KR20140061363A - Film laminate, film roll, and method for producing film roll - Google Patents

Abstract

An object of the present invention is to provide a film laminate and a film laminate which can be used for optical use members and which do not cause cracks on the surface or end portions and are excellent in transparency and thickness accuracy. The present invention relates to a laminate film comprising a polycarbonate resin film composed of a polycarbonate resin derived from a dihydroxy compound (a) having a moiety represented by formula (1) and a masking film laminated on a part of the structure, And a static friction coefficient with the non-adhesive surface of the masking film is not less than 1.8 or not less than 0.01 and not more than 1.8.

Description

TECHNICAL FIELD [0001] The present invention relates to a film laminate, a film laminate, and a method for producing the film laminate,

The present invention relates to a film laminate obtained by laminating a polycarbonate resin film having a high transparency and a high frictional resistance between film surfaces and a masking film, a film wound laminate obtained by winding the film laminate in roll form, and a method for producing the film wound laminate .

Background Art [0002] Polycarbonate resin films are inexpensive and light in weight, and have excellent transparency, moldability, optical properties, heat resistance, dimensional stability, and mechanical strength, and are used in a wide range of fields. In particular, it is widely used for optical use components such as an optical disk, a lightguide, a phase difference compensating plate such as a liquid crystal display and the like. In some cases, the polycarbonate film is subjected to surface treatment or surface treatment such as coating and printing for imparting performance and functions such as solvent resistance, abrasion resistance, scratch resistance and anti-reflection.

However, in general, the polycarbonate resin film has a large frictional resistance between the film surfaces, and if the mirror surface film is wound in a roll without any surface processing, the activity (slipperiness) between the film surfaces is insufficient, Wrinkles often occur.

A method of roughening the surface of the film in order to avoid the occurrence of such unwinds and rewinds has been proposed. This method is intended to improve the activity by reducing the contact area between the film surfaces.

As one of such means, a method of roughening a surface by kneading a fine particle with a polycarbonate resin has been disclosed (Patent Documents 1 and 2).

As another means, there is disclosed a method of forming a film by a double-sided touch method using a rubber roll or a roughened metal roll as a part of a cooling roll, and transferring the roughened surface to the film by pressurization Patent Documents 3 to 5).

As a recently proposed means, there has been disclosed a method of suppressing an increase in haze of a film while reducing the static friction between the film surfaces by using a double-sided touch method using a cooling roll in which the roughness is defined Document 6).

It is also disclosed that a protective film is laminated on an optical film mainly made of a polycarbonate resin to obtain an optical film product having small irregularities on its surface, or to obtain a rolled wound product having a clean appearance, (Patent Documents 7 and 8).

Japanese Patent Application Laid-Open No. 52-105957 Japanese Laid-Open Patent Publication No. 01-319540 Japanese Patent Application Laid-Open No. 64-72831 Japanese Patent Application Laid-Open No. 64-72832 Japanese Patent Application Laid-Open No. 64-72833 Japanese Patent Application Laid-Open No. 2008-7626 International Publication No. 2003/004270 Japanese Laid-Open Patent Publication No. 2011-112945 International Publication No. 2006/041190

However, in the methods disclosed in Patent Documents 1 and 2, a part of the fine particles kneaded in the polycarbonate resin float on the surface of the film, resulting in point defects on the optical characteristics of the film, or adherence to the cooling roll.

In the methods disclosed in Patent Documents 3 to 5, the haze of the film is increased and the transparency is impaired.

In the method disclosed in Patent Document 6, the intended thickness precision can not be attained especially in applications in which high precision film thickness accuracy is required, or in the case of obtaining a specific laminate of a polycarbonate resin film.

On the other hand, Patent Documents 7 and 8 disclose that a protective film is laminated and wound, but an optical film mainly composed of a polycarbonate resin is widely used. For example, a polycarbonate- The film is very brittle, so even if a protective film is laminated, if it is desired to be wound or to trim an edge, cracks will occur and the film can not be used.

That is, the polycarbonate resin having a bulk structure such as fluorene has high usability for optical use, but because of its rigid structure, entanglement of the molecular chains hardly occurs and the notch sensitivity is high, It is difficult to stably produce a molded body.

SUMMARY OF THE INVENTION Accordingly, it is an object of the present invention to provide a film laminate excellent in transparency and thickness accuracy, which can be used for an optical use member and does not cause cracks on the surface or end of the polycarbonate resin film during winding or trimming, An object of the present invention is to obtain a uniform film roll laminate using a film laminate without winding and unwinding wrinkles.

As a result of intensive investigations, the inventors of the present invention have found that a film laminate comprising a brittle non-breakable film produced by using a polycarbonate resin having a specific molecular structure, a specific masking film, and the film laminate are rolled And found that the obtained film laminate solves all of the above problems, thereby completing the present invention.

The first aspect of the present invention is a biaxially stretchable polycarbonate resin composition obtained by melt-extruding a polycarbonate resin containing a structural unit derived from a dihydroxy compound (a) having a moiety represented by the following formula (1) A film laminate comprising a polycarbonate resin film and a masking film having a base layer and an adhesive layer laminated thereon, wherein the film has a static friction coefficient of not less than 1.8 in a state that the polycarbonate resin films are in surface contact with each other, Wherein the film has a static friction coefficient of 0.01 or more and less than 1.8 in a state in which the one surface and the non-sticking surface of the masking film are in surface contact with each other.

[Chemical Formula 1]

In the present invention, the term "non-adhesive surface" refers to a surface on the side of the substrate layer opposite to the adhesive layer of the masking film. In the present invention, " static friction coefficient " refers to static friction coefficient measured based on JIS-K7125 (1999). In the present invention, " no brittle fracture " means that the polycarbonate resin film satisfies the following conditions.

First, a polycarbonate resin is melt-extruded to produce a film having a width of 200 mm or more and a thickness of 100 占 퐉. A rectangular test piece having a length of 40 mm in the flow direction MD of the film and a width of 10 mm in the width direction TD is obtained from the vicinity of the central portion in the width direction of the film.

The gap between the left and right joint surfaces of the vise is opened to 40 mm, and both ends of the test piece are fixed within the joint surface. Next, the gap between the left and right joint surfaces is narrowed down to a velocity of 2 mm / sec or less, and the whole of the folded film is compressed within the joint surface while the film is prevented from protruding from the joint surface of the vise.

A case where the test piece is cracked into two pieces (or three or more pieces) in the bent portion until the joint surfaces are completely adhered is called " cracked ", and the test piece is not cracked Is referred to as " no crack ".

The test was repeated five times on the same type of film. The test results were evaluated as follows. &Quot; C: brittle fracture " and " No ".

A second embodiment of the present invention is a laminated film comprising a polycarbonate resin film obtained by melt-extrusion molding a polycarbonate resin containing a structural unit derived from a dihydroxy compound (b) represented by the following formula (2) Wherein the film has a static friction coefficient of not less than 1.8 in a state in which the polycarbonate resin films are in surface contact with each other, and a surface of the polycarbonate resin film and a non- And a static friction coefficient in a contact state of not less than 0.01 and less than 1.8.

(2)

(In the formula (2), R ₁ to R ₄ each independently represent a hydrogen atom, a substituted or unsubstituted alkyl group having 1 to 20 carbon atoms, a substituted or unsubstituted cycloalkyl group having 6 to 20 carbon atoms, Unsubstituted aryl group having 6 to 20 carbon atoms, X is a substituted or unsubstituted alkylene group having 2 to 10 carbon atoms, a substituted or unsubstituted cycloalkylene group having 6 to 20 carbon atoms, or a substituted or unsubstituted C6- And m and n are each independently an integer of 1 to 5,

In the first or second aspect of the present invention, it is preferable that the absolute value of the in-plane retardation of the polycarbonate resin film is 10 nm or less.

