WO2009110337A1 - 熱賦形光学フィルム用ポリエステル樹脂およびそれを用いた二軸配向ポリエステルフィルム - Google Patents

熱賦形光学フィルム用ポリエステル樹脂およびそれを用いた二軸配向ポリエステルフィルム Download PDF

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WO2009110337A1
WO2009110337A1 PCT/JP2009/053141 JP2009053141W WO2009110337A1 WO 2009110337 A1 WO2009110337 A1 WO 2009110337A1 JP 2009053141 W JP2009053141 W JP 2009053141W WO 2009110337 A1 WO2009110337 A1 WO 2009110337A1
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Prior art keywords
polyester resin
heat
optical film
polyester
resin
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PCT/JP2009/053141
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English (en)
French (fr)
Japanese (ja)
Inventor
浩一 旦
純 坂本
宏光 高橋
弘造 高橋
大輔 尾形
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東レ株式会社
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Priority to CN200980108362.XA priority Critical patent/CN101959941B/zh
Priority to JP2009514573A priority patent/JPWO2009110337A1/ja
Publication of WO2009110337A1 publication Critical patent/WO2009110337A1/ja

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    • G—PHYSICS
    • G02—OPTICS
    • G02B—OPTICAL ELEMENTS, SYSTEMS OR APPARATUS
    • G02B1/00—Optical elements characterised by the material of which they are made; Optical coatings for optical elements
    • G02B1/04—Optical elements characterised by the material of which they are made; Optical coatings for optical elements made of organic materials, e.g. plastics
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
    • B29C—SHAPING OR JOINING OF PLASTICS; SHAPING OF MATERIAL IN A PLASTIC STATE, NOT OTHERWISE PROVIDED FOR; AFTER-TREATMENT OF THE SHAPED PRODUCTS, e.g. REPAIRING
    • B29C59/00—Surface shaping of articles, e.g. embossing; Apparatus therefor
    • B29C59/02—Surface shaping of articles, e.g. embossing; Apparatus therefor by mechanical means, e.g. pressing
    • B29C59/022—Surface shaping of articles, e.g. embossing; Apparatus therefor by mechanical means, e.g. pressing characterised by the disposition or the configuration, e.g. dimensions, of the embossments or the shaping tools therefor
    • B29C2059/023—Microembossing
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
    • B29C—SHAPING OR JOINING OF PLASTICS; SHAPING OF MATERIAL IN A PLASTIC STATE, NOT OTHERWISE PROVIDED FOR; AFTER-TREATMENT OF THE SHAPED PRODUCTS, e.g. REPAIRING
    • B29C59/00—Surface shaping of articles, e.g. embossing; Apparatus therefor
    • B29C59/02—Surface shaping of articles, e.g. embossing; Apparatus therefor by mechanical means, e.g. pressing
    • B29C59/022—Surface shaping of articles, e.g. embossing; Apparatus therefor by mechanical means, e.g. pressing characterised by the disposition or the configuration, e.g. dimensions, of the embossments or the shaping tools therefor
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
    • B29K—INDEXING SCHEME ASSOCIATED WITH SUBCLASSES B29B, B29C OR B29D, RELATING TO MOULDING MATERIALS OR TO MATERIALS FOR MOULDS, REINFORCEMENTS, FILLERS OR PREFORMED PARTS, e.g. INSERTS
    • B29K2067/00—Use of polyesters or derivatives thereof, as moulding material

Definitions

  • the present invention relates to a heat-forming optical film polyester that can be formed into a wide variety of shapes such as heat-formability on the surface, particularly ultra-high definition and high aspect ratio, and has excellent heat resistance and transparency. .
  • Optical elements have long been made of glass with excellent transparency and low birefringence. However, since it is inferior in moldability and difficult to reduce in weight, recently, polymer materials with excellent moldability, light weight, and easy property control have been used for disc substrates, lenses, cables, various display films, etc. according to their characteristics. Yes.
  • Imprint lithography is a technique for transferring a pattern on a mold to a resin, and there are two types of methods, thermal and optical.
  • the thermal type is a method in which a thermoplastic resin is heated to a glass transition temperature (Tg) or higher and lower than the melting point (Tm), and a mold having a concavo-convex pattern is pressed thereon, and the optical type is a photocurable property.
  • Tg glass transition temperature
  • Tm melting point
  • the optical type is a photocurable property.
  • the pattern on the mold is transferred to the resin by irradiating and curing the light with the mold pressed against the resin.
  • the thermal method has a feature that it is easier to shape a shape with a higher aspect ratio.
  • these technologies require initial costs for mold fabrication, many microstructures can be replicated from a single mold, resulting in a technology that allows the microstructure to be shaped cheaply compared to photolithography. It is.
  • Patent Document 1 liquid crystal display devices
  • Patent Document 2 optical waveguides used for optical communication
  • PC polycarbonate
  • PMMA polymethyl methacrylate
  • Polyester is promising because of its excellent cost, mechanical strength, and melt film-forming properties.
  • Polyethylene terephthalate (PET) is crystalline, so it has a high Tm, poor formability, and is not suitable for shaping. It is necessary to increase the mold temperature. Mold heating, 2. 2. imprint shaping; 3. mold cooling; There is a problem that the cycle time required for mold peeling is long and the productivity is low, and the heat resistance is low due to the low Tg.
  • the present invention solves the above-mentioned problems of the prior art, and can be shaped into a wide variety of shapes such as heat-formability on the surface, especially ultra-high definition and high aspect ratio, and heat-shaping productivity.
  • Another object of the present invention is to provide a polyester resin for heat-shaped optical film having excellent heat resistance and transparency.
  • a polyester resin for a heat-shaped optical film having a glass transition temperature (Tg) of 83 ° C. or higher, a melting point (Tm) of 230 ° C. or lower, and a crystal melting heat ( ⁇ Hm) of 0.3 J / g or higher.
  • Tg glass transition temperature
  • Tm melting point
  • ⁇ Hm crystal melting heat
  • polyester resin for heat-shaped optical film as described in any one of (1) to (9), which is as follows.
  • (11) The polyester resin for heat-shaped optical film as described in any one of (1) to (10), wherein IV (intrinsic viscosity) is 0.55 or more and 0.75 or less.
