-pentene polymer (A1) is within the above range, the occurrence of blocking can be effectively suppressed by adding the silylated polyolefin (B).

In this embodiment, the 4-methyl-1-pentene polymer (A1) preferably contains 4MP1 units (a1) and AO units (a2) in total of 100 mol%, and preferably contains 4MP1 units (a1) in an amount of 60 mol% to 99 mol%, more preferably 65 mol% to 98 mol%, and even more preferably 65 mol% to 97 mol%, and preferably contains AO units (a2) in an amount of 1 mol% to 40 mol%, more preferably 2 mol% to 35 mol%, and even more preferably 3 mol% to 35 mol%. This provides the sheet or film of this embodiment with even better mechanical properties such as elongation.

Examples of the α-olefin having 2 to 20 carbon atoms include linear or branched α-olefins, cyclic olefins, aromatic vinyl compounds, conjugated dienes, non-conjugated polyenes, functionalized vinyl compounds, and the like.
Examples of linear or branched α-olefins include linear α-olefins having 2 to 20 carbon atoms (preferably 2 to 10), such as ethylene, propylene, 1-butene, 1-pentene, 1-hexene, 1-octene, 1-decene, 1-dodecene, 1-tetradecene, 1-hexadecene, 1-octadecene, and 1-eicosene; and branched α-olefins having preferably 5 to 20 carbon atoms (more preferably 5 to 10), such as 3-methyl-1-butene, 3-methyl-1-pentene, 3-ethyl-1-pentene, 4,4-dimethyl-1-pentene, 4-methyl-1-hexene, 4,4-dimethyl-1-hexene, 4-ethyl-1-hexene, and 3-ethyl-1-hexene.

Examples of cyclic olefins include compounds having 4 to 20 carbon atoms (preferably 5 to 15 carbon atoms), such as cyclopentene, cycloheptene, norbornene, 5-methyl-2-norbornene, tetracyclododecene, vinylnorbornene, and vinylcyclohexane.

Examples of aromatic vinyl compounds include styrene; mono- or polyalkylstyrenes such as α-methylstyrene, o-methylstyrene, m-methylstyrene, p-methylstyrene, o,p-dimethylstyrene, o-ethylstyrene, m-ethylstyrene, and p-ethylstyrene.

Examples of conjugated dienes include compounds having 4 to 20 carbon atoms (preferably 4 to 10 carbon atoms), such as 1,3-butadiene, isoprene, chloroprene, 1,3-pentadiene, 2,3-dimethylbutadiene, 4-methyl-1,3-pentadiene, 1,3-hexadiene, and 1,3-octadiene.

Examples of non-conjugated polyenes include 1,4-pentadiene, 1,4-hexadiene, 1,5-hexadiene, 1,4-octadiene, 1,5-octadiene, 1,6-octadiene, 1,7-octadiene, 2-methyl-1,5-hexadiene, 6-methyl-1,5-heptadiene, 7-methyl-1,6-octadiene, 4-ethylidene-8-methyl-1,7-nonadiene, 4,8-dimethyl-1,4,8-decatriene (DMDT), dicyclopentadiene, cyclohexadiene, Examples of compounds having 5 to 20 carbon atoms (preferably 5 to 10) include dicyclooctadiene, methylenenorbornene, 5-vinylnorbornene, 5-ethylidene-2-norbornene, 5-methylene-2-norbornene, 5-isopropylidene-2-norbornene, 6-chloromethyl-5-isopropenyl-2-norbornene, 2,3-diisopropylidene-5-norbornene, 2-ethylidene-3-isopropylidene-5-norbornene, and 2-propenyl-2,2-norbornadiene.

Examples of functionalized vinyl compounds include hydroxyl group-containing olefins; halogenated olefins; unsaturated carboxylic acids such as acrylic acid, propionic acid, 3-butenoic acid, 4-pentenoic acid, 5-hexenoic acid, 6-heptenoic acid, 7-octenoic acid, 8-nonenoic acid, and 9-decenoic acid; unsaturated amines such as allylamine, 5-hexenamine, and 6-heptenamine; unsaturated acid anhydrides such as (2,7-octadienyl)succinic anhydride, pentapropenylsuccinic anhydride, and the anhydrides of the above unsaturated carboxylic acids; halides of the above unsaturated carboxylic acids; and unsaturated epoxy compounds such as 4-epoxy-1-butene, 5-epoxy-1-pentene, 6-epoxy-1-hexene, 7-epoxy-1-heptene, 8-epoxy-1-octene, 9-epoxy-1-nonene, 10-epoxy-1-decene, and 11-epoxy-1-undecene.

The hydroxyl-containing olefin is not particularly limited as long as it is an olefin-based compound having a hydroxyl group, but is preferably a terminally hydroxylated olefin compound.
Examples of the terminally hydroxylated olefin compounds include linear hydroxylated α-olefins having 4 to 20 carbon atoms (preferably 2 to 10), such as vinyl alcohol, allyl alcohol, 1-butene hydroxide, 1-pentene hydroxide, 1-hexene hydroxide, 1-octene hydroxide, 1-decene hydroxide, 1-dodecene hydroxide, 1-tetradecene hydroxide, 1-hexadecene hydroxide, 1-octadecene hydroxide, and 1-eicosene hydroxide; and branched hydroxylated α-olefins preferably having 5 to 20 carbon atoms (more preferably 5 to 10), such as 1-butene, 4-methyl-1-pentene hydroxide, 3-methyl-1-pentene hydroxide, 3-ethyl-1-pentene hydroxide, 4,4-dimethyl-1-pentene hydroxide, 4-methyl-1-hexene hydroxide, 4,4-dimethyl-1-hexene hydroxide, 4-ethyl-1-hexene hydroxide, and 3-ethyl-1-hexene hydroxide.
Examples of halogenated olefins include linear halogenated α-olefins having 4 to 20 carbon atoms (preferably 4 to 10), such as halogenated 1-butene, halogenated 1-pentene, halogenated 1-hexene, halogenated 1-octene, halogenated 1-decene, halogenated 1-dodecene, halogenated 1-tetradecene, halogenated 1-hexadecene, halogenated 1-octadecene, and halogenated 1-eicosene; halogenated 3-methyl-1-butene; and branched halogenated α-olefins having 5 to 20 carbon atoms (more preferably 5 to 10), such as halogenated 4-methyl-1-pentene, halogenated 3-methyl-1-pentene, halogenated 3-ethyl-1-pentene, halogenated 4,4-dimethyl-1-pentene, halogenated 4-methyl-1-hexene, halogenated 4,4-dimethyl-1-hexene, halogenated 4-ethyl-1-hexene, and halogenated 3-ethyl-1-hexene.

The 4-methyl-1-pentene polymer (A1) may contain only one type of AO unit (a2), or may contain two or more types.

As the α-olefin having 2 to 20 carbon atoms other than 4-methyl-1-pentene, from the viewpoint of controlling the copolymerizability and the physical properties of the resulting copolymer, particularly the melting point, at least one selected from the group consisting of ethylene, propylene, 1-butene, 1-pentene, 1-hexene, 1-heptene, 1-octene, 1-nonene, 1-decene, 1-hexadecene, and 1-octadecene is preferred, at least one selected from the group consisting of ethylene, propylene, 1-butene, 1-hexene, and 1-octene is more preferred, at least one selected from the group consisting of ethylene, propylene, and 1-butene is even more preferred, ethylene and propylene are particularly preferred, and propylene is extremely preferred.

The contents (mol %) of the 4MP1 units (a1) and the AO units (a2) in the 4-methyl-1-pentene polymer (A1) can be measured by the following method.
～Conditions～
Measurement device: Nuclear magnetic resonance device (ECP500 type, manufactured by JEOL Ltd.)
Observed nucleus: ^13C (125MHz)
Sequence: Single pulse proton decoupling Pulse width: 4.7 μs (45° pulse)
Repeat time: 5.5 seconds. Accumulation count: 10,000 times or more. Solvent: orthodichlorobenzene/deuterated benzene (volume ratio: 80/20) mixed solvent. Sample concentration: 55 mg/0.6 mL.
Measurement temperature: 120°C
Chemical shift reference value: 27.50 ppm

The 4-methyl-1-pentene polymer (A1) is preferably a copolymer in which the 4MP1 unit (a1) and the AO unit (a2) account for 100 mol % in total. In other words, the 4-methyl-1-pentene polymer (A1) preferably does not contain any other structural units than the 4MP1 unit (a1) and the AO unit (a2).