In the first or second aspect of the present invention, it is preferable that the polycarbonate resin has a glass transition temperature of 110 캜 or more and 160 캜 or less.

In the first or second aspect of the present invention, it is preferable that the dihydroxy compound (a) or the dihydroxy compound (b) is 9,9-bis (4- (2-hydroxyethoxy) .

In the first or second aspect of the present invention, it is preferable that the polycarbonate resin film has a thickness of 30 占 퐉 or more and 300 占 퐉 or less, a total light transmittance of 85% or more, and a haze of 2% or less.

In the first or second aspect of the present invention, it is preferable that the numerical contact angle (? ₀ ) of the surface of the polycarbonate resin film before the masking film is laminated on the polycarbonate resin film, And the absolute value |? _{0 -} ? ₁ | of the difference between the surface contact angle (? ₁ ) of the surface of the polycarbonate resin film after peeling off the masking film from the polycarbonate resin film is 20 ° or less.

In the first or second aspect of the present invention, the peel strength of the masking film to the polycarbonate resin film according to JIS-Z0237 (2009) is not less than 5 mN / 10 mm and not more than 200 mN / 10 mm .

In the first or second aspect of the present invention, it is preferable that the base layer of the masking film is made of a polyolefin resin.

In the first or second aspect of the present invention, it is preferable that the adhesive layer of the masking film is made of a modified polyolefin resin.

A third aspect of the present invention is a film wound laminate obtained by winding a film laminate according to the first or second aspect of the present invention into a cylindrical core and rolling it.

In the third aspect of the present invention, it is preferable that the winding displacement width of the side end portion of the film wound laminate is 4 mm or less.

A fourth aspect of the present invention is the method for producing a film wound laminate according to the third aspect of the present invention, wherein the polycarbonate resin is melt-extruded and a metal mirror roll having a maximum surface height (Rz) A step of forming a polycarbonate resin film by cooling the film to form a film laminate by laminating the produced polycarbonate resin film and a masking film, and a step of forming the film laminate into a roll core And a step of winding the film.

In the fourth aspect of the present invention, in the step of winding the film laminate into a cylindrical winding core in roll form, the winding tension per 1 m film width is preferably 80 N / m or more and 200 N / m or less.

According to the present invention, it is possible to provide a film laminate which can be used for an optical use member and does not cause cracks on the surface or end portion of the polycarbonate resin film during winding or trimming and is excellent in transparency and thickness accuracy, , It is possible to obtain a uniform film winding laminate without winding displacement or winding crimping.

Hereinafter, a film laminate formed by laminating a polycarbonate resin film and a masking film as one example of an embodiment of the present invention, and a film laminate obtained by winding the film laminate into a roll will be described. However, the present invention is not limited to the embodiments described below.

<Polycarbonate resin>

The polycarbonate resin used in the present invention is a polycarbonate resin containing a structural unit derived from a dihydroxy compound (a) having a moiety represented by the following formula (1) in a part of its structure, and the polycarbonate resin is melted The polycarbonate resin film formed by extrusion molding is not brittle. The term &quot; polycarbonate resin &quot; in the present invention includes the so-called &quot; polyester carbonate resin &quot;.

(3)

In order to obtain the brittle non-fractured polycarbonate resin film, it is important to appropriately set various production conditions such as polymerization conditions and molding conditions together with the molecular design of the polycarbonate resin. From the viewpoint of molecular design of the polycarbonate resin, by using a dihydroxy compound as described below as a raw material or by using various dihydroxy compounds in combination, flexibility is imparted to the polycarbonate resin, or a glass transition temperature Is adjusted to an appropriate range, a polycarbonate resin excellent in toughness can be obtained. Further, in order to exhibit inherent mechanical properties of the polycarbonate resin, it is necessary to advance the reaction to a sufficient molecular weight at the time of polymerization of the polycarbonate resin. Further, in the melt extrusion molding, it is possible to form the film without lowering the mechanical properties of the polycarbonate resin by appropriately setting the conditions of the extruder according to the properties of the resin and suppressing thermal decomposition at the time of processing. The details of each will be described later.

[Dihydroxy compound (a)]

The dihydroxy compound (a) is a dihydroxy compound having a moiety represented by the above formula (1) in a part of its structure. As described later, the polycarbonate resin film obtained by melt- And is not particularly limited as long as it has a static friction coefficient of not less than 1.8 in a state in which the polycarbonate resin films are in surface contact with each other.

Of these, the dihydroxy compound (a) is preferably a dihydroxy compound (b) represented by the following formula (2). This is because the obtained polycarbonate resin film is excellent in various optical properties such as optical isotropy and optical anisotropy of the stretched film and is not particularly remarkably brittle fractured.

[Chemical Formula 4]

In the formula (2), R ₁ to R ₄ each independently represent a hydrogen atom, a substituted or unsubstituted alkyl group having 1 to 20 carbon atoms, a substituted or unsubstituted cycloalkyl group having 6 to 20 carbon atoms, Substituted or unsubstituted aryl group having 6 to 20 carbon atoms, X is a substituted or unsubstituted alkylene group having 2 to 10 carbon atoms, a substituted or unsubstituted cycloalkylene group having 6 to 20 carbon atoms, M and n are each independently an integer of 1 to 5;

Specific examples thereof include 9,9-bis (4- (2-hydroxyethoxy) phenyl) fluorene, 9,9-bis (4- (2-hydroxyethoxy) , 9- bis (4- (2-hydroxyethoxy) -3-isopropylphenyl) fluorene, 9,9-bis , 9,9-bis (4- (2-hydroxyethoxy) -3-tert-butylphenyl) fluorene, ) Fluorene, 9,9-bis (4- (2-hydroxyethoxy) -3-phenylphenyl) fluorene, 9,9- Dimethyl phenyl) fluorene, 9,9-bis (4- (2-hydroxyethoxy) -3-tert- butyl-6-methylphenyl) fluorene, (2-hydroxypropoxy) phenyl) fluorene and the like, and from the viewpoint of heat resistance and flexibility of the obtained polycarbonate resin, 9,9-bis (4- (2-hydroxyethoxy) phenyl) Fluorene, 9,9-bis (4- (2- ) -3-methylphenyl) fluorene, and particularly preferably a 9,9-bis (4- (ethoxy) phenyl) 2-hydroxy-fluorene.

Among the polycarbonate resins containing a structural unit derived from the dihydroxy compound (a) having a moiety represented by the above formula (1) in part of the structure, the dihydroxy compound (b) represented by the formula (2) A film using a polycarbonate resin containing a derived structural unit has an excellent heat resistance due to a bulk molecular structure and also has a structure capable of imparting flexibility to the main chain so that it also has excellent mechanical properties. Thus, by selecting the dihydroxy compound (b) represented by the formula (2) as a monomer, it becomes possible to obtain a polycarbonate resin which is not brittle.

[Other dihydroxy compounds]

The polycarbonate resin used in the present invention may further contain a structural unit derived from a dihydroxy compound other than the dihydroxy compound (a) and the dihydroxy compound (b).

Among them, a resin containing a structural unit derived from a dihydroxy compound (c) having a moiety represented by the following formula (3) in a part of its structure is preferable because the optical properties and moldability of the polycarbonate resin are improved desirable. The dihydroxy compound (c) is different from the dihydroxy compound (a) and the dihydroxy compound (b), and the moiety represented by the formula (3) is a part of -CH ₂ -OH Shall be excluded.

