JP2016172454A - Method for producing polyester film - Google Patents

Abstract

PROBLEM TO BE SOLVED: To provide a method for producing a polyester film which is industrially practicable, while having an excellent balance between mechanical characteristics in MD and TD directions, excellent impact resistance and the like.SOLUTION: A method for producing a biaxially stretched polyester film is characterized by stretching an unstretched film obtained by multilayering and casting raw materials of the same composition.SELECTED DRAWING: None

Description

  The present invention relates to a method for producing a polyester film. More specifically, the present invention relates to a method for producing a polyester film excellent in the balance of impact resistance, flexibility and mechanical strength, which is suitable for applications in which nylon films and other flexible films have been conventionally used.

  Polybutylene terephthalate (PBT) has been used as an engineering plastic from the past because of its excellent mechanical properties and impact resistance. In particular, it is used as a useful material because of its high crystallization speed and good productivity. . However, since PBT has a high crystallization speed, it has been difficult to perform biaxial stretching. This is because crystallization occurs due to orientation in the stretching process, and stretching becomes difficult. On the other hand, in order to take advantage of the inherent properties of PBT, studies aimed at improving the mechanical properties and impact resistance as a film by increasing the plane orientation by biaxial stretching have been made over the past 40 years. The PBT films that are still on the market are unstretched cast sheets and films obtained by the inflation method, and these films have the characteristics of the original PBT because the orientation of the PBT is insufficient. It's hard to say. In particular, the PBT film of the inflation method has a problem that the draw ratio is difficult to be uniform due to the manufacturing method, the thickness accuracy is poor, and the puncture strength is low because the plane orientation coefficient does not increase. . Therefore, PBT films obtained by a biaxial stretching method using a tenter have been studied. In the following, some studies on past PBT films will be considered.

  Conventionally, after stretching in the TD direction at a stretching ratio of 3.5 times or less, the film is stretched in the MD direction at a deformation rate of 100000% / min or more to produce a biaxially stretched PBT film, thereby uniformly stretching the thickness. A technique of manufacturing a film without unevenness is known (see, for example, Patent Document 1). However, as can be seen from the results of the examples, the conventional technique increases the deformation speed only in the MD direction, so that the elongation is low, and there is a problem that the film cannot be balanced in the MD direction and the TD direction. It was.

  In addition, based on the experimental results, the stretching temperature is calculated from the crystallinity at the time of unstretching, and after the temperature is stretched in the MD (or TD) direction at a low magnification, orthogonal to the first stage stretching direction at a high temperature. A technique is known in which a film excellent in impact resistance in which unevenness in thickness and breakage during film formation are suppressed is produced by stretching in the direction in which the film is stretched (see, for example, Patent Document 2). However, in this conventional technique, the second stage stretching is performed at 120 ° C. and the PBT Tg (45 ° C.) at a very high temperature, and the state of advanced orientation crystallization is reoriented in the second stage direction. Because of such stretching, there was a problem that the balance of the mechanical properties in the MD direction and the TD direction was inferior.

  A technique for producing a film having excellent gas barrier properties and pinhole resistance by alternately laminating PBT and resins other than PBT such as polyethylene terephthalate (PET) and polyethylene naphthalate (PEN) is known. (For example, refer to Patent Document 3). However, since such a conventional technique has laminated a layer made of a resin such as PET or PEN in addition to PBT, the stretching temperature is stretched at a stretching temperature of PET or PEN having a Tg higher than that of PBT. It is stretched at. For this reason, the characteristics of the original PBT film are not drawn out, and since there are two types of resin compositions in the film, it is difficult to add trimming waste during film formation to the raw material and reuse it again. However, there was a problem that it was disadvantageous in terms of economy.

JP 51-146572 A Japanese Patent Laid-Open No. 51-40904 Japanese Patent No. 4273855

  The present invention has been made against the background of such prior art problems. That is, the purpose of the present invention is to suppress the breakage that occurs when stretching PBT with a high crystallization speed, in particular due to the difference in the shearing speed when discharging molten resin from the die in the width direction and the cooling speed during casting. By suppressing the non-uniformity of the crystallinity and reducing the specific gravity difference in the width direction in the unstretched state of the film, the breakage is greatly suppressed, and it can be industrially implemented, in the MD / TD direction. An object of the present invention is to provide a method for producing a polyester film which is excellent in improving the balance of mechanical properties and impact resistance.

  As a result of intensive studies to achieve the above object, the present inventors have completed the present invention.

  That is, this invention is a manufacturing method of the biaxially stretched polyester film characterized by extending | stretching the unstretched film obtained by multilayering and casting the raw material of the same composition.