The 4-methyl-1-pentene polymer (A1) preferably has an intrinsic viscosity [η] of 0.5 dl/g to 5.0 dl/g, more preferably 0.5 dl/g to 4.0 dl/g, measured in a decalin solvent at 135° C. When the intrinsic viscosity [η] of the 4-methyl-1-pentene polymer (A1) is within the above range, the amount of low molecular weight components is small, so that the stickiness of the sheet or film is reduced, and extrusion film molding is possible.
The intrinsic viscosity [η] of the 4-methyl-1-pentene polymer (A1) is a value measured by the following method using an Ubbelohde viscometer.

About 20 mg of 4-methyl-1-pentene polymer (A1) is dissolved in 25 ml of decalin, and the specific viscosity ηsp is measured using an Ubbelohde viscometer in an oil bath at 135° C. The decalin solution is diluted with 5 ml of decalin, and the specific viscosity ηsp is measured in the same manner as above. This dilution procedure is repeated two more times, and the value of ηsp/C when the concentration (C) is extrapolated to 0 is calculated as the limiting viscosity [η] (unit: dl/g) (see Equation 1 below).
[η] = lim (ηsp / C) (C → 0) ... Equation 1

The weight average molecular weight (Mw) of the 4-methyl-1-pentene polymer (A1) is preferably from 1×10 ⁴ to 2×10 ⁶ , and more preferably from 1×10 ⁴ to 1×10 ⁶ , from the viewpoint of film formability.
The molecular weight distribution (Mw/Mn) of the 4-methyl-1-pentene polymer (A1) is preferably from 1.0 to 3.5, and more preferably from 1.1 to 3.0, in order to effectively suppress the occurrence of blocking.
The weight average molecular weight (Mw) and the molecular weight distribution (Mw/Mn) represented by the ratio of the weight average molecular weight (Mw) to the number average molecular weight (Mn) of the 4-methyl-1-pentene polymer (A1) are values calculated by a standard polystyrene conversion method using gel permeation chromatography (GPC) described below.

～Conditions～
Measurement device: GPC (ALC/GPC 150-C plus type, differential refractometer detector integrated type, manufactured by Waters)
Column: 2 GMH6-HT (manufactured by Tosoh Corporation) and 2 GMH6-HTL (manufactured by Tosoh Corporation) connected in series Eluent: o-dichlorobenzene Column temperature: 140°C
Flow rate: 1.0 mL/min

From the viewpoint of fluidity during molding, the melt flow rate (MFR) of the 4-methyl-1-pentene polymer (A1) is preferably 0.1 g/10 min to 100 g/10 min, more preferably 0.5 g/10 min to 50 g/10 min, and even more preferably 0.5 g/10 min to 30 g/10 min.

When the melt flow rate (MFR) of the 4-methyl-1-pentene polymer (A1) is within the above range, it is easy to extrude the polymer to a relatively uniform thickness.
The melt flow rate (MFR) of the 4-methyl-1-pentene polymer (A1) is a value measured at 230° C. under a load of 2.16 kg in accordance with ASTM D1238.

The density of the 4-methyl-1-pentene polymer (A1), measured in accordance with ASTM D 1505 (water displacement method), is preferably 0.810 g/cm ³ to 0.850 g/cm ³ , more preferably 0.820 g/cm ³ to 0.850 g/cm ³ , and even more preferably 0.830 g/cm ³ to 0.850 g/cm ³ , from the viewpoint of handleability.

In addition, when the density of the 4-methyl-1-pentene polymer (A1) is 0.810 g/ ^cm3 or more, the mechanical strength is good. When the density of the 4-methyl-1-pentene polymer (A1) is 0.850 g/ ^cm3 or less, the occurrence of blocking can be effectively suppressed by adding the silylated polyolefin (B).

The melting point (Tm) of the 4-methyl-1-pentene polymer (A1) is 199° C. or lower, or is substantially unobservable. When the melting point (Tm) of the 4-methyl-1-pentene polymer (A1) is 199° C. or lower, or is substantially unobservable, a film that can be molded at low temperatures can be obtained. The melting point (Tm) of the 4-methyl-1-pentene polymer (A1) is preferably 100° C. to 180° C., or is substantially unobservable.
The phrase "substantially no melting point (Tm) is observed" means that no crystal melting peak having a heat of crystal melting of 1 J/g or more is observed in the range of -150°C to 200°C.
The melting point (Tm) of the 4-methyl-1-pentene polymer (A1) is a value measured by the following method using a differential scanning calorimetry (DSC).

Approximately 5 mg of 4-methyl-1-pentene polymer (A1) is sealed in an aluminum pan for measurement of a differential scanning calorimeter (DSC220C type) manufactured by Seiko Instruments Inc. and heated from room temperature to 200°C at 10°C/min. In order to completely melt the 4-methyl-1-pentene polymer (A1), it is held at 200°C for 5 minutes and then cooled to -50°C at 10°C/min. After leaving it at -50°C for 5 minutes, it is heated a second time to 200°C at 10°C/min, and the peak temperature (°C) at this second heating is taken as the melting point (Tm) of the copolymer. Note that if multiple peaks are detected, the peak detected on the highest temperature side is used.

The 4-methyl-1-pentene polymer (A1) can be produced by various methods. For example, it can be produced using known catalysts such as magnesium-supported titanium catalysts; metallocene catalysts described in WO 01/53369, WO 01/027124, JP-A 3-193796, and JP-A 02-41303; and olefin polymerization catalysts containing a metallocene compound described in WO 2011/055803.

The content of the 4-methyl-1-pentene copolymer (A1) in the sheet according to this embodiment is preferably 10 parts by mass to 90 parts by mass, more preferably 20 parts by mass to 80 parts by mass, and even more preferably 30 parts by mass to 70 parts by mass, relative to 100 parts by mass in total of the 4-methyl-1-pentene copolymer (A1) and the styrene-based elastomer (A2) described below.

<Styrene-based elastomer (A2)>
The styrene-based elastomer (A2) is an elastomer containing styrene as a monomer unit. The proportion of the monomer units derived from styrene in the styrene-based elastomer may be 5% by mass or more, or 10% by mass or more, and may be 80% by mass or less, 30% by mass or less, or 20% by mass or less, based on the total mass of the styrene-based elastomer. That is, the proportion of the monomer units derived from styrene is preferably 5% by mass to 80% by mass, more preferably 5% by mass to 30% by mass, even more preferably 5% by mass to 20% by mass, and particularly preferably 10% by mass to 20% by mass.
The styrene-based elastomer may be a hydrogenated product in which a part or all of the unsaturated bonds derived from the alkadiene monomer or the like (usually excluding the unsaturated bonds in the benzene ring derived from styrene) are converted to saturated bonds by hydrogenation. Hydrogenation tends to improve heat resistance.

The styrene-based elastomer (A2) may be, for example, a block copolymer composed of a polystyrene block and a polyolefin block consisting of monomer units derived from an alkadiene having 4 to 10 carbon atoms, or a hydrogenated product thereof. From the viewpoints of compatibility with the propylene-based polymer and impact resistance, the polyolefin block may contain at least one alkadiene of isoprene or butadiene as a monomer unit. In this specification, elastomers containing styrene and ethylene as monomer units are classified as styrene-based elastomers.
The styrene elastomer (A2) may be a diblock type copolymer consisting of a polystyrene block and a polyolefin block bonded thereto, or a triblock type copolymer consisting of polystyrene blocks arranged at both ends and a polyolefin block arranged therebetween. The triblock type copolymer can contribute to improving impact resistance.