[Chemical Formula 5]

Examples of the dihydroxy compound (c) having a moiety represented by the above formula (3) in a part of its structure include, for example, anhydric alcohol represented by the dihydroxy compound represented by the formula (4) And dihydroxy compounds having a cyclic ether structure typified by spiroglycol represented by formula (5), and the like.

Alcohol anhydrides generally have a plurality of hydroxy groups obtained by dehydrating cyclization of saccharides or their derivatives. The dihydroxy compound having a cyclic ether structure is a compound having a structural part having a cyclic ether structure and two hydroxy groups.

In the dihydroxy compounds having an alcoholic anhydride and a cyclic ether structure, all of the hydroxy groups may be bonded directly to the cyclic structure or may be bonded to the cyclic structure via a substituent. The annular structure may or may not be a single piece.

In the case of alcohols perhydric alcohols and dihydroxy compounds having a cyclic ether structure in the molecule, it is preferable that a plurality of cyclic structures are present, more preferably two cyclic structures, and the two cyclic structures It is more preferable that the same. In addition, a plurality of annular structures may be looped.

More specifically, examples of alcohols per anhydride include dihydroxy compounds represented by the following formula (4), and examples thereof include isosorbide, isomannide and isoidide in the relation of stereoisomers have.

[Chemical Formula 6]

The dihydroxy compound represented by the formula (4) is an ether diol which can be prepared from saccharides using a biogenic material as a raw material. In particular, isosorbide can be produced at low cost by dehydrating D-glucose obtained from starch and dehydrating it, and it is possible to obtain it abundantly as resources, and the optical properties and moldability of the polycarbonate resin are improved. By these circumstances, isosorbide is most preferable.

Examples of dihydroxy compounds having a cyclic ether structure include dihydroxy compounds having a cyclic ether structure represented by the following formula (5).

(7)

In the formula (5), R ₅ to R ₈ are each independently an alkyl group having 1 to 3 carbon atoms.

Specific examples of the dihydroxy compound having a cyclic ether structure include 3,9-bis (1,1-dimethyl-2-hydroxyethyl) -2,4,8,10-tetraoxa (5.5) undecane (commonly known as spiroglycol), 3,9-bis (1,1-diethyl-2-hydroxyethyl) -2,4,8,10-tetraoxaspiro 3,9-bis (1,1-dipropyl-2-hydroxyethyl) -2,4,8,10-tetraoxaspiro (5.5) undecane and the compound represented by the following formula (6).

[Chemical Formula 8]

These may be used alone or in combination of two or more.

The polycarbonate resin used in the present invention may contain a structural unit derived from other dihydroxy compound other than the dihydroxy compound (c).

More specifically, a dihydroxy compound represented by the following formula (7), a dihydroxy compound represented by the following formula (8), a dihydroxy compound represented by the following formula (9) Hydroxy compounds, and also bisphenols.

[Chemical Formula 9]

In the formula (7), R ₉ represents a substituted or unsubstituted monocyclic cycloalkylene group having 4 to 20 carbon atoms.

[Chemical formula 10]

In the formula (8), R ₁₀ represents a substituted or unsubstituted monocyclic cycloalkylene group having 4 to 20 carbon atoms.

(11)

In the formula (9), R ₁₁ represents a substituted or unsubstituted alkylene group having 2 to 10 carbon atoms, and p is an integer of 2 to 120.

[Chemical Formula 12]

In the formula (10), R ₁₂ represents an alkylene group having 2 to 20 carbon atoms.

The dihydroxy compound represented by the formula (7) includes a compound containing a cycloalkylene group having a monocyclic structure. By employing a monolithic structure, it is possible to improve the toughness when the obtained polycarbonate resin is used as a film. In addition, a compound containing a five-membered ring structure or a six-membered ring structure is usually used. 5-atom cyclic structure or 6-atom cyclic structure, the heat resistance of the resulting polycarbonate resin can be increased. The 6-membered ring structure may be fixed to the chair type or the boat type by covalent bonding.

Specific examples include 1,2-cyclopentanediol, 1,3-cyclopentanediol, 1,2-cyclohexanediol, 1,3-cyclohexanediol, 1,4-cyclohexanediol, -Cyclohexanediol, and the like.

The dihydroxy compound represented by the formula (8) includes a compound containing a cycloalkylene group having a monocyclic structure. By employing a monolithic structure, it is possible to improve the toughness when the obtained polycarbonate resin is used as a film. In general, R ₁₀ in the formula (8) includes various isomers represented by the following formula (11). Specific examples thereof include 1,2-cyclohexanedimethanol, 1,3-cyclohexanedimethanol and 1,4-cyclohexanedimethanol.

[Chemical Formula 13]

In the formula (11), R ₁₃ represents a hydrogen atom or a substituted or unsubstituted alkyl group having 1 to 12 carbon atoms.

Of the specific examples of the alicyclic dihydroxy compounds described above, cyclohexanedimethanol is particularly preferable, and from the viewpoints of availability, ease of handling, and mechanical properties of the obtained polycarbonate resin, 1,4-cyclohexane di Methanol, 1,3-cyclohexanedimethanol and 1,2-cyclohexanedimethanol are preferable.

The above-exemplified compounds are examples of the alicyclic dihydroxy compounds usable in the present invention and are not limited to them at all. These alicyclic dihydroxy compounds may be used singly or in combination of two or more kinds.

Specific examples of the dihydroxy compound represented by the formula (9) include diethylene glycol, triethylene glycol, polyethylene glycol (number average molecular weight: 150-2000), and among these, diethylene glycol, polyethylene glycol Number average molecular weight: 150 to 2,000).

Specific examples of the dihydroxy compound represented by the formula (10) include ethylene glycol, propylene glycol, 1,4-butanediol, 1,6-hexanediol, etc. Among them, propylene glycol, 1,4- Butanediol is preferred.

The polycarbonate resin used in the present invention is a polycarbonate resin having a structural unit derived from the dihydroxy compound represented by the formula (7), a structural unit derived from the dihydroxy compound represented by the formula (8) , Structural units derived from the dihydroxy compound represented by the formula (8) and structural units derived from the dihydroxy compound represented by the formula (10), among the structural units derived from the dihydroxy compound represented by the formula 9), and more preferably contains a structural unit derived from a dihydroxy compound represented by the above formula (9).

Examples of the bisphenols include 2,2-bis (4-hydroxyphenyl) propane (i.e., bisphenol A), 2,2-bis (4-hydroxy- Propane, 2,2-bis (4-hydroxy-3,5-diethylphenyl) propane, Bis (4-hydroxyphenyl) pentane, 2,4'-dihydroxy-diphenylmethane, bis (4-hydroxyphenyl) , Bis (4-hydroxyphenyl) methane, 1,1-bis (4-hydroxyphenyl) ethane, 3,3- (4-hydroxyphenyl) sulfone, 2,4'-dihydroxydiphenyl sulfone, bis (4-hydroxyphenyl) sulfide, 4,4'-dihydroxy Phenyl ether, 4,4'-dihydroxy-3,3'-dichlorodiphenyl ether, and 4,4'-dihydroxy-2,5-diethoxydiphenyl ether.

[Polycarbonate resin]

The content ratio of the structural unit derived from the dihydroxy compound (a) in the structural unit derived from the dihydroxy compound contained in the polycarbonate resin used in the present invention is preferably 10% by mole or more, more preferably 18% More preferably 20 mol% or more, and particularly preferably 25 mol% or more. The upper limit is preferably 90 mol% or less, more preferably 85 mol% or less, particularly preferably 80 mol% or less.

Here, the dihydroxy compound (a) also includes a dihydroxy compound (b).