  In this case, it is preferable that the multilayering is performed using a multilayering apparatus.

  In this case, it is preferable that the multi-layering apparatus is introduced into a melt line from an extruder to a die.

  Furthermore, in this case, the raw material having the same composition is preferably a polyester resin containing 60% by mass or more of polybutylene terephthalate.

  Furthermore, in this case, it is preferable that the cast is casting on a chill roll and the upper limit of the chill roll temperature is 80 ° C.

  Furthermore, in this case, it is preferable that stretching of the unstretched film is sequential biaxial stretching.

  In the method for producing a polyester film of the present invention, in order to suppress breakage that occurs when a PBT having a high crystallization rate is stretched, the shear rate in discharging the molten resin from the die in the width direction and the cooling rate during casting are particularly important. Suppressing non-uniformity of crystallinity due to the difference and reducing the specific gravity difference in the width direction in the unstretched state of the film, greatly suppressing breakage during film stretching, and can be implemented industrially, The balance of mechanical properties in MD and TD directions, impact resistance, etc. can be improved.

  Hereinafter, the present invention will be described in detail.

  The polyester resin used in the present invention is mainly composed of PBT, and the content of PBT is preferably 60% by mass or more, more preferably 70% by mass or more, and particularly preferably 75% by mass or more. Most preferably, it is 80 mass% or more. If it is less than 60% by mass, the impact strength and pinhole resistance of the film are lowered, and the film properties are not sufficient.

  PBT used as a main constituent component is preferably 90 mol% or more, more preferably 95 mol% or more, still more preferably 98 mol% or more, most preferably 100 mol% or more of terephthalic acid as a dicarboxylic acid component. Mol%. As the glycol component, 1,4-butanediol is preferably 90 mol% or more, more preferably 95 mol% or more, still more preferably 97 mol% or more, and most preferably 1,4-butanediol during polymerization. It is not included except by-products generated by the ether bond of butanediol.

Examples of the dicarboxylic acid component that may be copolymerized include isophthalic acid, orthophthalic acid, naphthalenedicarboxylic acid, biphenyldicarboxylic acid, cyclohexanedicarboxylic acid, adipic acid, azelaic acid, and sebacic acid. Examples of glycol components that may be copolymerized include ethylene glycol, 1,3-propylene glycol, 1,2-propylene glycol, neopentyl glycol, 1,5-pentanediol, 1,6-hexanediol, diethylene glycol, and cyclohexanediol. , Polyethylene glycol, polytetramethylene glycol, polycarbonate diol and the like.
For these, it is necessary to adjust the copolymerization amount of each monomer within a range in which the impact strength and piercing strength of the film can be satisfied in balance with the amounts of other polyester resins and additives described later.

Other constituent components are not particularly limited, but other polyester resins such as polyethylene terephthalate (PET), polyethylene naphthalate (PEN), polybutylene naphthalate (PBN), polypropylene terephthalate (PPT), etc. In order to improve pinhole resistance at the time of bending, a polyester-based and polyamide-based elastomer copolymerized with at least one of a flexible polyether component, a polycarbonate component, and a polyester component can be added to the polyester resin.
The lower limit of the amount of these additives is 0% by mass, and the upper limit is preferably 20% by mass. If it exceeds 20%, the above effect may be saturated and the transparency of the film may be lowered.

  The lower limit of the resin melting temperature is preferably 200 ° C., and if it is lower than 200 ° C., the discharge of the molten resin may become unstable. The upper limit of the resin melting temperature is preferably 320 ° C., and if it exceeds 320 ° C., the resin may be deteriorated.

  The polyester resin may contain conventionally known additives such as a lubricant, a stabilizer, a colorant, an antioxidant, an antistatic agent, and an ultraviolet absorber as necessary.

  As the lubricant type, organic lubricants and inorganic lubricants such as silica, calcium carbonate and alumina are preferable, silica and calcium carbonate are more preferable, and calcium carbonate is particularly preferable. By these, transparency and slipperiness of the film can be expressed.

  The lower limit of the lubricant concentration is preferably 100 ppm, and if it is less than 100 ppm, the slipperiness of the film may be lowered. The upper limit of the lubricant concentration is preferably 20000 ppm, and if it exceeds 20000 ppm, the transparency of the film may be lowered.

  As a point of the production method of the present invention, it is necessary to reduce the difference in crystallinity in the width direction of the unstretched film during casting.