The proportion of the polyolefin block in the block copolymer as the styrene-based elastomer (A2) may be 95% by mass or less, or 90% by mass or less, or 20% by mass or more, 70% by mass or more, or 80% by mass or more, based on the mass of the block copolymer. When the styrene-based elastomer (A2) contains a suitable proportion of polyolefin blocks, a sheet or film having good properties in terms of transparency, impact resistance, and rigidity is easily obtained. Furthermore, when the styrene-based elastomer (A2) contains the polyolefin blocks in the above proportion and also contains the silylated polyolefin (B), a sheet or film in which blocking is suppressed is obtained.
Specific preferred examples of the styrene-based elastomer (A2) include a hydrogenated product of a styrene-butadiene-styrene block copolymer, a hydrogenated product of a styrene-isoprene-styrene block copolymer, and a hydrogenated product of a styrene-isoprene-butadiene-styrene block copolymer.

The styrene-based elastomer (A2) can be produced by a conventional method such as anionic polymerization or cationic polymerization. Examples of commercially available styrene-based elastomers (A2) include Kraton Polymers (trade name: Kraton), Asahi Kasei Corporation (trade names: Tuftec and S.O.E.), Kuraray (trade names: Septon and Hybler), and JSR (trade name: Dynaron).

The content of the styrene-based elastomer (A2) in the sheet or film according to this embodiment is preferably 10 parts by mass to 90 parts by mass, more preferably 20 parts by mass to 80 parts by mass, and even more preferably 30 parts by mass to 70 parts by mass, per 100 parts by mass of the total of the 4-methyl-1-pentene copolymer (A1) and the styrene-based elastomer (A2).

Among the above, from the viewpoint of further suppressing the occurrence of blocking, it is preferable that polymer (A) contains 100 mol % in total of the structural unit (a1) derived from 4-methyl-1-pentene and the structural unit (a2) derived from an α-olefin having 2 to 20 carbon atoms other than 4-methyl-1-pentene, and contains 60 mol % to 99 mol % of structural unit (a1) and 1 mol % to 40 mol % of structural unit (a2).

<Silylated polyolefin (B)>
The silylated polyolefin (B) according to the present embodiment may have any structure as long as it has silicone chain and polyolefin chain.For example, it may be silicone grafted polyolefin, which is a structure in which silicone is grafted to polyolefin, a block copolymer of polyolefin and silicone, a structure in which polyolefin is grafted to silicone, or a structure in which polyolefin is grafted to the silicone part of the block copolymer.The silylated polyolefin (B) may be one type, or may be used in combination of two or more types.

Examples of the block copolymer include a block copolymer in which a polyolefin chain is bonded in the order of a silicone chain, and a block copolymer in which a polyolefin chain is bonded in the order of a silicone chain, a polyolefin chain, and a polyolefin chain.
The polyolefin chain is, for example, a polymer chain containing a structural unit derived from an olefin having 2 to 50 carbon atoms, preferably 2 to 20 carbon atoms.
Among them, those having a structure represented by the following general formula (1) are preferred.

In the above formula (1), A ¹ , A ² and A ³ are each independently a polyolefin chain or a hydrocarbon group having 1 to 20 carbon atoms. R is a hydrocarbon group having 1 to 20 carbon atoms. Each R may be the same or different. m is an integer of 1 to 10,000. When a plurality of ^{A 3s} are present, each A ³ may be the same or different. However, at least one of A ¹ , A ² and A ³ represents a polyolefin chain.

The polyolefin chain in A ¹ , A ² and A ³ above is, for example, a polymer chain containing a structural unit derived from an olefin having 2 to 50 carbon atoms, preferably 2 to 20 carbon atoms.

Specific examples of the olefin having 2 to 50 carbon atoms include ethylene and α-olefins having 3 to 50 carbon atoms (propylene, 1-butene, 1-pentene, 3-methyl-1-butene, 1-hexene, 4-methyl-1-pentene, 3-methyl-1-pentene, 3,4-dimethyl-1-pentene, 4-methyl-1-hexene, 3-ethyl-1-pentene, 3-ethyl-4-methyl-1-pentene, 3,4-dimethyl-1-hexene, 4-methyl-1-heptene, 3,4-dimethyl-1-heptene, 1-octene, 1-decene, 1-dodecene, 1-tetradecene, 1-hexadecene, 1-octadecene, 1-eicosene, vinylcyclohexane, etc.).
Of these, ethylene and α-olefins having 3 to 12 carbon atoms are preferred, ethylene and α-olefins having 3 to 8 carbon atoms are more preferred, and ethylene is particularly preferred.
The polyolefin chain may be a homopolymer chain or a copolymer chain.

Among these, a polymer chain composed only of an olefin having 2 to 50 carbon atoms selected from ethylene and an α-olefin having 3 to 50 carbon atoms is preferred, and an ethylene homopolymer chain, a propylene homopolymer chain, or a copolymer chain of ethylene and an α-olefin having 3 to 20 carbon atoms is more preferred. In a copolymer chain of ethylene and an α-olefin having 3 to 20 carbon atoms, when all structural units are taken as 100 mol%, the structural units derived from an α-olefin having 3 to 20 carbon atoms can be, for example, more than 0 mol% and 20 mol% or less, or more than 0 mol% and 10 mol% or less.

The polyolefin chain may also contain structural units derived from other olefins, if desired. Examples of other olefins include olefins containing internal double bonds, such as cis-2-butene; vinylidene compounds, such as isobutene; arylvinyl compounds, such as styrene; arylvinylidene compounds, such as α-methylstyrene; functional group-substituted vinylidene compounds, such as methyl methacrylate; aliphatic cyclic olefins containing internal double bonds, such as 5-methyl-2-norbornene, tetracyclododecene, cyclopentadiene, and dicyclopentadiene; cyclic olefins containing aromatic rings, such as indene; linear or cyclic polyenes, such as butadiene, isoprene, ethylidene norbornene, and vinyl norbornene.

The content of structural units derived from other olefins is preferably 0 to 10 mol %, and more preferably 0 to 5 mol %, when all structural units constituting the polyolefin chain are taken as 100 mol %.

The polyolefin chain preferably has a number average molecular weight, as determined by the GPC method described below, of 100 to 500,000, more preferably 200 to 100,000, even more preferably 500 to 50,000, and particularly preferably 700 to 10,000.
The polyolefin chain preferably has a molecular weight distribution (Mw/Mn) in the range of 1.1 to 3.0 as determined by the GPC method described below.

GPC measurement method:
The GPC measurement is performed at a temperature of 140° C. using orthodichlorobenzene as a solvent, and analytical values (weight average molecular weight (Mw), number average molecular weight (Mn) and Mw/Mn) can be obtained in terms of polyethylene.

The measurement can be carried out under the following conditions. The molecular weight can be calculated based on the following conversion method using a calibration curve prepared using commercially available monodisperse standard polystyrene.
Apparatus: Gel permeation chromatograph Alliance GPC2000 (manufactured by Waters)
Solvent: o-dichlorobenzene Column: TSKgel column (manufactured by Tosoh Corporation) x 4
Flow rate: 1.0 ml/min Sample: 0.15 mg/ml o-dichlorobenzene solution Temperature: 140° C.
Molecular weight conversion: PS conversion/universal calibration method For the calculation of universal calibration, the coefficients of the Mark-Houwink viscosity formula shown below can be used.
Coefficients of polystyrene (PS): KPS = 1.38 x 10 ^-4 , aPS = 0.70
Coefficients of polyethylene (PE): KPE = 5.06 x 10 ^-4 , aPE = 0.70

In the above A ¹ , A ² , A ³ and R, examples of the hydrocarbon group having 1 to 20 carbon atoms, preferably 1 to 10 carbon atoms, include an alkyl group, an arylalkyl group, an alkenyl group and an aryl group.

Examples of the alkyl group include linear or branched alkyl groups such as a methyl group, an ethyl group, an n-propyl group, an isopropyl group, an n-butyl group, an isobutyl group, a tert-butyl group, a hexyl group, a 2-ethylhexyl group, an octyl group, a decyl group, and an octadecyl group; and cycloalkyl groups such as a cyclopentyl group, a cyclohexyl group, and a norbornyl group.
Examples of the arylalkyl group include a benzyl group, a phenylethyl group, and a phenylpropyl group.
Examples of the alkenyl group include a vinyl group, a propenyl group, and a cyclohexenyl group.
Examples of the aryl group include a phenyl group, a tolyl group, a dimethylphenyl group, a trimethylphenyl group, an ethylphenyl group, a propylphenyl group, and a naphthyl group.