The content ratio of the structural unit derived from the dihydroxy compound (a) is not less than the lower limit value described above, so that the heat resistance is improved. In addition, since the content ratio is not more than the upper limit value, the processing temperature is not increased and the moldability is improved.

When the structural unit derived from the dihydroxy compound (c) contained in the polycarbonate resin for use in the present invention contains a structural unit derived from the dihydroxy compound (c), the lower limit of the content ratio is 5 mol% or more , More preferably at least 10 mol%, particularly preferably at least 15 mol%. The upper limit is preferably 90 mol% or less, more preferably 85 mol% or less, particularly preferably 80 mol% or less.

The content ratio of the structural unit derived from the dihydroxy compound (c) is not lower than the lower limit value described above, so that the heat resistance is improved. In addition, since the content ratio is equal to or less than the upper limit value, the water absorption rate is not increased, and the film is not deformed.

The content ratio of the structural unit derived from the dihydroxy compound contained in the polycarbonate resin used in the present invention to the structural units derived from other dihydroxy compounds other than the above (a) and (c) Is preferably 0.02 mol% or more, more preferably 0.05 mol% or more, and particularly preferably 0.1 mol% or more. Further, it is preferably 60 mol% or less, more preferably 50 mol% or less, particularly preferably 40 mol% or less.

When the content ratio of the structural units derived from other dihydroxy compounds other than the above (a) and (c) falls within the above range, the flowability during molding is improved, Loses. Also, heat resistance is improved.

The glass transition temperature (Tg) of the polycarbonate resin used in the present invention is preferably 110 占 폚 or higher, more preferably 115 占 폚 or higher, and particularly preferably 120 占 폚 or higher. The temperature is preferably 160 占 폚 or lower, more preferably 157 占 폚 or lower, and particularly preferably 155 占 폚 or lower.

The glass transition temperature is 110 占 폚 or higher, so that heat resistance is excellent and it is difficult to cause dimensional change after film forming. Further, the glass transition temperature is 160 占 폚 or less, which results in excellent molding stability at the time of film forming, transparency of the film, and mechanical properties.

As the method of setting the glass transition temperature to the above range, a method of suitably adjusting the composition ratio of the dihydroxy compound constituting the polycarbonate resin within the range described in this specification can be exemplified.

The molecular weight of the polycarbonate resin used in the present invention can be represented by the reduced viscosity. The reduced viscosity is measured by using a Ureter Viscosity Tube at a temperature of 20.0 ° C ± 0.1 ° C, precisely adjusting the polycarbonate concentration to 0.6 g / dl using methylene chloride as a solvent. The lower limit of the reduced viscosity is preferably 0.25 dl / g, more preferably 0.30 dl / g. The upper limit of the reduced viscosity is preferably 1.20 dl / g, more preferably 1.00 dl / g, and still more preferably 0.80 dl / g.

If the reduced viscosity of the polycarbonate resin is not lower than the lower limit, the mechanical strength of the molded article is not excessively reduced. On the other hand, if the reduced viscosity is below the upper limit value, there is little fear that the fluidity at the time of molding is lowered, and productivity and moldability are hardly lowered.

The polycarbonate resin to be used in the present invention can be produced by a commonly used polymerization method and can be any of an ester exchange method of reacting with a phosgene method or a carbonic acid diester. Among them, in the presence of a polymerization catalyst, an ester exchange method in which the dihydroxy compound (a), the dihydroxy compound (c), other dihydroxy compounds used as needed, and a carbonic acid diester are reacted .

The ester exchange method can be carried out by neutralizing the dihydroxy compound (a), the dihydroxy compound (c), other dihydroxy compounds, if necessary, and the carbonic acid diester with a basic catalyst and further with the basic catalyst And then an ester exchange reaction is carried out.

Typical examples of the carbonic acid diester include diphenyl carbonate, ditolyl carbonate, bis (chlorophenyl) carbonate, m-cresyl carbonate, dinaphthyl carbonate, bis (biphenyl) carbonate, diethyl carbonate, dimethyl carbonate, di Butyl carbonate, dicyclohexyl carbonate, and the like. Of these, diphenyl carbonate is particularly preferably used.

In addition, as described above, the term &quot; polycarbonate resin &quot; in the present invention includes the so-called &quot; polyester carbonate resin &quot;. In the case of using a polyester carbonate resin, a part of the carbonic acid diester is substituted with a dicarboxylic acid or an ester thereof (hereinafter referred to as a dicarboxylic acid compound). Examples of such dicarboxylic acid compounds include dicarboxylic acids such as terephthalic acid, isophthalic acid, oxalic acid, succinic acid, 1,4-cyclohexanedicarboxylic acid, and their methyl esters and phenyl esters.

In the polycarbonate resin used in the present invention, the content ratio of the structural unit derived from the dicarboxylic acid compound is preferably 45 By mole or less, more preferably 40% by mole or less. When the content of the dicarboxylic acid compound is 45 mol% or less, the possibility that the polymerization does not proceed to the desired molecular weight due to the lowering of the polymerizability is reduced.

<Polycarbonate resin film>

The polycarbonate resin film used in the present invention is produced using the polycarbonate resin. At this time, various commonly used additives may be added within the range not hindering the effect of the present invention. Specifically, antioxidants, antistatic agents, ultraviolet absorbers, flame retardants, release agents, lubricants, and antistatic agents can be given.

The polycarbonate resin to be used in the present invention may be, for example, an aromatic polycarbonate, an aromatic polyester, an aliphatic polyester, a polyamide, a polystyrene, a styrene / methacrylic acid ester copolymer, a styrene / methacrylic acid copolymer, Butadiene-styrene copolymer (ABS), acrylonitrile-styrene copolymer (AS), polymethyl methacrylate (PMMA), polyolefin, amorphous polyolefin, poly It may be kneaded with one or more kinds of thermoplastic resins such as lactic acid, polybutylene succinate, rubber, elastomer, etc., and used as polymer alloys.

By using a suitable amount of a thermoplastic resin having excellent mechanical properties and melt processability as a modifier and using such a mixture as described above, mechanical properties and melt processability can be improved while maintaining required optical properties and heat resistance.

In order to impart flexibility or melt processability to the polycarbonate resin to be used in the present invention, a method of adding a plasticizer type and appropriately lowering the glass transition temperature of the resin may be used. The plasticizer is not particularly limited as long as it can lower the glass transition temperature of the polycarbonate resin used in the present invention, and may be a compound having a long-chain alkyl group or an aryl group.

Specific examples include phthalic acid esters such as phthalic acid bis (2-ethylhexyl), adipic acid esters such as adipic acid bis (2-ethylhexyl), fatty acids such as stearic acid and calcium stearate, ethylene glycol distearate , Phosphoric acid esters such as tricresyl phosphate, tris (2-ethylhexyl) phosphate, fatty acid amides, higher alcohols such as stearyl alcohol, and liquid paraffin.

Low molecular weight polymers can also be used as modifiers. Specific examples thereof include styrene oligomers, polyhydroxy polyolefin oligomers (PolyTile: registered trademark), and terpene phenol resins.

When the above-mentioned various modifiers are used in excess, the transparency of the resin may be lowered or the amount of the volatile component during the melt processing may increase, which may cause foreign matter. On the other hand, if the amount is too small, a sufficient reforming effect can not be obtained. Therefore, the addition amount of the polycarbonate resin to be used in the present invention is preferably from 0.1 mass% to 10 mass%, more preferably from 0.2 mass% to 5 mass%, particularly preferably from 0.3 mass% to 3 mass% Or less.