  The present inventors have found that the difference in crystallinity in the width direction of an unstretched film can be reduced by using a novel method described later. That is, by casting multiple raw materials having the same composition during casting, the difference in crystallinity in the width direction of the unstretched film can be reduced, and the stretching stress distribution during TD stretching can be made uniform. I found out that I can do it. Conventionally, the crystallinity of the edge of the unstretched film is increased during casting, while the crystallinity of the center of the unstretched film is decreased, so that the stretching stress during stretching in the TD direction is the width of the unstretched film. Since the film is not uniform in the direction, the film is easily broken, and TD stretching at a very high temperature is required. On the other hand, this cause is speculated, but even when the same resin is laminated, the interface of the layer exists, and the crystallization is accelerated by the interface, while the large crystal beyond the layer is suppressed. Therefore, it is considered that the crystallinity in the width direction of the unstretched film becomes uniform. As a specific method, a general multi-layer device (multi-layer feed block, static mixer, multi-layer multi-manifold, etc.) can be used. For example, heat sent from different flow paths using two or more extruders. A method of laminating a plastic resin in multiple layers using a field block, a static mixer, a multi-manifold die, or the like can be used. In addition, when multi-layering raw materials having the same composition, the object of the present invention can be achieved by introducing the above multi-layering apparatus into the melt line from the extruder to the die using only one extruder. Is possible.

In addition, when using two or more extruders, the raw materials having the same composition are the maximum mass% and the minimum in the mass% of the individual raw materials blended in the thermoplastic resin fed from each extruder. The difference from the mass% is allowed to be 10 mass% or less, further 5 mass% or less, and particularly 2 mass% or less. In the case where a copolymer is used for the polyester, the difference between the maximum mol% and the minimum mol% is 5 mol% or less in the mol% of the monomer to be copolymerized in the thermoplastic resin fed from each extruder, Is allowed to be 3 mol% or less, particularly 2 mol% or less. The molecular weights of the individual raw materials may be different, but when the weight average molecular weight in terms of styrene is determined by GPC, the value obtained by dividing the difference in molecular weight by the molecular weight of the product having a large molecular weight is 30% or less. It is preferably 20% or less, particularly preferably 10% or less. Within this range, the same individual raw materials are allowed even if the molecular weights of the individual raw materials are different.
In addition, the method of introducing the above-mentioned multilayering apparatus into the melt line from the extruder to the die using only one extruder is a preferable method from the viewpoint of simplicity of the apparatus and management of each raw material.

  The lower limit of the die temperature is preferably 200 ° C., and if it is lower than 200 ° C., the discharge of the molten resin is not stable, and the film thickness may be uneven. The upper limit of the die temperature is preferably 350 ° C., and if it exceeds 350 ° C., the thickness of the film becomes non-uniform, the resin deteriorates, and the appearance may be poor due to die lip contamination.

The lower limit of the chill roll temperature is preferably −10 ° C., and if it is less than −10 ° C., the effect of homogenizing the crystallinity in the width direction of the unstretched film may be saturated. The upper limit of the chill roll temperature is preferably 80 ° C., and if it exceeds 80 ° C., the crystallinity of the unstretched film becomes too high and stretching may be difficult. In order to reduce the difference in crystallinity in the width direction of the unstretched film, it is effective to reduce the crystallinity. Therefore, when not using a method such as multi-layering described later, a preferable chill roll temperature is It is 10 degrees C or less, Furthermore, it is 5 degrees C or less. In this case, it is preferable to reduce the humidity of the environment near the chill roll in order to prevent condensation. On the other hand, the difference in crystallinity in the width direction of the unstretched film can be reduced by using a method such as multilayering described later, and in this case, casting is possible even at a temperature of 15 to 40 ° C.
The temperature difference in the width direction of the chill roll is preferably small, and the preferred temperature difference is 5 ° C. or less, more preferably 3 ° C. or less. When the temperature difference exceeds 5 ° C., the difference in crystallinity in the width direction of the unstretched film may not be reduced during casting.

  In casting, the surface of the chill roll rises due to the high temperature resin coming into contact with the surface. Normally, the chill roll is cooled by flowing cooling water through the pipe inside, but securing a sufficient amount of cooling water, devising the arrangement of the pipe, performing maintenance so that sludge does not adhere to the pipe, etc. It is necessary to reduce the temperature difference in the width direction. In particular, care should be taken when cooling at low temperatures without using a method such as multilayering.

  In the case of casting in a multilayer structure, there are at least 3 layers, preferably 5 layers or more, more preferably 8 layers or more, and most preferably 100 layers or more. When the number of layers is small, the specific gravity difference in the width direction of the unstretched film becomes large, and the effect of improving stretchability is small. When it is 100 layers or more, the effect of reducing the specific gravity difference in the width direction of the unstretched film is stabilized, the thickness uniformity of each layer is also stabilized, and the appearance is improved.