In the above formula (1), m is an integer of 1 to 10,000. m is preferably 5 or more, and more preferably 10 or more. Moreover, m is preferably 1,000 or less, more preferably 300 or less, and more preferably 50 or less.
That is, m is preferably an integer of 5 to 1,000, more preferably an integer of 10 to 300, and even more preferably an integer of 10 to 50.

The above A ¹ , A ² and the single or multiple A ³ may all be polyolefin chains, or some of the groups may be polyolefin chains and the rest may be hydrocarbon groups having 1 to 20 carbon atoms.

In the above formula (1), when m is 2 or more and at least one of ^A3 is different from other ^A3 , multiple types of the following units are present, but the order in which they are arranged is not particularly limited and may be in a block or random order.

As the above formula (1), structures represented by the following (1A), (1B) or (1C) are preferred, with (1A) being more preferred.

(1A) A structure represented by the above formula (1), in which A ¹ and A ² are polyolefin chains, and A ³ is a hydrocarbon group having 1 to 20 carbon atoms.
(1B) A structure in which, in the above formula (1), one of A ¹ and A ² is a polyolefin chain, the other is a hydrocarbon group having 1 to 20 carbon atoms, and A ³ is a hydrocarbon group having 1 to 20 carbon atoms.
(1C) A structure in which, in the above formula (1), A ¹ and A ² are hydrocarbon groups having 1 to 20 carbon atoms, and at least one of A ³ is a polyolefin chain.

In the silylated polyolefin (B) according to this embodiment, the silicone chain/polyolefin chain (mass ratio) is not particularly limited, but is preferably 5/95 to 99/1, and more preferably 10/90 to 95/5, for example.

The method for producing the silylated polyolefin (B) according to this embodiment is not particularly limited, but it can be produced, for example, by the method described in paragraphs 0089 to 0145 and paragraphs 0196 to 0207 of WO 2012/098865.

The content of silylated polyolefin (B) in the sheet or film according to this embodiment is not particularly limited, but from the viewpoint of further suppressing the occurrence of blocking, when the entire sheet or film containing both polymer (A) and the silylated polyolefin (B) described later is taken as 100 mass%, the content is preferably 0.1 mass% or more, more preferably 0.5 mass% or more, and even more preferably 1 mass% or more, and from the viewpoint of maintaining moldability, compatibility with other polymers, strength, and transparency, the content is preferably 10 mass% or less, more preferably 7 mass% or less, even more preferably 5 mass% or less, and preferably 3 mass% or less.
That is, the content of the silylated polyolefin (B) is preferably 0.1% by mass to 10% by mass, more preferably 0.5% by mass to 7% by mass, even more preferably 1% by mass to 5% by mass, and particularly preferably 1% by mass to 3% by mass, when the entire sheet or film is taken as 100% by mass. If the amount of the silylated polyolefin added is equal to or less than the above upper limit, it is preferable in terms of tensile strength at break, tensile elongation at break, and transparency.
That is, by using the silylated polyolefin (B) within the above numerical range, the above-mentioned effects are excellent, in other words, these effects are well balanced.

<Other polymers>
The sheet or film according to this embodiment can be obtained from a composition containing the polymer (A) and the silylated polyolefin (B), as well as other polymers other than these.
Examples of the other polymers include polyolefins other than the polymer (A) and the silylated polyolefin (B), polystyrene, polyvinyl chloride, polyvinylidene chloride, ethylene-vinyl acetate copolymers, ethylene-(meth)acrylic acid copolymers, ethylene-(meth)acrylic acid ester copolymers, polyesters such as polyethylene terephthalate, polycarbonates, polyamides, ABS resins, polyacetal resins, polyimides, polyurethanes, polylactic acid, phenolic resins, epoxy resins, silicone resins, (meth)acrylic resins, and fluorine-based resins.

<Additives>
The sheet or film according to the present embodiment can be obtained from a composition containing various known additives used in the manufacture of polyolefin products, as desired, within the scope of the present embodiment. Examples of such additives include softeners, antiaging agents, processing aids, activators, reaction inhibitors, colorants, dispersants, flame retardants, plasticizers, antioxidants, UV absorbers, antistatic agents, lubricants, antibacterial agents, antifungal agents, surfactants, etc.

The composition according to this embodiment can be obtained by mixing the above-mentioned components by a conventionally known method, and the sheet or film according to this embodiment can be produced by an extrusion molding method.

<Physical properties of sheet or film>
The tan δ determined by the dynamic viscoelasticity measurement will be described below.
The polymer (A) contained in the sheet or film according to this embodiment is subjected to dynamic viscoelasticity measurement while continuously changing the atmospheric temperature, the storage modulus E' (Pa) and the loss modulus E'' (Pa) are measured, and the loss tangent tan δ given by E''/E' is obtained. Looking at the relationship between temperature and loss tangent tan δ, the loss tangent tan δ generally has a peak at a specific temperature. The temperature at which the peak appears is generally called the glass transition point (hereinafter also referred to as Tg). The temperature at which the loss tangent tan δ peak appears can be obtained based on the dynamic viscoelasticity measurement described below. Here, in this embodiment, the peak value of the loss tangent tan δ is usually the maximum value of the loss tangent tan δ according to this embodiment. In addition, when two or more peaks of the loss tangent tan δ are observed, the peak value of the largest peak is the maximum value of the loss tangent tan δ according to this embodiment.

The sheet or film according to this embodiment has a maximum value of loss tangent tan δ of 0.6 or more in the temperature range of 0° C. to 50° C., more preferably a maximum value of loss tangent tan δ of 0.8 or more in the temperature range of 0° C. to 50° C., and even more preferably a maximum value of loss tangent tan δ of 1.0 or more in the temperature range of 0° C. to 50° C. By setting the maximum value of loss tangent tan δ within the above range, the effect of suppressing the occurrence of blocking due to the addition of the silylated polyolefin system (B) can be further improved. Here, the upper limit of the maximum value of loss tangent tan δ in the temperature range of 0° C. to 50° C. is not particularly limited, but is preferably 5.0 or less.
The loss tangent tan δ can be measured by the method described later. The loss tangent tan δ can be adjusted by changing the unit components of the polymer (A) and their molar ratio, as well as the weight average molecular weight (Mw), number average molecular weight (Mn), and the ratio thereof, that is, the molecular weight distribution (Mw/Mn), etc.

The glass transition point (Tg) of the sheet or film according to this embodiment is preferably -60°C to 60°C, more preferably -50°C to 50°C, even more preferably -50°C to 40°C, and particularly preferably -40°C to 40°C. By setting the glass transition point (Tg) within the above range, the occurrence of blocking can be further suppressed by adding the silylated polyolefin (B). The glass transition point (Tg) can be adjusted by changing the unit components of the polymer (A) and their molar ratio, the weight average molecular weight (Mw), the number average molecular weight (Mn), and further the ratio thereof, i.e., the molecular weight distribution (Mw/Mn), etc.

The content of the polymer (A) in this embodiment is not particularly limited, but when the entire sheet or film containing both the polymer (A) and the silylated polyolefin (B) described later is taken as 100 mass%, the content is preferably 90 mass% or more, more preferably 95 mass% or more, even more preferably 97 mass% or more, particularly preferably 99 mass% or more, and is preferably 99.5 mass% or less, more preferably 99 mass% or less.
That is, when the entire sheet or film is taken as 100% by mass, the content of the polymer (A) is preferably 90% by mass to 99.5% by mass, more preferably 95% by mass to 99.5% by mass, further preferably 97% by mass to 99.5% by mass, and particularly preferably 99% by mass to 99.5% by mass. By setting the content within the above range, the occurrence of blocking of the olefin resin composition is further suppressed, and a sheet with an excellent balance of light weight, mechanical properties, handleability, appearance, transparency, moldability, etc. can be obtained.