  • a polyester resin for a heat-shaped optical film which is excellent in heat-shaping property and has excellent heat-shaping productivity, heat resistance and transparency. By using this, it can be used for applications that require both heat-shaping productivity and heat resistance, such as a prism sheet for a backlight used in various display members.
  • (a) is a schematic view of the cross section of the shaping portion of the mold
  • (b) is a schematic view of the shaping portion of the mold as viewed from diagonally above
  • (c) is shaped by the mold. It is the figure which showed the film cross section typically.
  • a Prism sheet using the polyester resin of the present invention
  • b Diffusion sheet
  • c Diffuser plate
  • d Reflective sheet
  • e fluorescent lamp
  • f heating / cooling plate
  • g mold
  • h film
  • the present invention solves the above problems, that is, the problems of conventional resins, and after intensive studies, a specific polyester resin whose composition is controlled to have specific physical properties solves the above problems all at once, and heat shaping
  • the inventors have found that a sheet having excellent properties, heat shaping productivity, heat resistance, and transparency can be formed, and have reached the present invention.
  • the polyester resin of the present invention has a glass transition temperature (Tg) of 83 ° C. or higher, a melting point (Tm) of 230 ° C. or lower, and a crystal melting heat ( ⁇ Hm) of 0.3 J / g or higher.
  • the resin to be heat-shaped is preferably uniform and low in crystallinity without stretch distortion or the like before heat-forming, and has high Tg and does not hinder transparency after forming. Crystallization within a range is preferable from the viewpoint of the thermal stability of the shaped shape. Only by raising the glass transition temperature, the thermal stability after shaping is not sufficient, and excellent thermal stability is realized by combining with crystallization. On the other hand, if the glass transition temperature is too high, the heat shaping property is remarkably lowered.
  • the resin In order to achieve both the amorphousness before shaping and the transparency after shaping, that is, the microcrystalline structure, the resin must be crystalline, and before shaping, the resin is near the melting point of the polyester resin of the present invention. It is necessary to remelt the surface layer by heat treatment at the heat treatment temperature and to make it uniform by relaxing the orientation in order to realize excellent formability. In the heat treatment, the lower the melting point of the polyester resin of the present invention is, the easier it is to make it uniform.
  • the polyester resin of the present invention having a shaping layer on the surface layer of a base material having a higher melting point (here, the melting point of the resin constituting the base material is Tm1) (here, the heat treatment temperature (Ta) is preferably Tm1> Ta> Tm2 from the viewpoint of film forming property and heat treatment effect, When Tm2 is 230 ° C. or lower, stable film-forming is possible even when PET having a melting point of 260 ° C. is selected as the base material, film-forming properties, heat-forming properties, compatibility between layers, and low cost To preferred. In addition to the heat treatment step, it is preferable in terms of formability such as mold followability that the melting point is low at the time of heat shaping.
  • the melting point of the polyester resin of the present invention is preferably 230 ° C. or less, and if it is higher than this, the homogenization and low crystallization during heat treatment will be insufficient, and the heat formability will deteriorate.
  • the melting point is higher than 230 ° C. because stable film formation and heat treatment cannot be achieved in the heat treatment step.
  • a lower limit of the melting point is not particularly provided, but if it is lower than 130 ° C., the glass transition temperature is also lowered, which is not preferable.
  • the polyester resin of the present invention preferably has Tg ⁇ 83 ° C. More preferably, Tg ⁇ 85 ° C.
  • Tg ⁇ 85 ° C. By being in this range, for example, in the case of an optical sheet such as a prism sheet used in the field of flat panel displays, the required long-term heat resistance can be greatly improved.
  • the temperature is lower than this temperature, the shape that is thermally shaped during long-term use changes and the performance deteriorates. There is no particular upper limit, but if it is higher than 150 ° C., the heat formability is lowered, which is not preferable.
  • the polyester resin of the present invention preferably satisfies ⁇ Hm ⁇ 0.3 J / g. More preferably, ⁇ Hm ⁇ 1.0 J / g, and further preferably ⁇ Hm ⁇ 20.0 J / g. If it is smaller than this, it will not be crystallized at the time of heat shaping, and the thermal stability will decrease. There is no particular upper limit, but if it exceeds 40.0 J / g, it may be crystallized too much during heat shaping, which may result in poor molding.
  • the polyester resin of the present invention is preferably a homopolymer having a diol component and a dicarboxylic acid component each consisting of one component, and is preferably a copolymerized polyester resin in which either the diol component or the dicarboxylic acid component or both are composed of a plurality of monomers.
  • the type of monomer is not particularly limited. Specific monomers and the like will be described later.
  • terephthalic acid residue such as dimethyl terephthalate (DMT)
  • naphthalenedicarboxylic acid residue such as dimethyl 2,6-naphthalenedicarboxylate (DMN)
  • ethylene glycol ethylene glycol
  • Tg and Tm are determined by the copolymer composition of the polyester resin.
  • Tg it is effective to select a cyclic monomer having a rigid structure, and to increase its composition ratio, and in order to reduce the Tm, to select a linear monomer having a flexible structure, It is effective to disturb the ordered structure and reduce the crystallinity by introducing a copolymer component.
  • Tg is on the line connecting Tg of homopolymers such as PET and PEN having a single diol component and dicarboxylic acid component, and is a rigid monomer of cyclic monomer of 2,6-naphthalenedicarboxylic acid.
  • Tm is higher in the case of a homopolymer than that of a copolymer, and this Tm is determined by the rigidity of the monomer.
  • Tm decreases when a linear monomer having a flexible structure is selected as the monomer, or when the composition departs from a single composition and the regularity of the polymer backbone decreases.
  • Tm disappears and becomes amorphous.
  • Tg is 83 ° C. or higher and Tm is 230 ° C. or lower in the region of about 12 mol% of 2,6-naphthalenedicarboxylic acid.
  • ⁇ Hm generally decreases as the composition approaches the amorphous region. Therefore, in a region where ⁇ Hm does not satisfy 0.3 J / g or more, it can be controlled to 0.3 J / g or more by adding a crystal nucleating agent or by controlling IV low to facilitate crystallization.
  • a monomer that contributes to a high Tg is selected, the melting point is lowered by copolymerization of other monomers, and the copolymerization ratio is made amorphous. It is effective to select a composition range that does not become necessary, and it is effective to increase ⁇ Hm by adding a crystal nucleating agent as necessary.