  Next, the stretching method will be described. The stretching method can be simultaneous biaxial stretching or sequential biaxial stretching, but in order to increase the piercing strength of the film, it is necessary to increase the plane orientation coefficient of the film. Is preferred.

  The lower limit of the MD stretching temperature is preferably 40 ° C, more preferably 45 ° C. If it is lower than 40 ° C., breakage may easily occur. The upper limit of the MD stretching temperature is preferably 100 ° C, more preferably 95 ° C. If the temperature exceeds 100 ° C., it is difficult to align, and the mechanical properties of the film may be deteriorated.

  The lower limit of the MD draw ratio is preferably 2.5 times, and if it is less than 2.5, the film is difficult to be oriented and the mechanical properties and thickness unevenness of the film may deteriorate. The upper limit of the MD draw ratio is preferably 5 times, and if it exceeds 5 times, the effect of improving the mechanical strength and thickness unevenness of the film may be saturated.

  The lower limit of the TD stretching temperature is preferably 40 ° C, and if it is less than 40 ° C, the film may be easily broken. The upper limit of the TD stretching temperature is preferably 100 ° C., and when it exceeds 100 ° C., it is difficult to align, and the mechanical properties of the film may be deteriorated.

  The lower limit of the TD stretch ratio is preferably 2.5 times, and if it is less than 2.5 times, the orientation is difficult to align, and the mechanical properties and thickness unevenness may deteriorate. The upper limit of the TD stretch ratio is preferably 5 times, and if it exceeds 5 times, the effect of improving the mechanical strength and thickness unevenness of the film may be saturated.

  The lower limit of the TD heat setting temperature is preferably 150 ° C., and if it is less than 150 ° C., the thermal shrinkage rate of the film increases, and a shift or shrinkage during processing may occur. The upper limit of the TD heat setting temperature is preferably 250 ° C., and if it exceeds 250 ° C., the film melts, and even if it does not melt, it may become brittle.

  The lower limit of the TD relaxation rate is preferably 0.5%, and if it is less than 0.5%, the film may be easily broken during heat setting. The upper limit of the TD relaxation rate is preferably 10%, and if it exceeds 10%, sagging or the like may occur in the film and thickness unevenness may occur.

  In the film after biaxial stretching obtained by the present invention, the lower limit of the film thickness is preferably 3 μm, more preferably 5 μm, and further preferably 8 μm. If it is less than 3 μm, the strength as a film may be insufficient. The upper limit of the film thickness is preferably 100 μm, more preferably 75 μm, and still more preferably 50 μm. If it exceeds 100 μm, the film may become too thick and processing for the purpose of the present invention may be difficult.

  Regarding the thickness unevenness at the full width of the roll, the difference between the maximum thickness and the minimum thickness at the full width is preferably in the range of 0 to 25%, more preferably in the range of 0 to 20%. . If it exceeds 25%, the roll appearance is deteriorated and distortion in secondary processing occurs, which is not preferable. In order to reduce the difference between the maximum thickness and the minimum thickness of the entire width, it is necessary that the stretching ratio in the width direction is uniform. For that purpose, it is necessary to make the crystallinity when unstretched uniform. is there.

In the present invention, the lower limit of the specific gravity at the center of the unstretched film is preferably 1.25 g / cm ³ , and if it is less than 1.25 g / cm ³ , the effect of improving the stretchability of the unstretched film may be saturated. is there. The upper limit of the specific gravity at the center is preferably 1.3 g / cm ³ , and if 1.3 g / cm ³ is exceeded, the crystallinity becomes too high and stretching may be difficult.

In the present invention, the upper limit of the difference in the specific gravity in the width direction of the unstretched film is preferably 0.03 g / cm ³ , and if it exceeds 0.03 g / cm ³ , the stretching stress becomes non-uniform in the width direction and the film breaks. Occurring and stretching unevenness in the width direction of the film occurs, which may cause unevenness in thickness and physical properties.

  The lower limit of the MD elastic modulus of the film obtained by the present invention is preferably 1 GPa, and if it is less than 1 GPa, the film tends to be stretched, and pitch deviation may occur during processing such as printing and lamination. The upper limit of the MD elastic modulus is preferably 2 GPa, and if it exceeds 2 GPa, it may be disadvantageous in terms of workability such as drawing after the film is bonded to various sealants.