<Laminate>
The laminate of the present embodiment is formed by laminating the sheet or film (L1) of the present embodiment and a sheet or film (L2) composed of a layer containing a thermoplastic elastomer. The multilayer body can also be described as a multilayer sheet or a multilayer film.
The number of layers of (L1) and (L2) is not particularly limited, and it is sufficient that at least one layer of each is laminated. The order of layers is also not particularly limited, and (L1) layers or (L2) layers may be laminated together.

As described below, in the case of a laminate containing multiple sheets or films, it is sufficient that at least one of the sheets or films constituting the laminate contains both the polymer (A) and the silylated polyolefin (B) (a sheet or film containing both (A) and (B) is referred to as a sheet or film (L1)).
Although there is no particular limitation, preferably, the silylated polyolefin (B) is contained only in the sheet or film (L1).
The polymer (A) and the silylated polyolefin (B) contained in the sheet may be of one type or of multiple types having different molecular skeletons or physical properties.

The sheet or film (L1) constituting the laminate of this embodiment contains a polymer (A) and a silylated polyolefin (B), and when the maximum value of the loss tangent tan δ obtained by measuring the temperature dependence of dynamic viscoelasticity is 0.6 or more in the temperature range of 0°C to 50°C, by laminating this sheet or film (L1) with a layer (L2) containing a thermoplastic elastomer to form a laminate, it is possible to further suppress the occurrence of blocking while further improving durability.
Among these, from the viewpoint of improving the transparency of the sheet, it is preferable that the polymer (A) contains a 4-methyl-1-pentene copolymer (A1).

The inventors have found that a sheet made of a blend of a 4-methyl-1-pentene copolymer and a thermoplastic elastomer is prone to becoming cloudy due to the difference in refractive index between the 4-methyl-1-pentene copolymer and the thermoplastic elastomer described below, since the 4-methyl-1-pentene copolymer and the thermoplastic elastomer described below are difficult to completely accommodate at the molecular level. From this perspective, by forming a multilayer structure in which the 4-methyl-1-pentene copolymer and the thermoplastic elastomer are not blended but are separated into phases, it is possible to provide a laminate in which the clouding of the sheet is suppressed and the transparency of each phase is maintained.

In other words, in the laminate of this embodiment, it is preferable that the sheet or film (L1) contains only the 4-methyl-1-pentene polymer (A1) as the polymer (A) and the silylated polyolefin (B), and the sheet or film (L2) contains a styrene-based elastomer as the thermoplastic elastomer. By adopting this configuration, a laminate with excellent transparency can be obtained.

The sheet or film (L2) contains a thermoplastic elastomer, which will be described later. In addition, the above-mentioned configuration can suppress permanent deformation of the sheet, improve the bending resistance of the sheet in a low-temperature environment (for example, below 20°C), and further improve the durability of the sheet. Furthermore, from the viewpoint of suppressing the occurrence of blocking, it is more preferable that the outer layer of the laminate is (L1) containing a silylated polyolefin (B).

The thickness of one layer of the sheet or film (L1) is preferably 0.01 mm to 2 mm, more preferably 0.02 mm to 1 mm, even more preferably 0.03 mm to 0.5 mm, particularly preferably 0.03 mm to 0.3 mm, and extremely preferably 0.04 mm to 0.1 mm. When it is equal to or less than the upper limit, the flexibility of the sheet can be made good. That is, when the thickness of one layer of the sheet or film (L1) is within the above range, the flexibility of the sheet is excellent.
The thickness of one layer of the sheet or film (L2) is preferably 0.01 mm to 2 mm, more preferably 0.02 mm to 1 mm, even more preferably 0.02 mm to 0.5 mm, particularly preferably 0.03 mm to 0.5 mm, and extremely preferably 0.05 mm to 0.2 mm. When the thickness is equal to or greater than the lower limit, the sheet strength, heat resistance, and cold resistance can be improved. When the thickness is equal to or less than the upper limit, the flexibility of the sheet can be improved. That is, when the thickness of one layer of the sheet or film (L2) is within the above range, the flexibility of the sheet is excellent, in other words, the balance of these properties is excellent.

Such a laminate can be produced, for example, by a co-extrusion molding method, and specific examples thereof include the following configurations.
(1) Layer containing a polymer (A) containing a 4-methyl-1-pentene copolymer and a silylated polyolefin (B)/Layer composed of a thermoplastic elastomer/Layer containing a polymer (A) containing a 4-methyl-1-pentene copolymer and a layer containing a silylated polyolefin (B)=0.075 mm/0.15 mm/0.075 mm, total thickness 0.3 mm
(2) Layer containing a polymer (A) containing a 4-methyl-1-pentene copolymer and a silylated polyolefin (B) / Layer 1 composed of a thermoplastic elastomer / Layer 2 composed of a thermoplastic elastomer / Layer 3 composed of a thermoplastic elastomer / Layer containing a polymer (A) containing a 4-methyl-1-pentene copolymer and a silylated polyolefin (B) = 0.075 mm / 0.03 mm / 0.09 mm / 0.03 mm / 0.075 mm, total thickness 0.3 mm
In this way, when the sheet or film (L1) and the sheet or film (L2) are laminated in a total of three or more layers, it is preferable that at least one outer layer of the laminate is a sheet or film (L1).

A styrene-based elastomer was used as the thermoplastic elastomer, and the blocking properties and transparency were evaluated using the laminates (1) and (2) above, and the results were good.

Here, examples of the thermoplastic elastomer include olefin-based elastomers, styrene-based elastomers, urethane-based elastomers, ester-based elastomers, and amide-based elastomers. These thermoplastic elastomers may be used alone or in combination of two or more. Among these thermoplastic elastomers, the above-mentioned styrene-based elastomer has a moderate compatibility with copolymer (A), and when a co-extruded multilayer sheet is formed from both, it has the advantage of easily ensuring interlayer adhesion. In addition, among styrene-based elastomers, hydrogenated styrene-based elastomers with a low styrene content are compatible with copolymer (A) and can be preferably used. Specific examples of such hydrogenated styrene-based elastomer products include Kraton G1657MS (manufactured by Kraton Polymer Japan Co., Ltd.) and Tuftec H1221, Tuftec H1062, Tuftec H1521, Tuftec 1052, S.O.E. 1606, and S.O.E. 1605, manufactured by Kuraray Co., Ltd.; Septon 2004F and Hybra 7311F are examples.

The laminate of this embodiment may include other layers or members between its layers (between L1 and L2, between L1 and L1, between L2 and L2). Examples of other layers include adhesive layers, and examples of members include reinforcing materials such as elastic fibers.

A composite can be produced by laminating other members to the sheet or laminate according to this embodiment, and, if necessary, by hot pressing or welding using a press or the like. Also, a composite can be produced by providing an adhesive between the sheet or laminate and other members, and then bonding the sheet or laminate and other members via the adhesive. When other members are laminated to the laminate, it is preferable that the layer (outer layer) on the opposite side to the layer facing the other members of the laminate is (L1) containing silylated polyolefin (B) from the viewpoint of suppressing the occurrence of blocking.
As the adhesive, an SBR-based solvent adhesive or a hot melt adhesive made of EVA, petroleum resin, or a mixture of EVA and petroleum resin can be suitably used.
The other materials are not particularly limited, and examples thereof include woven fabric, nonwoven fabric, synthetic fiber, artificial leather, synthetic leather, natural leather, fur, metal, carbon material, rubber, thermoplastic elastomer, thermoplastic resin, thermosetting resin, polymer foam, mesh structure (warp knitted fiber, double russell mesh, three-dimensional spring structure, etc.), fiber reinforced plastic, paper, wood, glass, stone material, ceramic, etc. These materials may be used alone or in combination of two or more.