  • the temperature difference ( ⁇ Tcg: Tcc ⁇ Tg) between the temperature rising crystallization temperature (Tcc) and the glass transition point (Tg) is 50 ° C. ⁇ ⁇ Tcg ⁇ 90 ° C. . More preferably, 60 ° C. ⁇ ⁇ Tcg ⁇ 90 ° C., and still more preferably 60 ° C. ⁇ ⁇ Tcg ⁇ 85 ° C.
  • ⁇ Tcg is larger than this, crystallization at the time of heat shaping does not proceed sufficiently, and the thermal stability is lowered. If ⁇ Tcg is smaller than this, it will crystallize at the time of the heat treatment before the heat shaping, and the heat shaping property is lowered.
  • the polyester resin of the present invention preferably contains a crystal nucleating agent.
  • ⁇ Tcg can be controlled to some extent independent of Tg and Tm of the resin, and various thermal characteristics can be more easily satisfied.
  • the crystal nucleating agent has the effect of reducing ⁇ Tcg, and the effect can be adjusted by the type and the amount added. Further, since the number of crystal nuclei increases due to the presence of the crystal nucleating agent, the size of the generated crystal becomes small and uniform, and whitening during microcrystallization can be suppressed.
  • crystal nucleating agent those generally used as polymer crystal nucleating agents can be used without particular limitation, and any of inorganic crystal nucleating agents and organic crystal nucleating agents can be used.
  • specific examples of inorganic crystal nucleating agents include talc, kaolin, montmorillonite, synthetic mica, clay, zeolite, silica, graphite, carbon black, calcium sulfide, boron nitride, aluminum, zinc oxide, magnesium oxide, titanium oxide, and oxidation.
  • metal oxides such as aluminum and neodymium oxide, metal carbonates such as calcium carbonate, and metal sulfates such as barium sulfate.
  • organic crystal nucleating agents are preferably modified with an organic substance in order to enhance dispersibility in the composition.
  • organic crystal nucleating agent include acetic acid, oxalic acid, propionic acid, butyric acid, octanoic acid, stearic acid, montanic acid, benzoic acid, terephthalic acid, lauric acid, myristic acid, toluic acid, salicylic acid, Combination of various organic carboxylic acids such as naphthalenecarboxylic acid and cyclohexanecarboxylic acid, various organic sulfonic acids such as p-toluenesulfonic acid and sulfoisophthalic acid, and various metals such as sodium, potassium, lithium, calcium, magnesium, barium, and aluminum Organic carboxylic acid metal salt, organic sulfonic acid metal salt, stearic acid amide, ethylenebislauric acid amide, palmitic acid amide, hydroxy stearic acid
  • the crystal nucleating agent used in the present invention among those exemplified above, at least one selected from organic carboxylic acid sodium salt and talc is particularly preferable from the viewpoint of crystallization promoting effect and low haze of the resin.
  • the crystal nucleating agent used in the present invention may be used alone or in combination of two or more.
  • the blending amount of the crystal nucleating agent is preferably in the range of 0.01 to 30 parts by weight, more preferably in the range of 0.05 to 5 parts by weight with respect to 100 parts by weight of the polyester resin containing various fillers.
  • the range of 1 to 3 parts by weight is more preferable.
  • various thermal characteristic values such as Tm, Tg, Tcc, ⁇ Hm, and heat-up crystallization calorie ( ⁇ Hc) of the polyester resin in the present invention are temperature rise curves of differential scanning calorimetry (DSC) of a sample in a substantially amorphous state. It is a value calculated from Specifically, a 2nd cycle after the DSC is melted in the first cycle and then rapidly cooled to an amorphous solid is used.
  • DSC differential scanning calorimetry
  • the cooling rate after the 1st cycle melting must be 100 ° C./min or more, and the difference ⁇ Hm ⁇ Hc between ⁇ Hm and ⁇ Hc of the resin when the temperature rises by 2nd cycle is ⁇ Hm ⁇ Hc ⁇ 5 J / g It must be amorphous. If it is larger than this, crystallization proceeds in the process of cooling the resin, and an accurate value cannot be calculated. In that case, it is necessary to further increase the cooling rate by changing the cooling rate setting, or by taking the sample out of the electric furnace and exposing it to cold air or immersing it in liquid nitrogen in the sample cooling process.
  • the sodium element is more preferably in the range of 50 to 1500 ppm, more preferably 150 to 1000 ppm with respect to the polyester resin.
  • the haze of the resin is increased, which is not suitable for optical applications.
  • it is smaller than this range sufficient crystallization promoting effect is not exhibited.
  • the polyester resin of the present invention was prepared by dissolving 2 g of polyester resin in 20 ml of a phenol / 2,1,1,2,2-tetrachloroethane 3/2 (volume ratio) mixed solvent and measuring the haze of the solution measured using a cell having an optical path length of 20 mm. Is preferably 40% or less. More preferably, it is 10% or less, More preferably, it is 5% or less. If it exceeds this range, the amount of transmitted light decreases in optical applications, and if the same amount of transmitted light is to be secured, it is not preferable because the film must be made extremely thin.
  • the number average average diameter in the resin of the crystal nucleating agent or the crystal nucleating agent derivative particles is preferably 1.2 ⁇ m or less.
  • the crystal nucleating agent derivative particles refer to particles precipitated in the resin by the crystal nucleating agent.
  • various metal salts such as alkali metal salts, alkaline earth metal salts, magnesium, and aluminum are added, the metal itself becomes precipitated particles due to a reducing component such as a phosphorus compound, or metal is disposed at the end of the polyester molecule.
  • these particles are included in the crystal nucleating agent derivative particles.
  • the number average particle diameter is more preferably 1.0 ⁇ m or less, further preferably 0.5 ⁇ m or less, and most preferably 0.3 ⁇ m or less. If it is larger than this range, the haze becomes large and it is not suitable for optical applications. Moreover, when the pattern to be heat-formed is a fine shape, the shape after heat-forming may be adversely affected.
  • the intrinsic viscosity (IV) of the polyester resin of the present invention is preferably 0.55 or more and 0.75 or less.
  • a more preferable range is 0.57 or more and 0.7 or less, and a most preferable range is 0.58 or more and 0.65 or less. When it is larger than this range, the heat formability is lowered, and when it is smaller than this range, the heat resistance is lowered.