  The lower limit of the TD elastic modulus of the film obtained by the present invention is preferably 1 GPa, and if it is less than 1 GPa, the film tends to be stretched, and problems may occur during processing. The upper limit of the TD elastic modulus is preferably 2 GPa, and if it exceeds 2 GPa, it may be disadvantageous in terms of workability such as drawing after the film is bonded to various sealants. Note that the TD elastic modulus can be within a range depending on the heat setting temperature.

  The lower limit of the TD breaking strength of the film obtained by the present invention is preferably 100 MPa, and if it is less than 100 MPa, breakage or the like may occur during processing of the film. The upper limit of the TD breaking strength is preferably 500 MPa, and if it exceeds 500 MPa, the effect of improving the breaking strength of the film may be saturated.

  The lower limit of the MD breaking elongation of the film obtained by the present invention is preferably 80%, more preferably 90%. If it is less than 80%, it may be disadvantageous in terms of workability such as drawing after the film is bonded to various sealants. The upper limit of the MD breaking elongation is not particularly limited, but is preferably 200%. MD breaking elongation can be made into the range with MD magnification and heat setting temperature.

  The lower limit of the TD breaking elongation of the film obtained by the present invention is preferably 80%, more preferably 90%. If it is less than 80%, it may be disadvantageous in terms of workability such as drawing after the film is bonded to various sealants. The upper limit of the TD breaking elongation is not particularly limited, but is preferably 500%. The TD breaking elongation can be set within the range by the TD magnification and the heat setting temperature.

  The lower limit of the plane orientation coefficient of the film obtained by the present invention is preferably 0.12, and if it is less than 0.12, the piercing strength, impact strength, etc. may be lowered. The upper limit of the plane orientation coefficient is preferably 0.14, and if it exceeds 0.14, the productivity of the film may be lowered and the flexibility may be lowered. The plane orientation coefficient can be set within the range by the MD magnification and the heat setting temperature. Further, as the stretching method, sequential biaxial stretching, particularly sequential biaxial stretching in which stretching in the MD direction and then stretching in the TD direction is preferable to simultaneous biaxial stretching.

  Further, the variation of the plane orientation coefficient in the width direction of the stretched film obtained in the present invention is such that the difference between the maximum value and the minimum value of the plane orientation coefficient measured by dividing the entire width of the film into 10 equal parts is 0.02. Hereinafter, it is more preferably 0.015 or less, and most preferably 0.01 or less. If it exceeds 0.02, in addition to variations in mechanical properties, the thickness unevenness of the film is large, which is not preferable. Further, in order to reduce the fluctuation of the plane orientation coefficient, it is realized by reducing the specific gravity difference (difference in crystallinity) in the width direction of the unstretched film.

  Moreover, it is preferable that the orientation axis | shaft angle of the film after extending | stretching obtained in this invention exists in the range of 0-40 degree | times. In the present invention, the MD direction and the TD direction are balanced, but if it exceeds 40 degrees, the film is distorted after heating, which is not preferable. As a specific method for this purpose, a method for reducing shrinkage in the MD direction when performing heat fixation after TD stretching, which is the same as a method for reducing general bowing, can be adopted. By reducing the difference in crystallinity between the center and the end of the unstretched film, the bowing at the end of the stretched film can be advantageously reduced.

  The lower limit of the piercing strength of the film obtained by the present invention is preferably 0.5 N / μm, more preferably 0.9 N / μm. If it is less than 0.5 N / μm, the strength when processing the film or when the film is used as a bag may be insufficient. The upper limit of the piercing strength is preferably 1.5 N / μm, and if it exceeds 1.5 N / μm, the improvement effect is saturated. The piercing strength can be within the range by the MD magnification and the heat setting temperature.

  The lower limit of the impact strength (impact resistance) of the film obtained by the present invention is preferably 0.05 J / μm, more preferably 0.06 J / μm. When it is less than 0.05 J / μm, the strength may be insufficient when used as a bag. The upper limit of impact strength (impact resistance) is preferably 0.2 J / μm, and if it exceeds 0.2 J / μm, the above-described improvement effect is saturated.

  The lower limit of the moisture absorption rate of the film obtained by the present invention is preferably 0.1%, and if it is less than 0.1%, the improvement effect will be saturated. The upper limit of the moisture absorption rate is preferably 1%, and if it exceeds 1%, a change in moisture absorption dimension or the like may easily occur.

  The lower limit of the MD heat shrinkage rate of the film obtained by the present invention is preferably 0.1%, and if it is less than 0.1%, the improvement effect is saturated and it may become mechanically brittle. The upper limit of the MD thermal contraction rate is preferably 4%, and if it exceeds 4%, pitch deviation may occur due to a dimensional change during processing such as printing.