The modifier may be mixed with a tumbler, a super mixer, a plotter, a V-type blender, a Nauta mixer, a Banbury mixer, an extruder or the like before performing various molding.

It is important that the polycarbonate resin film used in the present invention is obtained by melt extrusion molding. For example, the polycarbonate resin film can be formed by using a T-die molding method, an inflation molding method, or the like, and particularly, a T-die molding method is preferable.

Generally, as a method for producing a polycarbonate resin film, a solution casting method or the like is also employed. However, the method using these organic solvents has problems in terms of productivity and environmental load, such as obtaining a film having a uniform thickness and excellent surface smoothness, while requiring a low yield and treating the used organic solvent. Therefore, production by melt extrusion molding is preferable.

For example, in the case of the T-die molding method, the polycarbonate resin and, if necessary, various blended additives are blended, the pellets prepared by adding various additives to the polycarbonate resin in advance, the polycarbonate resin, Is added to the extruder through a feeder, melt-kneaded, and extruded while being molded into a film by a T-die. At this time, the set temperature of the extruder and the T die is usually 220 deg. C or higher, preferably 280 deg. C or lower, more preferably 220 deg. C or higher and 250 deg. C or lower.

The resin temperature at the outlet of the extruder is preferably 300 ° C or lower, more preferably 280 ° C or lower, and particularly preferably 260 ° C or lower. When the resin temperature is higher than 300 ° C, thermal decomposition of the polycarbonate resin is promoted to lower the molecular weight, or defects resulting from the foaming of the resin may be generated in the resulting film, and the strength of the film may be lowered. The resin temperature at the outlet of the extruder is controlled by the rotation speed of the screw, the composition of the screw element and the throughput of resin, in addition to the set temperature of the extruder and the T die described above.

In the present invention, the shape of the extruder is not limited, but a uniaxial or biaxial extruder is used. Among them, it is preferable to use a biaxial extruder which is capable of removing moisture and residual low-molecular components in the polycarbonate resin by desulfurization by installing a vent hole and reducing pressure by using a vacuum pump or the like. When a polycarbonate resin containing a large amount of water or remaining low molecular weight is melted at a high temperature, there is a possibility that a large molecular weight is lowered. Therefore, the molecular weight reduction of the resin can be suppressed by vacuum devolatilization.

The polycarbonate resin film used in the present invention can be obtained by bringing the resin extruded while being molded into a film into contact with the castrol and cooling it, further bringing it into contact with at least one cooling roll at the downstream end, Further, the surface of the film may be smoothed by using a touch roll, a touch belt, or the like.

At this time, it is preferable that at least one of the cast roll or the touch roll is a metallic mirror roll, and that the maximum height Rz of the surface of the mirror roll measured in accordance with JIS-B0601 (2001) is 0.3 占 퐉 or less desirable. Generally, if there is minute unevenness on the roll surface, the unevenness is transferred to the product film. In applications in which high precision film thickness precision is required, such as in optical applications, such transfer irregularities can not be overlooked. Therefore, the above range is preferable as the upper limit of the size of the minute irregularities on the roll surface.

The setting temperature of the castrol is preferably Tg-50 DEG C or more and Tg-5 DEG C or less with respect to the glass transition temperature (Tg) of the polycarbonate resin.

The polycarbonate resin film used in the present invention preferably has a thickness of 30 占 퐉 or more and 300 占 퐉 or less. For example, when combined with a display device, it is possible to make the thickness of the product thinner and reduce the intensity of the light source as long as predetermined optical characteristics are exhibited. On the other hand, in order to maintain ease of handling, it is preferable that the thickness is 30 占 퐉 or more. Further, it is preferable that the thickness is not more than 300 占 퐉 so as not to suppress the roll-up of wrinkles in the form of a laminate or excessively reduce the total light transmittance.

The polycarbonate resin film used in the present invention preferably has a water absorption rate of more than 1.0% by mass and 2.0% by mass or less, more preferably 1.1% by mass or more and 1.5% by mass or less. When the water absorption rate is greater than 1.0% by mass, it is easy to design the adhesive freely when bonding the film to another film or the like, and adhesiveness can be secured easily. On the other hand, if the water absorption rate is 2.0% by mass or less, the durability of optical properties under a high temperature and high humidity environment can be secured.

In addition, the water absorption rate is measured in accordance with &quot; method for obtaining plastic-water absorption rate &quot; described in JIS-K7209 (2000) for a film having a thickness of 100 to 400 mu m.

In order to set the absorption rate of the polycarbonate resin film to be used in the present invention within the above range, a method of suitably adjusting the composition ratio of the dihydroxy compound constituting the polycarbonate resin within the range described in this specification can be exemplified .

The polycarbonate resin film used in the present invention preferably has a total light transmittance of 85% or more, more preferably 87% or more, and particularly preferably 89% or more. When the transmittance is in the above-mentioned range, a film with little discoloration is obtained. For example, when combined with a display device, a high display quality can be realized.

The polycarbonate resin film used in the present invention preferably has a haze of 2% or less, more preferably 1.5% or less, particularly preferably 1% or less. When the haze is within the above range, a film having high transparency can be obtained and can be preferably used as an optical use member.

The polycarbonate resin film used in the present invention preferably has an absolute value of the in-plane retardation (Re) of 10 nm or less, more preferably 8 nm or less, and particularly preferably 6 nm or less. When the absolute value of the in-plane retardation is within the above-mentioned range, a disc having a small optical anisotropy is obtained, and a retardation film having a desired in-plane retardation with little fluctuation is obtained by stretching the original film under a predetermined condition. .

In the polycarbonate resin film used in the present invention, the total light transmittance, the haze, and the absolute value of the in-plane retardation (Re) are set within the above-mentioned range. The composition ratio of the dihydroxy compound constituting the polycarbonate resin A method in which the polycarbonate resin film is appropriately adjusted, a method in which the film is taken under conditions in which the molecular orientation is not likely to be applied in the production process of the polycarbonate resin film, a method using a mirror-surface roll, And a method of appropriately adjusting within the range described can be preferably exemplified.

The static friction coefficient measured based on JIS-K7125 (1999) is 1.8 or more in a state where the polycarbonate resin films used in the present invention are in surface contact with each other. With a static friction coefficient of 1.8 or more, the surface of the polycarbonate resin film is excellent in smoothness, and thus a polycarbonate resin film can be preferably used as an optical use member. However, as will be described later, when only the polycarbonate resin film like this is wound to produce a film wound laminate, there is a possibility that winding displacement and winding wrinkle may occur.

As a method of making the static friction coefficient measured on the basis of JIS-K7125 (1999) with the polycarbonate resin films in surface contact with each other at 1.8 or more, And the like. Alternatively, the coefficient of static friction is influenced not only by the physical shape of the surface but also by the chemical affinity of the polycarbonate resin films in a state of face-to-face contact with each other. Therefore, the dihydroxy compound constituting the polycarbonate resin And a method in which the composition ratio is within the range described in this specification can be exemplified.

<Masking film>

The masking film used in the present invention has an adhesive layer formed on one side of the substrate layer. That is, the surface of the masking film on the side of the adhesive layer serves as an adhesive surface, and the side of the substrate opposite to the masking film serves as a non-adhesive surface.

The base layer is not particularly limited, and examples thereof include films such as polyester resins and polyolefin resins. Among them, a film using a polyolefin resin such as polyethylene or polypropylene is preferable from the viewpoint of chemical affinity with a preferable adhesive layer described later and productivity of a masking film.

The adhesive layer is not particularly limited, and examples thereof include acrylic resins, urethane resins, ethylene / vinyl acetate copolymer resins, and modified polyolefin resins. Among them, it is preferable to use a modified polyolefin resin to which an acidic functional group or a basic functional group has been added, because contamination of the product by the outgassing component and the occurrence of adhesive residue at the time of peeling the masking film from the laminated film of the present invention Do.