<Physical Properties of Laminate>
The tan δ determined by measuring the dynamic viscoelasticity of the sheet or film (L1) positioned as the outermost layer of the laminate of this embodiment will be described below.
The polymer (A) contained in the sheet or film (L1) according to this embodiment is subjected to dynamic viscoelasticity measurement while continuously changing the atmospheric temperature, the storage modulus E' (Pa) and the loss modulus E'' (Pa) are measured, and the loss tangent tan δ given by E''/E' is obtained. Looking at the relationship between temperature and loss tangent tan δ, the loss tangent tan δ generally has a peak at a specific temperature. The temperature at which the peak appears is generally called the glass transition point (hereinafter also referred to as Tg). The temperature at which the loss tangent tan δ peak appears can be obtained based on the dynamic viscoelasticity measurement described below. Here, in this embodiment, the peak value of the loss tangent tan δ is usually the maximum value of the loss tangent tan δ according to this embodiment. In addition, when two or more peaks of the loss tangent tan δ are observed, the peak value of the largest peak is the maximum value of the loss tangent tan δ according to this embodiment.

The sheet or film (L1) located in the outermost layer of the laminate has a maximum loss tangent tan δ of 0.6 or more in the temperature range of 0°C to 50°C, more preferably a maximum loss tangent tan δ of 0.8 or more in the temperature range of 0°C to 50°C, and even more preferably a maximum loss tangent tan δ of 1.0 or more in the temperature range of 0°C to 50°C.

By setting the maximum value of the loss tangent tanδ of the sheet or film (L1) located in the outermost layer within the above range, the effect of suppressing the occurrence of blocking in the laminate due to the addition of the silylated polyolefin (B) can be further improved. Here, the upper limit of the maximum value of the loss tangent tanδ in the temperature range of 0°C to 50°C is not particularly limited, but it is preferably 5.0 or less.
In addition, when sheets or films (L1) are present in both outermost layers of the laminate according to this embodiment, it is preferable that the maximum value of the loss tangent tan δ of each of the two sheets or films (L1) is within the above range. On the other hand, the maximum value of the loss tangent tan δ of the sheet or film (L1) located between layers of the laminate is not particularly limited.

The loss tangent tan δ can be measured by the method described below. The loss tangent tan δ can be adjusted by changing the unit components of the polymer (A) and their molar ratios, etc.

The glass transition point (Tg) of the sheet or film (L1) according to this embodiment is preferably -60°C to 60°C, more preferably -50°C to 50°C, even more preferably -50°C to 40°C, and particularly preferably -40°C to 40°C. By setting the glass transition point (Tg) within the above range, the occurrence of blocking can be further suppressed by adding the silylated polyolefin (B). The glass transition point (Tg) can be adjusted by changing the unit components of the polymer (A) and their molar ratios, etc.

The above describes the embodiments, but these are merely examples, and various configurations other than those described above can also be adopted.

The present embodiment will be described in detail below with reference to examples, but the present embodiment is not limited to these examples.

1. Measurement and Evaluation Methods (1) Composition The contents (mol %) of 4-methyl-1-pentene and α-olefin in the 4-methyl-1-pentene polymer (A1) were measured by ¹³ C-NMR under the following measurement conditions.
～Measurement conditions～
Measurement device: Nuclear magnetic resonance device (ECP500 type, manufactured by JEOL Ltd.)
Observed nucleus: ^13C (125MHz)
Sequence: Single pulse proton decoupling Pulse width: 4.7 μs (45° pulse)
Repeat time: 5.5 seconds. Accumulation count: 10,000 times or more. Solvent: orthodichlorobenzene/deuterated benzene (volume ratio: 80/20) mixed solvent. Sample concentration: 55 mg/0.6 mL.
Measurement temperature: 120°C
Chemical shift reference value: 27.50 ppm

(2) Intrinsic Viscosity The intrinsic viscosity [η] of the 4-methyl-1-pentene polymer (A1) was measured in a decalin solvent at 135° C. using an Ubbelohde viscometer as a measuring device.
Specifically, about 20 mg of powdered polymer (A) was dissolved in 25 ml of decalin, and the specific viscosity η _SP was measured using an Ubbelohde viscometer in an oil bath at 135° C. The decalin solution was diluted with 5 ml of decalin, and the specific viscosity η _SP was measured in the same manner as above. This dilution procedure was repeated twice, and the value of η _SP /C when the concentration (C) was extrapolated to 0 was calculated as the limiting viscosity [η] (unit: dl/g) (see formula 1).
[η]=lim(η _SP /C) (C→0) ...Equation 1

(3) Weight average molecular weight (Mw) and molecular weight distribution (Mw/Mn)
The GPC measurement was performed at a temperature of 140° C. using orthodichlorobenzene as a solvent and a polystyrene calibration curve, and analytical values (weight average molecular weight (Mw), number average molecular weight (Mn) and Mw/Mn) can be obtained as polyethylene-equivalent values. The weight average molecular weight (Mw) and molecular weight distribution (Mw/Mn) of the 4-methyl-1-pentene polymer (A1) and the silylated polyolefin (B) were measured under the following conditions.

(3.1) Measurement conditions for 4-methyl-1-pentene polymer (A1):
Calculation was performed using standard polystyrene conversion method.
Apparatus: GPC (ALC/GPC 150-C plus type, differential refractometer detector integrated type, manufactured by Waters Corporation, product name)
Solvent: o-dichlorobenzene Column: Two GMH6-HT (trade name) columns manufactured by Tosoh Corporation and two GMH-HTL (trade name) columns manufactured by Tosoh Corporation connected in series Flow rate: 1.0 mL/min
Column temperature: 140° C.
・Molecular weight conversion: Standard polystyrene conversion method

(3.2) Measurement conditions for silylated polyolefin (B):
A calibration curve was prepared using commercially available monodisperse standard polystyrene, and the values were calculated based on the following conversion method.
Apparatus: Gel permeation chromatograph Alliance GPC2000 (manufactured by Waters)
Solvent: o-dichlorobenzene Column: Four TSKgel columns manufactured by Tosoh Corporation connected in series Flow rate: 1.0 ml/min Temperature: 140°C
Sample: 0.15 mg/mL lo-dichlorobenzene solution Molecular weight conversion: PS conversion/general-purpose calibration method The coefficients of the Mark-Houwink viscosity formula shown below were used for the general-purpose calibration calculation.
Coefficients of polystyrene (PS): KPS = 1.38 x 10 ^-4 , aPS = 0.70
Coefficients of polyethylene (PE): KPE = 5.06 x 10 ^-4 , aPE = 0.70

(4) Melt flow rate (MFR)
The melt flow rate (MFR) of the 4-methyl-1-pentene polymer (A1) was measured in accordance with ASTM D1238 at 230° C. under a load of 2.16 kg, and expressed in g/10 min.

(5) Density The density of the 4-methyl-1-pentene polymer (A1) was measured in accordance with ASTM D1505 (water displacement method).

(6) Melting point (Tm)
The melting point (Tm) of the 4-methyl-1-pentene polymer (A1) was measured using a differential scanning calorimeter (DSC220C, manufactured by Seiko Instruments Inc.) as a measuring device.

(7) Dynamic Viscoelasticity Measurement The prepared resin sheet was cut into a rectangular piece having a length of 20 mm and a width of 10 mm. Using a viscoelasticity measuring device RSA-III (trade name) manufactured by TA Instruments Japan Inc., the temperature dependency data of dynamic viscoelasticity was measured under the following measurement conditions in the tensile mode. The ratio (E''/E': loss tangent) of the storage modulus (E') to the loss modulus (E'') obtained in the measurement was defined as tan δ. In addition, when tan δ was plotted against temperature, if an upwardly convex curve, i.e., a peak, was obtained within a specific temperature range, the temperature at the maximum value of the apex of the peak was defined as the glass transition point (Tg).
(Measurement condition)
Frequency: 1.59Hz
Temperature: -70 to 80 degrees Celsius
Ramp Rate: 4.0° C./min Strain: 0.1%
Here, when the resin sheet is a laminate, a single-layer sheet (thickness: 0.075 mm) having the same composition as L1, which is the outermost layer of the resin sheet, was separately prepared, and the dynamic viscoelasticity was measured in the same manner as above to determine tan δ and its peak temperature (glass transition point: Tg).