  • the polyester resin of the present invention is a surface forming agent, processability improver, antioxidant, ultraviolet absorber, light stabilizer, antistatic agent, lubricant, in addition to the above-mentioned crystal nucleating agent within the range not impairing the heat formability.
  • Additives such as antiblocking agents, soft particles, plasticizers, antifogging agents, colorants, dispersants, infrared absorbers and the like can be added.
  • the additive may be colorless or colored, but is preferably colorless and transparent so as not to impair the characteristics of the optical film.
  • any of addition during polymerization, melt kneading, and solution kneading can be preferably applied. Among these, melt kneading is most preferable from the viewpoint of ease of polymerization control and cost.
  • the alloy component include various acrylics, polyesters, polycarbonates, cyclic olefins, etc., but it is desirable to contain the resin of the present invention in an amount of 50% by weight or more in the alloy composition, and the entire alloy composition satisfies the characteristics of the present invention. There is a need.
  • the method for polymerizing the polyester resin of the present invention is not limited, and a known polymerization method such as an esterification method using a dicarboxylic acid and a glycol as a derivative, a transesterification method using a dicarboxylic acid diester and a glycol, or the like can be used.
  • a known polymerization method such as an esterification method using a dicarboxylic acid and a glycol as a derivative, a transesterification method using a dicarboxylic acid diester and a glycol, or the like can be used.
  • Various diols can be used as the diol component.
  • aliphatic diols such as ethylene glycol, trimethylene glycol, 1,2-propanediol, 1,3-propanediol, butanediol, 2-methyl-1,3-propanediol, hexanediol, neopentylglycol, Cyclohexanedimethanol, cyclohexanediethanol, decahydronaphthalene diethanol, decahydronaphthalene diethanol, norbornane dimethanol, norbornane diethanol, tricyclodecane dimethanol, tricyclodecane diethanol, tetracyclododecane dimethanol, tetracyclo Saturated alicyclic primary diols such as decanediethanol, decalin dimethanol and decalin diethanol, 2,6-dihydroxy-9-oxabicyclo [3,3, ] Nonane, 3,9-bis (2-hydroxy-1,1-dimethylethyl
  • ethylene glycol is preferred from the viewpoint of reactivity and low cost. Further, from the viewpoint of heat resistance, a cyclic diol is also preferable, and as the cyclic diol, for example, spiroglycol, cyclohexanedimethanol, tricyclodecanedimethanol and the like are preferable. Of these, ethylene glycol is most preferred.
  • heat resistance, reactivity, and cost can be adjusted by a combination of spiroglycol and ethylene glycol.
  • the dicarboxylic acid component of the polyester of the present invention is not particularly limited, and general ester forming derivatives of carboxylic acids can be used.
  • ester-forming derivatives acid anhydrides such as terephthalic anhydride, acid halides such as acid chlorides corresponding to dicarboxylic acids, lower alkyl esters such as dimethyl terephthalate, and the like can be used.
  • dicarboxylic acid includes an ester-forming derivative of dicarboxylic acid.
  • the aromatic dicarboxylic acid includes, but is not limited to, phthalic acid, terephthalic acid, isophthalic acid, naphthalenedicarboxylic acid, 4,4′-diphenyldicarboxylic acid, diphenylether-4,4′-dicarboxylic acid, 4,4'-diphenylmethanedicarboxylic acid, benzylmalonic acid and the like.
  • chain aliphatic dicarboxylic acids examples include succinic acid, glutaric acid, adipic acid, pimelic acid, suberic acid, azelaic acid, sebacic acid, methylmalonic acid, ethylmalonic acid, 2,2-dimethylsuccinic acid, 2,3- Examples include dimethyl succinic acid, 2,3-dimethyl succinic acid, 3-methyl glutaric acid, and 3,3-dimethyl glutaric acid.
  • alicyclic dicarboxylic acids examples include 1,2-cyclohexanedicarboxylic acid, 1,3-cyclohexanedicarboxylic acid, 1,4-cyclohexanedicarboxylic acid, cyclopentanedicarboxylic acid, 1,4-cyclohexanedione-2,5-dicarboxylic acid.
  • 2,6-decalin dicarboxylic acid 1,5-decalin dicarboxylic acid, 1,6-decalin dicarboxylic acid, 2,7-decalin dicarboxylic acid, 2,3-decalin dicarboxylic acid, 2,3-norbornane dicarboxylic acid, bicyclo Saturated alicyclic dicarboxylic acids such as [2,2,1] heptane-3,4-dicarboxylic acid, cis-5-norbornene-endo-2,3-dicarboxylic acid, methyl-5-norbornene-2,3 -Dicarboxylic acid, cis-1,2,3,6-tetrahydrophthalic acid, methyltetrahydrophthalic acid, 3 4,5,6-tetrahydrophthalic acid, unsaturated aliphatic dicarboxylic acids such as exo-3,6-epoxy-1,2,3,6-tetrahydrophthalic acid can be exemplified.
  • cyclic dicarboxylic acids are preferred from the viewpoint of heat resistance.
  • terephthalic acid and naphthalenedicarboxylic acid are preferable from the viewpoints of polymerizability, cost, and resin properties. As long as the object of the present invention is not impaired, these can be used alone or in combination of two or more. For example, Tg and Tm can be adjusted by using terephthalic acid and naphthalenedicarboxylic acid in combination.
  • 2,6-naphthalenedicarboxylic acid is used as the copolymer component as the dicarboxylic acid component
  • 2,6-naphthalenedicarboxylic acid is 8 to 17 mol% in the dicarboxylic acid component.
  • the more preferable copolymerization ratio of 2,6-naphthalenedicarboxylic acid is 10 to 15 mol%, most preferably 11 to 14 mol%.
  • the catalyst for producing the polyester of the present invention is not particularly limited, and various catalysts can be used.
  • effective catalysts for transesterification include alkali metal or alkaline earth metal compounds such as calcium acetate, magnesium acetate, lithium acetate, sodium acetate, manganese acetate, cobalt acetate, zinc acetate, tin acetate, alkoxide titanium, etc.
  • antimony compounds such as antimony trioxide
  • germanium compounds such as germanium oxide
  • various titanium compounds such as alkoxide titanium, and composite oxides of aluminum and silica can be used.
  • the stabilizer examples include phosphoric acid-based, phosphorous acid-based, phosphonic acid-based, and phosphinic acid-based compounds.