The method for producing the masking film to be used in the present invention is not particularly limited and includes a co-extrusion method in which a base layer and an adhesive layer are laminated by co-extrusion, a cast coating method in which an adhesive layer is applied in- A hot pressing method in which a base layer and an adhesive layer are separately formed and laminated by heat fusion. Of these, the co-extrusion method is particularly preferable from the viewpoint of reducing the risk of product contamination due to volatilization of the residual solvent and increasing the thickness accuracy.

The thickness of the masking film used in the present invention can be arbitrarily selected in consideration of ease of handling and rigidity and toughness of the film laminate of the present invention. Among them, it is preferable that it is not less than 30 탆 and not more than 70 탆.

The adhesive strength of the adhesive layer of the masking film used in the present invention is preferably 10 m or less in terms of the adhesive strength in accordance with JIS-Z0237 (2009) when the masking film is peeled from the polycarbonate resin film in the film laminate of the present invention Can be evaluated as the peel strength measured at a peel angle of 180 deg. And a peel rate of 100 mm / min. The peel strength is preferably 5 mN / 10 mm or more and 200 mN / 10 mm or less. If the peel strength is 5 mN / 10 mm or more, the polycarbonate resin film and the masking film in the film laminate and the film wound laminate of the present invention do not easily peel off during handling. When the peel strength is 200 mN / 10 mm or less, the polycarbonate resin film is free from peeling marks or peeling marks and can be sufficiently protected.

&Lt; Film laminate &

The film laminate of the present invention is a laminate of the polycarbonate resin film and the masking film. At this time, by laminating the polycarbonate resin film so that the adhesive surface of the masking film is on one side of the polycarbonate resin film, the film laminate of the present invention described later can be provided with a surface of the polycarbonate resin film, But is a mirror-like film, and is a uniform film laminate without winding displacement or winding.

The method for producing the film laminate of the present invention is not particularly limited. For example, there may be used a method in which a polycarbonate resin film and a masking film are separately prepared, then laminated in-line as they are without winding, A roll, and a method in which a polycarbonate resin film is produced and then the masking film is loosened from the roll and laminated in-line.

As described above, when the polycarbonate resin films used in the present invention are in surface contact with each other, their activity is insufficient. Thus, there is a fear that winding rolls and rolled wrinkles may occur in the case of the film winding layer. In this case, JIS-K7125 ), The static friction coefficient measured is 1.8 or more. On the other hand, in the film laminate of the present invention, the static friction coefficient measured based on JIS-K7125 (1999) when the non-sticking side of the polycarbonate resin film and the masking film are in contact with each other is 0.01 or more 1.8, preferably 0.02 or more and 1.4 or less, particularly preferably 0.03 or more and 1.0 or less. When the coefficient of static friction is in the above range, it is possible to prevent winding displacement and winding of the film winding laminate of the present invention to be described later.

In the film laminate of the present invention, the numerical contact angle (? ₀ ) of the surface of the polycarbonate resin film before lamination of the masking film to the polycarbonate resin film, and the above masking film are laminated on the polycarbonate resin film, And the absolute value |? _0- ? ₁ | of the difference from the numerical contact angle? ₁ of the surface of the polycarbonate resin film after peeling off the masking film from the polycarbonate resin film is preferably 20 or less. Here, the &quot; water contact angle &quot; is a value measured in accordance with JIS-K6768 (1999). The numerical contact angle [theta] ₀ is preferably in the range of 70 [deg.] To 85 [deg.], And the numerical contact angle [theta] ₁ is preferably in the range of 85 [deg.] To 100 [deg.]. When | _{0 -} ? ₁ | is 20 or less, even after the peeling of the masking film, adhesive residue or scratches on the surface of the polycarbonate resin film are very few, and the smoothness of the surface is maintained , A polycarbonate resin film can be preferably used as an optical use member.

The method of setting | _{0 -} ? ₁ | to 20 ° or less includes a method in which the composition ratio of the dihydroxy compound constituting the polycarbonate resin used in the present invention is within the range described in this specification, A method of setting the kind and the peel strength of the adhesive layer of the masking film within the ranges described in the present specification, and the like are preferably exemplified.

&Lt; Film wound laminate &

In the film wound laminate of the present invention, the film laminate of the present invention is rolled up into a cylindrical reed. More specifically, it can be obtained by laminating the polycarbonate resin film and the masking film, and then winding the film in a roll shape continuously around a cylindrical core. At this time, it is preferable that the polycarbonate resin can be sufficiently protected by winding the masking film out of the film laminate so that the masking film always comes to the outside of the polycarbonate resin film.

The winding core used in the production of the film winding laminate of the present invention is not particularly limited, and may be various ones made of paper, plastic, fiber-reinforced plastic, metal, or the like, And the like.

In the film wound laminate of the present invention, it is preferable that the winding displacement width of the side end portion is 4 mm or less. The take-off width of the side end portion is more preferably 2 mm or less, particularly preferably 1 mm or less. The take-off width of the side end portion refers to the maximum width of the unevenness formed on the side surface of the film wound layered body on the roll. When the take-off width of the side end portion is 4 mm or less, there is a problem that the yield of the film is squeezed due to an unexpected situation during transportation of the film wound laminate, and the problem that the unwinding direction becomes unstable when the film laminate is unwound from the film winding, It is difficult to cause problems such as snaking.

The winding tension per 1 m of the film width when the film wound laminate of the present invention is produced is suitably set in accordance with the thickness of the polycarbonate resin film and the kind of the masking film. In particular, if the winding tension is 80 N / m or more and 200 N / m or less, it is preferable that winding tension and winding swelling are not caused. In addition, if the winding tension is 200 N / m or less, there is no case where the winding wrinkles are generated.

Example

In order to further illustrate the present invention in more detail, the following examples are given. However, the present invention is not limited at all by the following examples.

<Evaluation method>

Evaluation of polycarbonate resin and film was carried out according to the following method.

(1) Glass transition temperature (Tg)

About 10 mg of the polycarbonate resin was measured by heating at a temperature raising rate of 20 캜 / minute using a differential scanning calorimeter (DSC 220, manufactured by SII Nanotechnology Co., Ltd.) according to JIS-K7121 (1987) And the extrapolated glass transition start temperature which is the temperature at the point of intersection between the straight line extending to the high temperature side and the tangent line at the point where the curve gradient of the step change portion of the glass transition becomes the maximum is obtained, Temperature.

(2) Presence or absence of brittle fracture

First, a polycarbonate resin was melt-extruded to produce a film having a width of 200 mm or more and a thickness of 100 占 퐉. A rectangular test piece having a length of 40 mm in the flow direction MD of the film and a width of 10 mm in the width direction TD was produced from the vicinity of the central portion in the width direction of the film.

The gap between the left and right joint surfaces of the vise was opened to 40 mm, and both ends of the test piece were fixed in the joint surface. Next, the gap between the left and right joint surfaces was narrowed at a velocity of 2 mm / sec or less so that the entire film was compressed in the joint surface while the film did not protrude from the joint surface of the vise.

"Cracked" when the specimen was cracked into two pieces (or more than three pieces) from the bend until the joint between the joints completely came to a close; "When the test piece was bent without being cracked Quot; no crack &quot;.

Tests were repeated five times on the same type of film, and those having "cracks" four times or more were evaluated as "x: brittle failure" and those having three or less "cracks" were evaluated as "○: It is not. "

(3) Measurement of total light transmittance and haze

The total light transmittance and haze of the polycarbonate resin film were measured using a haze meter (HR-100, manufactured by Murakami Color Research Laboratory) according to JIS-K7136 (2000) and JIS-K7361-1 .