(8) Total Light Transmittance The total light transmittance of the resin sheet was measured at room temperature (23° C.) in accordance with the test standard JIS K7361.
(9) Blocking Property Two rectangular test pieces (10 cm x 5 cm) were cut out from a resin sheet (single layer sheet or laminate), and were overlapped with each other. The overlapping portion of the two resin sheets was then sandwiched between a support and a weight from above and below so that a constant surface pressure of 0.4 N/ ^cm2 was applied vertically to the square-shaped portion (5 cm x 5 cm).
Thereafter, the single-layer sheet was left to stand in an oven at 60° C. for 12 hours, and then the laminated sheet of two resin sheets was taken out of the oven and cooled at room temperature (23° C.) for 20 minutes. Thereafter, the ease of peeling when peeling the film by hand from the laminated two resin sheets was determined as blocking property and evaluated according to the following criteria.
<Evaluation Criteria for Single-Layer Sheets or Films>
Good: Adhesive strength is present, but peels off without stretching.
×: When peeled off, the film was stretched and peeled off.
On the other hand, the laminate was left in an oven at 80° C. for 12 hours, and then the laminate of two resin sheets was taken out of the oven and cooled at room temperature (23° C.) for 20 minutes. After that, the ease of peeling when peeling the film by hand from the two overlapping resin sheets was determined as blocking property and evaluated according to the following criteria.
<Evaluation Criteria for Laminates>
◯: Almost no adhesion, no resistance, and easy peeling.
×: Sticky.

2. Raw Materials Raw materials used in the examples and comparative examples are shown below.

(1) Polymer (A)
<Synthesis of Copolymer A-1>
A 1.5-liter stainless steel autoclave equipped with an agitator and thoroughly purged with nitrogen was charged with 300 ml of normal hexane (dried over activated alumina in a dry nitrogen atmosphere) and 450 ml of 4-methyl-1-pentene at 23° C. 0.75 ml of a 1.0 mmol/ml toluene solution of triisobutylaluminum (TIBAL) was charged into the autoclave, and the agitator was turned on.
Next, the autoclave was heated to an internal temperature of 60°C, and pressurized with propylene so that the total pressure was 0.40 MPa (gauge pressure). Subsequently, 1 mmol of methylaluminoxane prepared in advance in terms of Al and 0.34 ml of a toluene solution containing 0.01 mmol of diphenylmethylene (1-ethyl-3-t-butyl-cyclopentadienyl) (2,7-di-t-butyl-fluorenyl) zirconium dichloride were pressed into the autoclave using nitrogen, and polymerization was initiated. During the polymerization reaction, the temperature was adjusted so that the internal temperature of the autoclave was 60°C. 60 minutes after the start of polymerization, 5 ml of methanol was pressed into the autoclave using nitrogen to stop the polymerization, and the autoclave was depressurized to atmospheric pressure. Acetone was poured into the reaction solution while stirring.
The thus obtained polymer containing the solvent was dried at 100° C. under reduced pressure for 12 hours to obtain an olefin copolymer (A-1). The content of structural units derived from 4-methyl-1-pentene in this olefin copolymer (A-1) was 72 mol%, and the content of structural units derived from propylene was 28 mol%. In addition, the intrinsic viscosity [η] of this olefin copolymer (A-1) was 1.5, the weight average molecular weight (Mw) was 337,000, the molecular weight distribution (Mw/Mn) was 2.1, the MFR measured in accordance with ASTM D1238 was 10 g/10 min, and the density evaluated in accordance with ASTM D1505 (underwater displacement method) was 0.84 g/cm ^3. The melting point (Tm) was not observed.
The maximum value of the loss tangent tan δ measured by the above method was 2.5 in both the temperature ranges of -20°C to 80°C and 0°C to 60°C. The temperature showing the maximum value of tan δ, i.e., the glass transition point (Tg), was 28°C.

<Synthesis of Copolymer A-2>
A 1.5-liter stainless steel autoclave equipped with an agitator and thoroughly purged with nitrogen was charged with 300 ml of normal hexane (dried over activated alumina in a dry nitrogen atmosphere) and 450 ml of 4-methyl-1-pentene at 23° C. 0.75 ml of a 1.0 mmol/ml toluene solution of triisobutylaluminum (TIBAL) was charged into the autoclave, and the agitator was turned on.
Next, the autoclave was heated to an internal temperature of 60°C, and pressurized with propylene so that the total pressure was 0.19 MPa (gauge pressure). Subsequently, 1 mmol of methylaluminoxane prepared in advance in terms of Al and 0.34 ml of a toluene solution containing 0.01 mmol of diphenylmethylene (1-ethyl-3-t-butyl-cyclopentadienyl) (2,7-di-t-butyl-fluorenyl) zirconium dichloride were pressed into the autoclave using nitrogen, and polymerization was initiated. During the polymerization reaction, the temperature was adjusted so that the internal temperature of the autoclave was 60°C. 60 minutes after the start of polymerization, 5 ml of methanol was pressed into the autoclave using nitrogen to stop the polymerization, and the autoclave was depressurized to atmospheric pressure. Acetone was poured into the reaction solution while stirring.

The thus obtained polymer containing the solvent was dried at 100°C under reduced pressure for 12 hours to obtain an olefin copolymer (A-2). The content of structural units derived from 4-methyl-1-pentene in this olefin copolymer (A-2) was 85 mol%, and the content of structural units derived from propylene was 15 mol%. In addition, the intrinsic viscosity [η] of this olefin copolymer (A-2) was 1.4, the weight average molecular weight (Mw) was 340,000, the molecular weight distribution (Mw/Mn) was 2.1, the MFR measured in accordance with ASTM D1238 was 10g/10min, and the density measured in accordance with ASTM D1505 (underwater displacement method) was 0.84g/cm ^3. The melting point (Tm) was 130°C. The maximum value of the loss tangent tanδ in both the temperature ranges of -20°C to 80°C and 0°C to 60°C measured by the above method was 1.7. The temperature at which tan δ was maximum, that is, the glass transition point (Tg), was 40°C.

(2) Silylated polyolefin (B)
[Synthesis Example 1]
(Synthesis of polyethylene having a vinyl group at one end)
An ethylene polymer (P-1) containing a vinyl group at one end was synthesized according to the method described in Synthesis Example 2 of WO 2012/098865.
It was clear from ¹ H-NMR measurement that the obtained polymer was a homopolyethylene containing a double bond only at one end. The physical properties of this ethylene-based polymer (P-1) (single unit) containing a double bond at one end were as follows:
Melting point (Tm) 127°C
Mw=4770, Mw/Mn=2.25 (GPC)
Terminal unsaturation rate: 97%

[Synthesis Example 2]
(Preparation of platinum catalyst composition (C-1))
In a 50 ml sample tube equipped with a magnetic stirrer tip, 0.50 g of platinum(II) chloride was suspended in hydrosilane A (HS(A), manufactured by Gelest, Inc., DMS-H11) (10 ml) having the following structure, and the suspension was stirred at room temperature under a nitrogen stream. After stirring for 190 hours, about 0.4 ml of the reaction liquid was sampled with a syringe and filtered using a 0.45 μm PTFE filter to collect the filtrate in a 10 ml sample tube, thereby obtaining a platinum catalyst composition (C-1) having a platinum concentration of 3.8 mass%.
Hydrosilane A (HS(A)): HSi(CH ₃ ) ₂ O—(—Si(CH ₃ ) ₂ —O—) _n —Si(CH ₃ ) ₂ H
(n=12-13)

[Synthesis Example 3]
(Introduction of polyethylene having terminal vinyl groups into hydrosilane)
A 300 ml two-neck flask was charged with 25.1 g (11.8 mmol) of the ethylene polymer (P-1) containing a vinyl group at one end obtained in [Synthesis Example 1], and 6.7 g (5.9 mmol; equivalent to 11.8 mmol as Si-H groups) of hydrosilane A (HS(A)) and 150 μl (1.4 × 10 -6 mmol in terms of Pt) of the platinum catalyst composition (C-1) prepared in [Synthesis Example 2] diluted 200 times with hydrosilane A (HS(A)) (C-1a) were further charged under a nitrogen atmosphere. The two-neck flask was set in ^an oil bath whose internal temperature had been raised to 130°C in advance, and stirring was performed. After about 3 minutes, the polymer melted. Then, after 6 hours, it was cooled, about 200 ml of methanol was added, and the contents were taken out into a 300 ml beaker and stirred for 2 hours. Thereafter, the solid was filtered, washed with methanol, and dried at 60 ° C. under reduced pressure of 2 hPa or less to obtain 33.1 g of a white solid silylated polyolefin (B-1). As a result of NMR analysis, the obtained silylated polyolefin (B-1) had a yield of 98%, an olefin conversion rate of 100%, and an isomerization rate of 2%. The MFR was equal to or higher than the upper limit of measurement (MFR>100 g / 10 min), and the polyorganosiloxane content in (B-1) calculated from the molecular formula was 23% by mass.