  • these ester compounds are preferable from the viewpoint of suppressing the formation of foreign matters, and phosphonic acid ester derivatives are particularly preferable as foreign materials.
  • triethylphosphonoacetate is specifically preferred.
  • the phosphorus compound is preferably added at the beginning of the polycondensation reaction after the esterification reaction or after the transesterification reaction.
  • the polymerization method is a transesterification method
  • dimethyl terephthalate, dimethyl naphthalene dicarboxylate, or ethylene glycol is used
  • dimethyl terephthalate, dimethyl naphthalene dicarboxylate, or ethylene glycol is reacted so as to have a predetermined polymer composition.
  • the reactivity is improved by adding 1.7 to 2.3 mole times of ethylene glycol with respect to the total dicarboxylic acid component.
  • magnesium acetate is added as a catalyst and stirred. At 150 ° C., these monomer components become a homogeneous molten liquid.
  • the reaction is terminated, and the resin is discharged from the polymerization apparatus into a water tank in a strand shape.
  • the discharged resin is rapidly cooled in a water tank, and after winding it is made into chips with a cutter.
  • the target IV is 0.7 or more
  • the chip is temporarily formed at an IV lower than the target, and then the target IV is reduced under Tm of the chip, specifically, at a temperature of 170 to 230 ° C. and 133 Pa or less. It is also preferable to perform solid phase polymerization.
  • the composition of the heat-shaped optical film of the present invention may be a single layer film composed only of the polyester resin of the present invention, or may be a laminate composed of a plurality of resin layers.
  • a laminate comprising a heat shaping layer made of a polyester resin and a support layer is preferred.
  • characteristics such as slipperiness and friction resistance, mechanical strength, and heat resistance can be imparted as compared with the case of a single layer film.
  • the material of the base material of the support layer to be laminated is not particularly limited as long as the optical properties are not inhibited, and organic film base materials such as polyester, polycarbonate, acrylic, cycloolefin polymer, polyimide, epoxy, polyethylene, glass, etc.
  • the inorganic base material is exemplified, but polyester, particularly polyethylene terephthalate is preferable from the viewpoint of adhesion between laminated layers, film-forming property, and cost.
  • a heat shaping layer made of the polyester resin of the present invention on at least one outermost layer of the laminate. This is because the heat formability and heat resistance of the film surface are improved by providing the heat shaping layer comprising the polyester resin of the present invention in the outermost layer. Moreover, in the case of a laminated body, it is more preferable to provide the heat shaping layer which consists of the polyester resin of this invention in both outermost layers. Further, it is more preferable to have a laminated structure in which the front and back are symmetric when viewed from the center in the thickness direction of the laminated body. Satisfying such requirements is preferable because film curling caused by heat shaping, heat resistance test, and moist heat resistance test is reduced.
  • the number of layers is not particularly limited as long as this requirement is satisfied, but the preferred number of layers is 3 or more.
  • the resin of the present invention is heated and melted in an extruder and extruded from a die onto a cast drum cooled to form a sheet.
  • a processing method (melt cast method) can be mentioned.
  • a sheet forming material is dissolved in a solvent, and the solution is extruded from a die onto a support such as a cast drum or an endless belt to form a film, and then the solvent is dried and removed from the film layer to form a sheet.
  • a method of processing into a solution (solution casting method) or the like can also be used.
  • thermoplastic resins are charged into a plurality of extruders, melted and coextruded on a cast drum cooled from a die
  • a method of laminating the raw material of the coating layer into a sheet made of a single film into an extruder, melt extrusion and extruding it from the die (melt laminating method), a film made as a single layer film and a heat-shaped film respectively
  • thermo laminating method thermocompression bonding with a heated group of rolls
  • adhesion method a method of laminating via an adhesive (adhesion method), and other materials for film formation are dissolved in a solvent, and the solution is
  • a method of coating on a film (coating method) or the like can be used.
  • the heat-shaped optical film of the present invention is preferably oriented in a uniaxial or biaxial direction. More preferably, it is oriented in the biaxial direction.
  • an oriented film it is possible to easily impart mechanical strength, dimensional stability, and the like preferable as a base material.
  • the configuration of the heat-shaped optical film of the present invention is particularly preferably a laminate, and more preferably biaxially oriented.
  • stretching methods for orientation sequential biaxial stretching methods (stretching methods that combine stretching in each direction, such as a method of stretching in the width direction after stretching in the longitudinal direction), simultaneous biaxial stretching methods (longitudinal direction) And a method of stretching them in the width direction at the same time) or a method combining them can be used, but the present invention is not limited to these stretching methods.
  • excellent mechanical properties can be imparted by biaxially stretching the polyester film by these stretching methods.
  • the plane orientation coefficient (hereinafter sometimes referred to as fn) of at least one heat-shaped layer is 0.12 or less.
  • the resin constituting the thermoformed layer becomes an amorphous state with low orientation, and a fine high aspect ratio pattern and a large area are formed. It becomes possible.
  • the plane orientation coefficient is larger than 0.12, the orientation of the resin constituting the heat-shaped layer becomes strong and the elastic modulus becomes high, so that the above-described molding becomes impossible.
  • the plane orientation coefficient of at least one heat-shaped layer can be adjusted by the stretching ratio of the laminated film, the heat treatment temperature after biaxial stretching, and the heat treatment time as long as the effects of the present invention are not impaired.
  • the plane orientation coefficient of the molding layer by setting the draw ratio to a low ratio or increasing the heat treatment time.
  • the lower limit of the plane orientation coefficient is not particularly set, it is preferably 0.05 or more in order to avoid deterioration in film forming property due to high heat treatment temperature and long heat treatment time.
  • a temperature not lower than the melting endothermic peak temperature (Tm2 ′) of the resin constituting the heat-shaped layer after biaxial stretching and lower than the melting endothermic peak temperature (Tm1 ′) of the resin constituting the support layer There is a method in which the effect of the present invention is manifested by applying a heat treatment.
  • the resin constituting the heat-shaped layer becomes an amorphous state, and the resin constituting the support layer can maintain the orientation state without melting and improve the mechanical strength. is there. That is, it is preferable to set the heat treatment temperature after biaxial stretching in this range because a film having both formability and mechanical strength can be obtained in a consistent film forming process by coextrusion.