  The lower limit of the TD heat shrinkage rate of the film obtained by the present invention is preferably 0.1%, and if it is less than 0.1%, the improvement effect is saturated and it may become mechanically brittle. The upper limit of the TD heat shrinkage is preferably 3%, and if it exceeds 3%, shrinkage in the width direction of the film may occur due to dimensional changes during processing such as printing.

  The lower limit of the haze of the film obtained by the present invention is preferably 0. The upper limit of haze is preferably 50%, more preferably 30%, and still more preferably 20%. This does not apply to applications where the contents cannot be seen. If the haze exceeds 30%, the contents may be difficult to see when used as a bag.

  The lower limit of the number of pinholes generated in a gelbo flex test of a laminate obtained by laminating a film obtained by the present invention and a sealant by a dry laminating method is preferably zero. The upper limit of the number of pinholes is preferably 10, and more preferably 5. When it exceeds 10, it may be easy to open a hole in the film when used as a bag. A method for measuring the number of pinholes will be described later.

  EXAMPLES Next, although an Example demonstrates this invention further in detail, this invention is not limited to the following examples. The film was evaluated by the following measurement method.

[Specific gravity of unstretched film]
The specific gravity at 23 ° C. of each sample was measured using a Shimadzu specific gravity measuring device SGM-300P according to JIS Z88078 (weighing in liquid method).
The difference in the specific gravity in the width direction was determined by taking a 10-point sample in the width direction from the obtained unstretched film, measuring the specific gravity by the above method, and subtracting the minimum value from the maximum value of the obtained results. It was obtained by dividing.

[Mechanical properties (breaking strength, breaking elongation)]
According to JIS K7113. A sample having a width of 10 mm and a length of 100 mm was cut out from the film using a razor. The cut sample was allowed to stand for 12 hours in an atmosphere of 23 ° C. and 35% RH, and then measured under conditions of a distance between chucks of 40 mm and a pulling speed of 200 mm / min in an atmosphere of 23 ° C. and 35% RH. The average value of the measurement results was used. As a measuring device, an autograph AG5000A manufactured by Shimadzu Corporation was used.

[Plane orientation]
A 10-point sample was taken from the roll sample in the width direction. According to JISK7142-1996 5.1 (Method A), the sample was subjected to refractive index (nx) in the film longitudinal direction, refractive index (ny) in the width direction, refractive index (in the thickness direction) with an Abbe refractometer using sodium D line as a light source ( nz) was measured, and the plane orientation coefficient (ΔP) was calculated by the following formula. In addition, the average value of the obtained plane orientation coefficient was made into the plane orientation coefficient.
ΔP = (nx + ny) / 2−nz
The difference in the plane orientation coefficient in the width direction was the difference between the maximum value and the minimum value of the above 10 samples.

[Orientation axis angle]
Using a MOA-6004 type molecular orientation meter manufactured by Oji Scientific Instruments, the orientation angle (θ) of the molecular chain orientation principal axis at the end of the film was determined.

[Impact strength]
Using an impact tester manufactured by Toyo Seiki Seisakusho Co., Ltd., the strength against impact punching of the film in an atmosphere at 23 ° C. was measured. An impact spherical surface having a diameter of 1/2 inch was used. The unit is J / μm.

[Puncture strength]
It was measured in accordance with “2. Test methods for strength, etc.” in “Standards for Foods, Additives, etc. 3: Equipment and Containers and Packaging” in the Food Sanitation Law (Ministry of Health and Welfare Notification No. 20 of 1982). A needle having a tip diameter of 0.7 mm was pierced into the film at a piercing speed of 50 mm / min, and the strength when the needle penetrated the film was measured to obtain the piercing strength. The measurement is performed at room temperature (23 ° C.), and the unit is N.