A total light transmittance of 85% or more was evaluated as good (good), and a case of less than 85% was evaluated as poor (poor). The haze was evaluated as good (good) when the haze was 2% or less and good (poor) when the haze was exceeded by 2%.

(4) In-plane retardation

The phase difference was measured using a phase difference measuring apparatus (manufactured by Oji Instruments Co., Ltd., KOBRA-WR) under the conditions of the low phase difference mode, the order selection mode, and the average measurement frequency of 5 times. The measurement film was loaded with the side on which the masking film was peeled to the side of the paper, and the side to which the masking film was not adhered to the top side. (Good) when the absolute value of the retardation was 10 nm or less and x (defective) when the absolute value of the retardation was more than 10 nm.

(5) Measurement of static friction coefficient

In accordance with JIS-K7125 (1999), the coefficient of static friction of the polycarbonate resin film was measured using a coefficient of friction meter (manufactured by Intesco). In the case of laminating the masking film, when the static friction coefficient between one surface of the polycarbonate resin film and the non-sticking surface of the masking film is not laminated, the static friction coefficient between the surface and the back surface of the polycarbonate resin film is Table 1 shows the static friction coefficient.

When the coefficient of static friction measured by the above method was less than 1.8, it was evaluated as good (good), and when it was not less than 1.8, it was evaluated as poor (poor).

(6) Measurement of peel strength

After the laminate was laminated on one side of the polycarbonate resin film so that the side of the adhesive layer of the masking film was on the side, the film cut to a width of 10 mm in accordance with JIS-Z0237 (2009) was peeled under the conditions of a peeling angle of 180 ° and a peeling rate of 100 mm / The peel strength was measured.

(Poor) when the peel strength was 5 mN / 10 mm or more and 200 mN / 10 mm or less was rated as good (good), 5 mN / 10 mm or more than 200 mN /

(7) Measurement of numerical contact angle

The polycarbonate resin film after the test of the above (6) was measured for the numerical contact angle (? ₀ ) of the surface on which the masking film was not laminated and the numerical contact angle (? θ ₁ ) were measured to calculate | θ ₀ -θ ₁ |.

(Good) when the value of | _{0 -} ? ₁ | is 20 or less, and x (poor) when the value is greater than 20.

<Examples>

[Example 1]

(Hereinafter abbreviated as &quot; ISB &quot; in some cases) in the case of 1976.0 parts by mass, 9,9- [4- (2-hydroxyethoxy) phenyl] fluorene ), 73.4 parts by mass of polyethylene glycol having an average molecular weight of 1000 (hereinafter sometimes abbreviated as &quot; PEG # 1000 &quot;), and diphenyl carbonate (hereinafter sometimes abbreviated as "DPC" And 3.0 parts by mass of magnesium acetate tetrahydrate (5.0% by mass aqueous solution) as a catalyst were charged into a reaction vessel, and the temperature of the reaction vessel was adjusted to 150 占 폚 , And the raw materials were dissolved while stirring as required (about 15 minutes).

Subsequently, the pressure in the reaction vessel was changed from the atmospheric pressure to 13.3 ㎪, and the temperature of the reaction vessel was elevated to 190 캜 for 1 hour, and the resulting phenol was taken out of the reaction vessel. After the temperature in the reaction vessel was maintained at 190 캜 for 15 minutes, the pressure in the reaction vessel was set to 6.67 제 as a second step, the temperature of the reaction vessel was elevated to 230 캜 for 15 minutes, I pulled it out. Since the stirring torque of the stirrer rises, the temperature is raised to 250 캜 for 8 minutes, and the pressure in the reaction vessel is reduced to 0.200 ㎪ or less in order to remove additional phenol. After the reaction reached a predetermined stirring torque, the resulting reaction product was extruded into water and then pelletized to obtain a polycarbonate resin A of BHEPF / ISB / PEG # 1000 = 44.5 / 55.2 / 0.3 mol% . The glass transition temperature of the polycarbonate resin A was 145 占 폚.

The resulting polycarbonate resin A was vacuum-dried at 80 DEG C for 5 hours and then subjected to vacuum drying using a twin screw extruder (screw diameter: 41 mm, cylinder set temperature: 250 DEG C) equipped with a vacuum degassing apparatus, T die (set temperature: 250 DEG C) Using a film-forming apparatus equipped with a cooling roll (chrome-plated mirror roll, maximum surface height (Rz) = 0.2 占 퐉, set temperature: 70 to 120 占 폚), a nip roll for masking film lamination and a winder, Mu] m of a polycarbonate resin film was produced and laminated with a masking film in-line. Then, the film was taken up in rolls of 1,000 m in a continuous manner on the core of a fiber-reinforced plastic so that the masking film came outward. The masking film was used while being unwound from the roll, "Sanitect, PAC-3-50 THK" (substrate layer: low density polyethylene, adhesive layer: special polyolefin, thickness: 50 μm) manufactured by Sanayakaken Co.,

[Example 2]

571.1 parts by mass of the BHEPF, 267.4 parts by mass of the ISB, diethylene glycol (hereinafter, is sometimes abbreviated as "DEG") to 64.3 parts by weight, the 808.7 parts by weight of the DPC, magnesium acetate tetrahydrate 8.02 × 10 ^-3 parts by mass (Oxygen concentration: 0.0005 to 0.001 vol%) were sufficiently introduced into the reactor. Subsequently, heating was carried out with the resulting mixture, and stirring was started when the internal temperature reached 100 占 폚. The internal temperature was set to 220 캜 for 40 minutes after the start of the temperature rise, and the temperature was maintained at the time when the internal temperature reached 220 캜. At the same time, the decompression was started, and after reaching 220 캜, 13.3 ㎪ Pressure, same hereinafter), and the pressure was maintained, and the pressure was further maintained for 30 minutes. The phenol vapor produced as a by-product together with the polymerization reaction was led to a reflux condenser at 100 ° C to return the monomer components contained in the phenol vapor to a polymerization reactor and the condensed phenol vapor was continuously introduced into a condenser at 45 ° C for recovery .

The thus obtained oligomerized contents were once pressurized to atmospheric pressure, transferred to another polymerization reactor equipped with a stirring blade and a reflux condenser controlled at 100 DEG C, and the temperature and decompression were started. And the pressure was set to 200 Pa. ISH / DEG = 60.5 / 31.5 / 8.0 &lt; / RTI &gt; as a pellet using a rotary cutter, and the mixture was stirred for 20 minutes over a period of 20 minutes at a pressure of 133 Pa or less. Mol% of a polycarbonate resin B was obtained. The polycarbonate resin B had a reduced viscosity of 0.425 L / g and a glass transition temperature of 127 deg.

A film roll laminate was obtained in the same manner as in Example 1 with respect to the polycarbonate resin B thus obtained.

[Example 3]

Example 2 In, 804.9 parts by mass of BHEPF, bisphenol A (hereinafter, sometimes abbreviated as "BPA") to 132.3 parts by mass of calcium acetate monohydrate the DPC as 532.9 parts by weight, and the catalyst 1.28 × 10 ^{- 2} parts by mass were used to obtain a final polymerization temperature of 260 占 폚. A polycarbonate resin C of BHEPF / BPA = 76.0 / 24.0 mol% was obtained in the same manner as in Example 2 except for the above. The polycarbonate resin C had a reduced viscosity of 0.344 dl / g and a glass transition temperature of 149 占 폚.