  • the heat treatment temperature may be higher than the melting endothermic peak temperature Tm2 ′ of the resin constituting the heat shaping layer, but is preferably 5 ° C or higher, more preferably 10 ° C or higher, and further preferably 20 ° C. High temperature.
  • the orientation relaxation of the resin constituting the heat shaping layer proceeds and the amorphous part increases. It is preferable because moldability is improved.
  • the preferred thickness (thickness, film thickness) of the biaxially oriented polyester film of the present invention is preferably in the range of 10 ⁇ m to 5 mm. More preferably, it is 20 ⁇ m to 2 mm, and still more preferably 20 ⁇ m to 200 ⁇ m.
  • a heat shaping layer made of the resin of the present invention having a thickness in the range of 1 ⁇ m to 30 ⁇ m on the substrate. Further, when the heat shaping layers are provided on both outermost layers, the thickness of each heat shaping layer is preferably 1 ⁇ m to 30 ⁇ m.
  • the thickness of the heat shaping layer has a strong influence on the heat shaping property. That is, the volume of the heat-shaped layer is preferably equal to the volume amount deformed by heat shaping, and more preferably the volume of the heat-shaped layer is larger than the volume amount deformed by heat shaping. More preferably, the thickness of the heat shaping layer is larger than the height at which the heat shaping layer is deformed. This is because the resin constituting the heat-shaped layer in the vicinity of the support layer is restricted in thermal motion by the support layer, and it is difficult to impart a shape by heat-forming.
  • the shape imparted by heat shaping is preferably a prism shape with the hypotenuse of an isosceles right triangle as the base.
  • a prism shape By imparting a prism shape, a biaxially stretched polyester film having a high brightness enhancement effect can be obtained.
  • the length (pitch) of the base of each prism shape is preferably in the range of 1 ⁇ m to 50 ⁇ m. More preferably, it is 5 ⁇ m to 25 ⁇ m. By setting it as this range, the favorable brightness improvement effect is acquired and the total thickness of a film can also be made small.
  • the thickness of the heat-shaped layer is preferably larger than the height of deformation due to the shape to be applied, and is preferably about 30 ⁇ m. If a prism shape with a small pitch is provided by heat shaping, the influence of the wave nature of light becomes strong, a diffraction phenomenon occurs, and a sufficient brightness improvement effect cannot be obtained, which is not preferable. For this reason, if the thickness of the heat-shaped layer is less than 1 ⁇ m, the effect as a prism cannot be obtained sufficiently, which is not preferable because it is a biaxially oriented polyester film that is not suitable for heat-shaping.
  • the film is heated in a temperature range not less than the glass transition temperature (Tg) and less than the melting point (Tm), the film and the mold are brought close to each other, pressed at a predetermined pressure, and held for a predetermined time. Next, the temperature is lowered while maintaining the pressed state. Finally, release the press pressure and release the film from the mold.
  • a roll-shaped mold having irregularities formed on the surface is used to form a roll-shaped sheet, and a roll It may be a roll-to-roll continuous molding to obtain a shaped molded body.
  • Roll-to-roll continuous molding is superior to the lithographic press method in terms of productivity.
  • the heating temperature and the press temperature T1 are preferably in the range of the glass transition temperature Tg to Tg + 60 ° C. of the polyester resin of the present invention constituting the heat-shaped layer. If the glass transition temperature Tg of the resin constituting the heat shaping layer is not exceeded, the softening of the resin constituting the heat shaping layer has not sufficiently progressed, so that deformation when the mold is pressed is less likely to occur. The pressure required for molding becomes very high. If the temperature exceeds this range, the heating temperature and the press temperature T1 become too high, which is inefficient in energy, and the volume fluctuation during heating / cooling of the sheet is about one digit larger than that of the mold.
  • the sheet cannot be released due to being bitten into the mold, and even if the sheet can be released, the accuracy of the pattern is deteriorated, or the pattern is partially lost, which is not preferable.
  • the heating temperature and the press temperature T1 within this range, both good moldability and mold release properties can be achieved.
  • the pressing pressure is preferably 0.5 to 50 MPa, although it depends on the plane orientation coefficient of the heat-shaped layer. More preferably, it is 1 to 30 MPa. If it is less than this range, the resin is not sufficiently filled in the mold, and the pattern accuracy is lowered. On the other hand, exceeding this range is not preferable because the required load increases, the load on the mold increases, and the repeated use durability decreases. By setting the press pressure within this range, good moldability and durability of the mold can be maintained.
  • the press pressure holding time is preferably in the range of 0 second to 10 minutes, depending on the plane orientation coefficient of the heat-shaped layer. Exceeding this range is not preferable because the tact time is too long, the productivity is not increased, the resin is thermally decomposed, and the mechanical strength of the molded sheet may be lowered. In the molding method preferably employed in the present invention, both good moldability and uniformity can be achieved by setting the holding time within this range.
  • the press pressure release temperature T2 is preferably lower than the press temperature T1 within the temperature range of the glass transition temperature Tg + 20 ° C. of the resin constituting the heat shaping layer. Exceeding this range is not preferable because the resin at the time of pressure release is softened, the fluidity is high, and the molding accuracy is lowered, for example, the pattern is deformed. In the molding method preferably employed in the present invention, by setting the press pressure release temperature T2 within this range, both good moldability and mold release properties can be achieved.
  • the mold release temperature T3 is preferably within the temperature range equal to or lower than the Tg.
  • a temperature range of 20 ° C. to the Tg is more preferable. If it exceeds this range, the fluidity of the resin at the time of mold release is high, so that the pattern is deformed and the accuracy is lowered, or the sheet itself is deformed.
  • by setting the temperature at the time of mold release within this range it is possible to release the pattern with high accuracy and to suppress deformation of the sheet itself.
  • the molded product produced using the heat-shaped sheet of the present invention can be used for various applications.
  • applications optical circuits, optical connector members, prism sheets and other displays
  • the member is exemplified.
  • Resin solution haze 2 g of polyester was dissolved in 20 ml of a phenol / 1,1,2,2-tetrachloroethane 3/2 (weight ratio) mixed solvent, and a haze meter (suga Analysis was carried out by integrating sphere photoelectric photometry with HZ-1) manufactured by Test Instruments.