[Pinhole resistance]
A film according to the present invention and a sealant (unstretched propylene film manufactured by Toyobo Co., Ltd., P1146, thickness 70 μm), polyester polyol (manufactured by Toyo Morton Co., Ltd., TM-509), 33.6 parts by mass, polyisocyanate (manufactured by Toyo Morton Co., Ltd., (CAT-10L) 4.0 parts by mass and 62.4 parts by mass of ethyl acetate were mixed and dry-laminated using a urethane adhesive to prepare a laminate.
The laminate was cut to a size of 20.3 cm (8 inches) × 27.9 cm (11 inches), and the cut rectangular test film was subjected to a temperature of 23 ° C. and a relative humidity of 50% for 24 hours. It was left and conditioned. Thereafter, the rectangular test film is wound to form a cylindrical shape having a length of 20.32 cm (8 inches). Then, one end of the cylindrical film is fixed to the outer periphery of a disk-shaped fixing head of a gelbo flex tester (manufactured by Rigaku Kogyo Co., Ltd., NO.901 type) (conforming to the standard of MIL-B-131C). The other end of the tester was fixed to the outer periphery of a disk-shaped movable head of a tester facing the fixed head at a distance of 17.8 cm (7 inches). Then, the movable head is rotated by 440 ° while approaching 7.6 cm (3 inches) along the axis of both heads facing in parallel to the direction of the fixed head, and then 6.4 cm (2. 5 cycles), a one-cycle bending test in which the movements were performed in the opposite direction to return the movable head to the initial position was repeated 1000 cycles continuously at a rate of 40 cycles per minute. . Implementation was at 5 ° C. Thereafter, the number of pinholes generated in a portion within 17.8 cm (7 inches) × 27.9 cm (11 inches) excluding the portion fixed to the outer periphery of the fixed head and the movable head of the tested film was measured (ie, The number of pinholes per 497 cm 2 (77 square inches) was measured).

[Intrinsic viscosity of polyester]
0.1 g of polyester was dissolved in 25 mL of a mixed solvent of phenol / tetrachloroethane (volume ratio: 3/2), and the intrinsic viscosity of the polyester was measured at 30 ° C. using an Ostwald viscometer.

[Melting point of polyester]
Using a differential scanning calorimeter (DSC) manufactured by SII, the sample amount was 10 mg, and the heating rate was 20 ° C./min. The melting endothermic peak temperature detected here was defined as the melting point of the polyester.

[Thickness]
The thickness of the film was measured by a method according to JIS-Z-1702.

[Heat shrinkage]
Except that the test temperature was 150 ° C. and the heating time was 10 minutes, the thermal shrinkage rate was measured by the dimensional change test method described in JIS-C-2318.

[Haze]
Using a method according to JIS-K-7105, the sample was measured for haze at three different locations using a haze meter (NDH2000, manufactured by Nippon Denshoku Industries Co., Ltd.), and the average value was taken as haze.

[Thickness uniformity (Tv (%))]
A film piece was cut out in the longitudinal direction from the center of the obtained film roll, the thickness of the film was measured using a dial gauge at a pitch of 5 cm, and the thickness uniformity was calculated from the result.

[Peel strength]
The film according to the present invention and a sealant (Toyobo unstretched propylene film, P1146, thickness 70 μm), polyester polyol (Toyo Morton, TM-509) 33.6 parts by mass, polyisocyanate (Toyo Morton, CAT) -10L) Dry lamination was performed using a urethane-based adhesive obtained by mixing 4.0 parts by mass and 62.4 parts by mass of ethyl acetate to prepare a laminate.
The laminate was cut into a width of 15 mm and a length of 200 mm to obtain a test piece, and “Tensilon UMT-II-500 type” manufactured by Toyo Baldwin Co., Ltd. was used at a temperature of 23 ° C. and a relative humidity of 65%. The peel strength at the joint surface between the untreated surface of the polyester film and the polyolefin resin layer was measured. The tensile speed was 10 cm / min and the peeling angle was 180 degrees.

[Hygroscopic rate]
The film according to the present invention was cut into a square with a side of 50 mm and before and after being immersed in water maintained at a temperature of 23 ° C. ± 2 ° C. according to JIS-K-7209-7.2.1 (Method A). The change in weight of the film was measured. The moisture absorption rate was calculated by the following formula (1).
Moisture absorption rate (%) = 100 × ([M2] − [M1]) / [M1] (1)
In the above formula (1), [M1] is the film weight before water immersion, and [M2] is the film weight after water immersion.

[Reference Example 1]
A master batch containing PBT resin (Mitsubishi Engineering Plastics Novaduran 5020, melting point 220 ° C.) and calcium carbonate as a lubricant was added using a twin screw vent type extruder, and the mixture was formulated to a lubricant concentration of 2000 ppm. After melting at 0 ° C., it was cast from a T-die at 270 ° C., and adhered to a 0 ° C. cooling roll by an electrostatic adhesion method to obtain an unstretched film. When the surface temperature of the cooling roll was measured at 10 cm intervals in the width direction (thermocouple), the variation was 3 ° C. or less. Next, the film was stretched 3.2 times in the machine direction at 60 ° C., then stretched 3 times in the transverse direction at 80 ° C. through a tenter, and subjected to tension heat treatment at 200 ° C. for 3 seconds and relaxation treatment for 1 second. Thereafter, both ends were cut and removed to obtain a PBT film having a thickness of 12 μm. Table 1 shows the film forming conditions, physical properties, and evaluation results of the obtained film. The orientation axis angle at the film edge was 35 degrees, and the distortion of the sample after measuring the heat shrinkage rate was slight.