A film roll laminate was obtained in the same manner as in Example 1 with respect to the polycarbonate resin C obtained.

[Example 4]

In Example 2, BHEPF (868.4 parts by mass), 149.5 parts by mass of dimethyl terephthalate (hereinafter may be abbreviated as "DMT"), 284.7 parts by mass of DPC, and 1.35 × 10 ^-1 Mass part was used and the final polymerization temperature was set to 250 占 폚. The procedure of Example 2 was otherwise repeated to obtain a polyester carbonate resin D of BHEPF / DMT = 72.0 / 28.0 mol%. This polyester carbonate resin D had a reduced viscosity of 0.277 dl / g and a glass transition temperature of 154 占 폚.

A film roll laminate was obtained in the same manner as in Example 1 for the obtained polyester carbonate resin D.

[Example 5]

The procedure of Example 1 was repeated except that the masking film was changed to "Purutect, VLH9" (base layer: polyolefin mixture, adhesive layer: olefin-based special polymer, thickness: 30 μm) manufactured by Mitsui Chemicals, In the same manner, a film roll laminate was obtained.

[Comparative Example 1]

In Example 2, 322.0 parts by mass of 9,9-bis (4-hydroxy-3-methylphenyl) fluorene (biscresol fluorene, hereinafter abbreviated as BCF) (Spiroglycol, hereinafter abbreviated as &quot; SPG &quot;) was added in an amount of 604.3 parts by weight based on 100 parts by weight of (1,1-dimethyl- 619.7 parts by mass of DPC and 9.99 10 ^-2 parts by mass of calcium acetate monohydrate as a catalyst were used to adjust the final polymerization temperature to 260 ° C. A polycarbonate resin E of BCF / SPG = 30.0 / 70 mol% was obtained in the same manner as in Example 2 except for the above. The polycarbonate resin E had a reduced viscosity of 0.499 dl / g and a glass transition temperature of 135 캜.

The obtained polycarbonate resin E was tried to obtain a film wound laminate in the same manner as in Example 1. However, since it was brittle and fractured, cracks and scratches were produced during the production of the film wound laminate, and a film wound laminate could not be obtained.

[Comparative Example 2]

In Example 1, only the polycarbonate resin film was intended to be wound without adhering the masking film, but it was remarkably difficult to take up the film and the film laminate could not be obtained.

As described above, in the embodiment exemplifying the constitution of the present invention, a film laminate and a film wound laminate can be obtained by laminating a specific masking film on a brittle, undamaged polycarbonate resin film.

On the other hand, in Comparative Example 1, since a brittle-destroying polycarbonate resin film is used, even if a specific masking film is laminated, a film wound laminate can not be obtained. In Comparative Example 2, since a specific masking film was not laminated, when the film wound laminate was intended to be obtained, the friction between the polycarbonate resin films which were in contact with each other excessively occurred, and the film wound laminate could not be obtained.

From the results of the above Examples and Comparative Examples, it can be seen that according to the present invention, it is possible to provide a film which can be used for an optical use member, does not cause cracks on the surface or end portion of the polycarbonate resin film during winding or trimming, It has been found that a laminated film and a uniform laminated film can be provided without any unwind or roll-up wrinkles using the film laminate. In addition, it has been shown that such a film roll laminate can be provided.

While the present invention has been described with reference to the embodiment which is presently considered to be the most practical and preferred at present, it is to be understood that the invention is not limited to the embodiments disclosed in the specification, The film laminate, the film laminate, and the method of producing the laminate film which are appropriately changeable without departing from the gist or the spirit of the present invention and which involve such changes are also to be understood as being included in the technical scope of the present invention .

The present application is based on Japanese Patent Application (Japanese Patent Application No. 2011-165833) filed on July 28, 2011, the content of which is incorporated herein by reference.

Claims (14)

A brittle non-fractured polycarbonate resin film obtained by melt-extruding a polycarbonate resin containing a structural unit derived from a dihydroxy compound (a) having a moiety represented by the following formula (1) in a part of its structure, And a masking film having an adhesive layer laminated thereon,
Wherein a static friction coefficient of the polycarbonate resin film in a state in which the polycarbonate resin films are in surface contact with each other is 1.8 or more and a static friction coefficient in a state in which one surface of the polycarbonate resin film and the non- , Film laminate.
[Chemical Formula 1]

A polycarbonate resin film obtained by melt extrusion molding of a polycarbonate resin containing a structural unit derived from a dihydroxy compound (b) represented by the following formula (2), and a masking film having a base layer and an adhesive layer As the film laminate,
Wherein a static friction coefficient of the polycarbonate resin film in a state in which the polycarbonate resin films are in surface contact with each other is 1.8 or more and a static friction coefficient in a state in which one surface of the polycarbonate resin film and the non- , Film laminate.
(2)

(In the formula (2), R ₁ to R ₄ each independently represent a hydrogen atom, a substituted or unsubstituted alkyl group having 1 to 20 carbon atoms, a substituted or unsubstituted cycloalkyl group having 6 to 20 carbon atoms, Unsubstituted aryl group having 6 to 20 carbon atoms, X is a substituted or unsubstituted alkylene group having 2 to 10 carbon atoms, a substituted or unsubstituted cycloalkylene group having 6 to 20 carbon atoms, or a substituted or unsubstituted C6- And m and n are each independently an integer of 1 to 5, 3. The method according to claim 1 or 2,
Wherein the polycarbonate resin film has an absolute value of in-plane retardation of 10 nm or less. 4. The method according to any one of claims 1 to 3,
Wherein the polycarbonate resin has a glass transition temperature of 110 ° C or more and 160 ° C or less. 5. The method according to any one of claims 1 to 4,
Wherein the dihydroxy compound (a) or the dihydroxy compound (b) is 9,9-bis (4- (2-hydroxyethoxy) phenyl) fluorene. 6. The method according to any one of claims 1 to 5,
Wherein the polycarbonate resin film has a thickness of 30 占 퐉 or more and 300 占 퐉 or less, a total light transmittance of 85% or more, and a haze of 2% or less. 7. The method according to any one of claims 1 to 6,
(? ₀ ) of the surface of the polycarbonate resin film before the masking film is laminated on the polycarbonate resin film, and the masking film is laminated on the polycarbonate resin film, and the masking film And the numerical contact angle (? ₁ ) of the surface of the polycarbonate resin film after peeling off the film is? _{0 -} ? ₁ | is 20 or less. 8. The method according to any one of claims 1 to 7,
Wherein the peel strength of said masking film to said polycarbonate resin film conforming to JIS-Z0237 (2009) is not less than 5 mN / 10 mm and not more than 200 mN / 10 mm. 9. The method according to any one of claims 1 to 8,
Wherein the base layer of the masking film is made of a polyolefin resin. 10. The method according to any one of claims 1 to 9,
Wherein the adhesive layer of the masking film is composed of a modified polyolefin resin. A film roll laminate obtained by winding the film laminate according to any one of claims 1 to 10 onto a cylindrical core to form a roll. 12. The method of claim 11,
Wherein the side edge portions of the film wound laminated body have a winding displacement width of 4 mm or less. A method for producing a film roll laminate according to claim 11 or 12,
Extruding the polycarbonate resin to obtain a polycarbonate resin film by cooling while using a metal mirror-surface roll having a maximum height (Rz) of the surface of 0.3 m or less,
A step of producing a film laminate by laminating the produced polycarbonate resin film and a masking film,
And winding the formed film laminate into a cylindrical shape in a rolled form. 14. The method of claim 13,
Wherein the winding tension per film width of 1 m is set to 80 N / m or more and 200 N / m or less in the step of winding the film laminate into a cylindrical winding core in a roll form.