  • Resin sodium element content 1 g of polyester was heated on an electric stove to incinerate the polymer, then placed in an electric furnace and treated at 650 ° C. for 1 hour to completely incinerate.
  • This ashed product was dissolved in dilute hydrochloric acid to obtain a measurement solution, the absorbance was measured at a measurement wavelength of 589 nm using an atomic absorption measurement device, and the amount of sodium was calculated from a calibration curve. The content was calculated for the case of 30 ppm or more.
  • Average particle diameter A part of the sheet is cut out from the center of the sheet, an ultrathin section having a thickness of 0.2 ⁇ m is prepared using a microtome, and observed with a transmission electron microscope (TEM) H-7100 manufactured by Hitachi, Ltd. About 100 dispersed particles, the primary particle diameter was measured, and the average value was defined as the dispersed particle diameter.
  • TEM transmission electron microscope
  • Thermoforming formability After cutting out the cross section of the heat forming product and depositing platinum-palladium, photographs were taken using a scanning electron microscope S-2100A manufactured by Hitachi, Ltd., and the cross section was observed. It was.
  • the mold used for shaping has a shape in which a plurality of triangular prisms having a right-angled isosceles triangle (height 12 ⁇ m) with a vertical angle of 90 ° are formed on the surface in parallel with a pitch of 24 ⁇ m (cross section: figure 2 (a), perspective view: FIG. 2 (b)).
  • FIG. 2 (c) shows a molded product shaped using the mold.
  • the average value of the ratio b / a of the height b (mold design value 12 ⁇ m) and the 1 ⁇ 2 double width a (mold design value 12 ⁇ m) of this molded product pattern convex portion is 0.8 or more: ⁇ 0.7 or more and less than 0.8: ⁇ Less than 0.7: ⁇ It was. If an evaluation result is (triangle
  • Luminance retention rate The prism sheet formed by heat-molding the resin of the present invention is subjected to a heat resistance test at 85 ° C. for 250 hours, and (luminance after the heat resistance test / luminance before the test) ⁇ 100 (%) is the luminance retention rate. It was.
  • the prism sheet was fixed on the Kapton sheet with tape at the four corners and treated in a hot air oven at 85 ° C. for 250 hours.
  • “Clarex” DR-65C, c) in FIG. 3 diffusion sheet (manufactured by Kimoto Co., Ltd., “Light-up” 188GM3, b in FIG. 3), prism formed by heat-molding the resin of the present invention
  • the measurement position was performed on a line shifted to the right or left by 25 mm from the center of the backlight in the direction perpendicular to the linear portion of the fluorescent tube.
  • the brightness was evaluated as an average value of the measurement positions.
  • Example 1 Weigh each at a ratio of 86.2 parts by weight of dimethyl terephthalate and 14.8 parts by weight of dimethyl 2,6-naphthalenedicarboxylate and 62.6 parts by weight of ethylene glycol (2 moles of dicarboxylic acid component). After charging and melting the contents at 150 ° C., 0.06 parts by weight of magnesium acetate tetrahydrate, 0.02 parts by weight of antimony trioxide and 0.003 parts by weight of lithium acetate dihydrate were added and stirred as a catalyst. .
  • the temperature was raised to 190 ° C. over 60 minutes, further raised to 200 ° C. over 60 minutes, and then methanol was distilled while raising the temperature to 240 ° C. over 90 minutes. After distillation of a predetermined amount of methanol, an ethylene glycol solution containing 0.04 part by weight of triethylphosphonoacetate was added as a catalyst deactivator and stirred for 5 minutes to stop the transesterification reaction.
  • the reaction product is charged into a polymerization apparatus, and while the temperature in the apparatus is increased from 235 ° C. to 290 ° C. over 90 minutes, the pressure in the apparatus is reduced from normal pressure to vacuum to distill ethylene glycol.
  • the reaction is terminated when the viscosity of the reaction product increases with the progress of the polymerization reaction and reaches a predetermined stirring torque.
  • the inside of the polymerization apparatus was returned to normal pressure with nitrogen gas, the valve at the bottom of the polymerization apparatus was opened, and gut-shaped polyester was discharged into the water tank. The discharged polyester resin was quenched in a water tank and then cut with a cutter to form a chip.
  • the obtained polyester chip was put into a water tank filled with 95 ° C. ion exchange water and treated with water for 5 hours.
  • the chip after the water treatment was separated from the water by a dehydrator. Fines contained in the polyester chips were also removed by this water treatment.
  • a polyester resin A was thus obtained.
  • Table 1 shows the IV, solution haze, and thermal characteristics of the obtained polyester resin.
  • This polyester resin A and PET resin (IV 0.65) were each vacuum-dried at 170 ° C. for 3 hours and then melted at 280 ° C. in separate extruders, both outermost layers being resin A and PET resin being the inner layer.
  • the laminated resin extruded from the layer coextrusion die was closely cooled and solidified while applying an electrostatic charge to a cooling drum maintained at 25 ° C.
  • the cast film was stretched 3.3 times in a longitudinal direction at 90 ° C. by a roll type stretching machine.
  • it was introduced into a tenter, stretched by 3.4 times at 110 ° C., and then heat treated in a temperature zone controlled at 238 ° C., followed by 4% relaxation treatment at 170 ° C. in the width direction, and then to room temperature.
  • the film was cooled and wound to obtain a three-layer laminated film having a surface layer thickness of 20 ⁇ m, an inner layer thickness of 148 ⁇ m, and a total thickness of 188 ⁇ m.
  • the heat forming flow is shown in FIG.
  • the mold has the prism shape shown in FIG. 2, and the uneven surface of the mold (g in FIG. 4) whose temperature is controlled by this film (h in FIG. 4) and the heating / cooling plate (f in FIG. 4).
  • the mold was cooled to 70 ° C., and then the press was released and released from the mold to obtain a resin molded product.
  • Table 1 shows the results of the 85 ° C. luminance retention rate of the obtained molded product.
  • Example 2 A polyester resin was obtained in the same manner as in Example 1 except that the copolymer composition ratio was changed. Table 1 shows the IV, solution haze, and thermal characteristics of the obtained polyester resin.
  • Example 2 A three-layer laminated film was obtained in the same manner as in Example 1 except that this polyester resin was used as a sublayer, and then a heat-forming product was obtained.
  • Table 1 shows the results of the 85 ° C. luminance retention rate of the obtained molded product.