[Example 2]
Add a masterbatch containing PBT resin (Mitsubishi Engineering Plastics Novaduran 5020) and calcium carbonate as a lubricant using a twin screw vent type extruder, and melt at 270 ° C. to blend the lubricant concentration to 2000 ppm. After that, the melt line was introduced into a 12-element static mixer (STMX). Thereby, the PBT melt was divided and laminated to obtain a multilayer melt made of the same raw material. Thereafter, the film was introduced into a T-die at 270 ° C., cast, and adhered to a cooling roll at 15 ° C. by an electrostatic adhesion method to obtain an unstretched film. When the surface temperature of the cooling roll was measured at 10 cm intervals in the width direction (thermocouple), the variation was 3 ° C. or less. Next, the film was stretched 3.8 times in the machine direction at 60 ° C., then passed through a tenter and stretched 3 times in the transverse direction at 65 ° C., and subjected to tension heat treatment at 200 ° C. for 3 seconds and relaxation treatment for 1 second. Thereafter, both ends were cut and removed to obtain a PBT film having a thickness of 12 μm. Table 1 shows the film forming conditions, physical properties, and evaluation results of the obtained film. The orientation axis angle at the film edge was 25 degrees, and the distortion of the sample after measuring the heat shrinkage rate was slight.

[Examples 3 to 4]
Films were obtained under the conditions described in Table 1. Table 1 shows the film forming conditions, physical properties, and evaluation results of the obtained film. Ecoflex (registered trademark) was a polybutylene adipate butylene terephthalate copolymer (PBAT) manufactured by BASF.

[Comparative Example 1]
Film formation was examined by the method described in Example 1 except that the cooling roll temperature at the time of casting was 15 ° C. Table 2 shows the film forming conditions. The unstretched film was broken during MD stretching, and a film could not be obtained.

[Comparative Example 2]
Films were obtained under the conditions described in Table 2. Table 2 shows the film forming conditions, physical properties, and evaluation results of the obtained film.

[Comparative Example 3]
An unstretched film obtained under the conditions described in Table 2 was used as a sample. A film was formed by adjusting the winding speed so that the thickness was 20 μm. The orientation axis angle at the film edge was 5 degrees or less, and no distortion of the sample after the measurement of the heat shrinkage rate was observed.

[Comparative Example 4]
Toyobo Ester (registered trademark) film E5100 (thickness: 12 μm) manufactured by Toyobo Co., Ltd. was used.

[Reference Example 1]
As a typical PBT film, a commercially available PBT film manufactured by Kansai Chemical Industry Co., Ltd. was used. The orientation axis angle at the film edge was 5 degrees or less, and no distortion of the sample after the measurement of the heat shrinkage rate was observed.

  The polyester film obtained by the method for producing a polyester film according to the present invention has a shear rate and cast in the discharge of molten resin from a die particularly in the width direction in order to suppress breakage that occurs when stretching a PBT having a high crystallization rate. By suppressing the non-uniformity of the crystallinity due to the difference in cooling rate at the time, and reducing the specific gravity difference in the width direction in the unstretched state, the breakage during stretching is greatly suppressed, which can be implemented industrially. Yes, the balance of mechanical properties in the MD and TD directions, impact resistance, etc. can be improved.

Claims (6)

  A method for producing a biaxially stretched polyester film, comprising stretching an unstretched film obtained by casting a raw material having the same composition in multiple layers.   The method for producing a biaxially stretched polyester film according to claim 1, wherein the multilayering is performed using a multilayering apparatus.   The manufacturing method of the biaxially-stretched polyester film of Claim 2 with which the said multilayering apparatus is introduce | transduced into the melt line from an extruder to die | dye.   The method for producing a biaxially stretched polyester film according to any one of claims 1 to 3, wherein the raw material having the same composition is a polyester resin containing 60% by mass or more of polybutylene terephthalate.   The manufacturing method of the biaxially stretched polyester film in any one of Claims 1-4 whose said cast is casting to a chill roll, and the upper limit of chill roll temperature is 80 degreeC.   The method for producing a biaxially stretched polyester film according to any one of claims 1 to 5, wherein stretching of the unstretched film is sequential biaxial stretching.