Details of the resin sheets (single layer sheets) shown in Table 1 are as follows.
PMP-A1 is a sheet having a thickness of 0.1 mm obtained by T-die extrusion molding, which is composed of a blend of 30 parts by mass of 4-methyl-1-pentene/propylene copolymer (A-1), 10 parts by mass of 4-methyl-1-pentene/propylene copolymer (A-2), 60 parts by mass of a hydrogenated styrene-based elastomer (Hybler, brand 7311F, manufactured by Kuraray Co., Ltd., content of monomer units derived from styrene: 12% by mass), and 1 part by mass of a silylated polyolefin (B-1).
PMP-A2 and PMP-A3 are sheets having a thickness of 0.1 mm obtained in the same manner as PMP-A1, except that the amount of silylated polyolefin (B-1) was changed to the value shown in Table 1.
PMP-A4 is a sheet having a thickness of 0.1 mm obtained in the same manner as PMP-A1, except that the silylated polyolefin (B-1) was not used.
PMP-A5 is a sheet having a thickness of 0.1 mm obtained in the same manner as PMP-A1, except that the silylated polyolefin (B-1) was changed to 0.3 parts by mass of erucic acid amide (Alflo P-10 (trade name), manufactured by NOF Corporation).

Details of the resin sheets (laminates) shown in Table 2 are as follows.
PMP-B1 is a sheet having a total thickness of 0.3 mm obtained by T-die coextrusion sheet molding so that the cross-sectional structure is (L1)/(L2)/(L1)=0.075 mm/0.15 mm/0.075 mm, where (L1) is a layer formed by blending 4-methyl-1-pentene/propylene copolymer (A-1), 4-methyl-1-pentene/propylene copolymer (A-2), and silylated polyolefin (B-1) in a blending ratio of 60/40/0.5 parts by mass, and (L2) is a layer formed only of Kraton G1657VS manufactured by Kraton Polymer Japan as a hydrogenated styrene-based elastomer.
PMP-B2 and PMP-B3 are sheets having a total thickness of 0.3 mm obtained in the same manner as PMP-B1, except that the amount of silylated polyolefin (B-1) was changed to the value shown in Table 2.
PMP-B4 is a sheet having a thickness of 0.3 mm obtained in the same manner as PMP-B1, except that the silylated polyolefin (B-1) was not used.
PMP-B5 is a sheet having a total thickness of 0.3 mm obtained in the same manner as PMP-B1, except that the silylated polyolefin (B-1) was changed to 0.3 parts by mass of erucic acid amide (Alflo P-10 (trade name), manufactured by NOF Corporation).

As is clear from Table 1, the resin sheets of Examples 1, 2, and 3, which are made of compositions containing the polymer (A) and the silylated polyolefin (B), were found to have excellent blocking properties. On the other hand, the resin sheets of Comparative Examples 1 and 2, which do not contain the silylated polyolefin (B), were poor in blocking properties.
As is clear from Table 2, the laminates (Examples 4, 5, and 6) including resin sheets made of a composition containing polymer (A) and silylated polyolefin (B) showed almost no adhesion and were easily peeled off without resistance even when stacked, and were therefore found to have very excellent blocking properties. On the other hand, Comparative Examples 3 and 4, which used multilayers including resin sheets not including silylated polyolefin (B), showed adhesion when stacked, and there was room for improvement in blocking properties.
In this way, since the resin sheet or laminate of the examples according to this embodiment has excellent blocking properties, it is considered that it can be easily unwound even when it is wound into a roll to form an original sheet. Furthermore, since blocking between resin sheets or between laminates is suppressed by pressure bonding when overlapping and cutting, it is considered that the workability is excellent, and further the manufacturing stability of products using the resin sheet or laminate according to this embodiment is excellent.
Furthermore, as is clear from Tables 1 and 2, it has become clear that by forming the film into a multi-layered body, the total light transmittance, which is related to transparency, is further improved.

Claims (12)

A polymer (A) containing one or more polymers selected from the group consisting of a 4-methyl-1-pentene polymer (A1) and a styrene elastomer (A2); and a silylated polyolefin (B);
A sheet or film comprising a composition comprising: The sheet or film according to claim 1, wherein the maximum value of the loss tangent tan δ obtained by measuring the temperature dependence of the dynamic viscoelasticity of the sheet or film is 0.6 or more in the temperature range of 0°C to 50°C. The 4-methyl-1-pentene polymer (A1) contains 100 mol % in total of the structural units (a1) derived from 4-methyl-1-pentene and the structural units (a2) derived from an α-olefin having 2 to 20 carbon atoms other than 4-methyl-1-pentene,
3. The sheet or film according to claim 1, comprising 60 mol% to 99 mol% of the structural unit (a1) and 1 mol% to 40 mol% of the structural unit (a2). The styrene-based elastomer (A2) includes a hydrogenated styrene-based elastomer,
The sheet or film according to any one of claims 1 to 3, wherein the proportion of monomer units derived from styrene in 100% by mass of the hydrogenated styrene-based elastomer is 5% by mass to 80% by mass. the polymer (A) comprises a copolymer in which the total content of the structural unit (a1) derived from 4-methyl-1-pentene and the structural unit (a2) derived from an α-olefin having 2 to 20 carbon atoms other than 4-methyl-1-pentene is 100 mol %,
The sheet or film according to claim 1 or claim 2, wherein the copolymer contains 60 mol% to 99 mol% of the structural unit (a1) and 1 mol% to 40 mol% of the structural unit (a2). The sheet or film according to any one of claims 1 to 5, wherein the silylated polyolefin (B) comprises a silylated polyolefin represented by the following general formula (1):

(In the general formula (1), A ¹ , A ² and A ³ each independently represent a polyolefin chain or a hydrocarbon group having 1 to 20 carbon atoms. R represents a hydrocarbon group having 1 to 20 carbon atoms. Each R may be the same or different. m represents an integer of 1 to 10,000. When a plurality of A ³ 's are present, each A ³ 's may be the same or different. However, at least one of A ¹ , A ² and A ³ 's represents a polyolefin chain.) The sheet or film according to any one of claims 1 to 6, comprising 0.5 to 10 parts by mass of the silylated polyolefin (B) per 100 parts by mass of the polymer (A). A sheet or film (L1) according to any one of claims 1 to 7,
A sheet or film (L2) consisting of a layer containing a thermoplastic elastomer;
A laminate in which the above-mentioned are stacked. The sheet or film (L1) is
a copolymer in which the total amount of the structural unit (a1) derived from 4-methyl-1-pentene and the structural unit (a2) derived from an α-olefin having 2 to 20 carbon atoms other than 4-methyl-1-pentene is 100 mol %,
9. The laminate according to claim 8, wherein the copolymer contains 60 mol % to 99 mol % of the structural unit (a1) and 1 mol % to 40 mol % of the structural unit (a2). The sheet or film (L1) and the sheet or film (L2) are laminated in a total of three or more layers,
11. The laminate according to claim 9 or 10, wherein at least one outer layer is a sheet or film (L1). The sheet or film (L1) contains only a 4-methyl-1-pentene polymer (A1) as the polymer (A),
The laminate according to any one of claims 8 to 10, wherein the sheet or film (L2) contains a styrene-based elastomer as the thermoplastic elastomer. The laminate according to any one of claims 8 to 11, wherein the maximum value of the loss tangent tanδ obtained by measuring the temperature dependence of the dynamic viscoelasticity of the sheet or film (L1) located in the outermost layer is 0.6 or more in the temperature range of 0°C to 50°C.