  • Example 3 A polyester resin was obtained in the same manner as in Example 1 except that the copolymer composition ratio was changed. Table 1 shows the IV, solution haze, and thermal characteristics of the obtained folded ester resin.
  • Example 2 A three-layer laminated film was obtained in the same manner as in Example 1 except that this polyester resin was used as a sublayer, and then a heat-forming product was obtained.
  • Table 1 shows the results of the 85 ° C. luminance retention rate of the obtained molded product.
  • Example 4 Lithium acetate dihydrate was removed from the added catalyst after melting the monomer, and 5 parts by weight of sodium montanate (Licomont NaV101 manufactured by Clariant Japan Co., Ltd.) was added 5 minutes after addition of the ethylene glycol solution of the catalyst deactivator triethylphosphonoacetate.
  • a polyester resin was obtained in the same manner as in Example 1 except that was added. Table 1 shows the IV, solution haze, and thermal characteristics of the obtained polyester resin.
  • Example 2 A three-layer laminated film was obtained in the same manner as in Example 1 except that this polyester resin was used as a sublayer, and then a heat-forming product was obtained.
  • Table 1 shows the results of the 85 ° C. luminance retention rate of the obtained molded product.
  • Example 5 A polyester chip of IV0.53 was obtained in the same manner as in Example 4 except that the amount of diantimony trioxide was changed to 0.1 parts by weight for solid-phase polymerization and the ultimate stirring torque at the end of the polycondensation reaction was lowered. .
  • the obtained chip was vacuum-dried at 150 ° C. for 4 hours, and then subjected to solid-phase polymerization at 210 ° C. for 4 hours under a vacuum of 133 Pa or less to obtain a polyester resin having an IV of 0.72.
  • Table 1 shows the IV, solution haze, and thermal characteristics of the obtained polyester resin.
  • Example 2 A three-layer laminated film was obtained in the same manner as in Example 1 except that this polyester resin was used as a sublayer, and then a heat-forming product was obtained.
  • Table 1 shows the results of the 85 ° C. luminance retention rate of the obtained molded product.
  • Example 6 Example 1 was repeated except that lithium acetate dihydrate was removed from the added catalyst after melting the monomer, and 0.3 parts by weight of sodium acetate was added 5 minutes after addition of the ethylene glycol solution of the catalyst deactivator triethylphosphonoacetate. To obtain a polyester resin. Table 1 shows the IV, solution haze, and thermal characteristics of the obtained polyester resin.
  • Example 2 A three-layer laminated film was obtained in the same manner as in Example 1 except that this polyester resin was used as a sublayer, and then a heat-forming product was obtained.
  • Table 1 shows the results of the 85 ° C. luminance retention rate of the obtained molded product.
  • Example 7 A polyester resin was obtained in the same manner as in Example 6 except that the amount of sodium acetate added was changed to 0.02 parts by weight. Table 1 shows the IV, solution haze, and thermal characteristics of the obtained polyester resin.
  • Example 2 A three-layer laminated film was obtained in the same manner as in Example 1 except that this polyester resin was used as a sublayer, and then a heat-forming product was obtained.
  • Table 1 shows the results of the 85 ° C. luminance retention rate of the obtained molded product.
  • Example 8 A polyester resin was obtained in the same manner as in Example 6 except that the amount of sodium acetate added was changed to 0.5 parts by weight. Table 1 shows the IV, solution haze, and thermal characteristics of the obtained polyester resin.
  • Example 2 A three-layer laminated film was obtained in the same manner as in Example 1 except that this polyester resin was used as a sublayer, and then a heat-forming product was obtained.
  • Table 1 shows the results of the 85 ° C. luminance retention rate of the obtained molded product.
  • the solution haze of the resin was high and the initial luminance was 5% lower than that of Example 1, but there was no problem with the prism sheet characteristics.
  • Example 9 30 parts by weight of talc (SG-95, nominal particle size: 2.8 ⁇ m) manufactured by Nippon Talc Co., Ltd., together with 300 parts by volume of ethylene glycol and 300 parts by volume of glass beads (average particle size: 50 ⁇ m), 5 at 3000 rpm using a jet agitator. The mixture was stirred at high speed for a period of time, and the glass beads were removed with a membrane filter to obtain a talc ethylene glycol slurry (average particle size 0.8 ⁇ m).
  • Example 2 A three-layer laminated film was obtained in the same manner as in Example 1 except that this polyester resin was used as a sublayer, and then a heat-forming product was obtained.
  • Table 1 shows the results of the 85 ° C. luminance retention rate of the obtained molded product.
  • Example 10 30 parts by weight of talc (SG-95, nominal particle size: 2.8 ⁇ m) manufactured by Nippon Talc Co., Ltd., together with 300 parts by volume of ethylene glycol and 300 parts by volume of glass beads (average particle size: 50 ⁇ m), are mixed at 3000 rpm with a jet agitator. The mixture was stirred at high speed for a period of time, and the glass beads were removed with a membrane filter to obtain talc ethylene glycol slurry (average particle size 1.1 ⁇ m).
  • a polyester resin was obtained in the same manner as in Example 9 except that the talc EG slurry to be added was changed to this slurry.
  • Table 1 shows the IV, solution haze, and thermal characteristics of the obtained polyester resin.
  • Example 2 A three-layer laminated film was obtained in the same manner as in Example 1 except that this polyester resin was used as a sublayer, and then a heat-forming product was obtained.
  • Table 1 shows the results of the 85 ° C. luminance retention rate of the obtained molded product.
  • Example 11 30 parts by weight of talc (SG-95, nominal particle size: 2.8 ⁇ m) manufactured by Nippon Talc Co., Ltd., together with 300 parts by volume of ethylene glycol and 300 parts by volume of zirconia beads (average particle size: 300 ⁇ m), 6 000 rpm with a jet agitator. The mixture was stirred at high speed for a period of time, and the glass beads were removed with a membrane filter to obtain a talc ethylene glycol slurry (average particle size 0.4 ⁇ m).
  • a polyester resin was obtained in the same manner as in Example 9 except that the talc EG slurry to be added was changed to this slurry and the addition amount was changed.
  • Table 1 shows the IV, solution haze, and thermal characteristics of the obtained polyester resin.
  • Example 2 A three-layer laminated film was obtained in the same manner as in Example 1 except that this polyester resin was used as a sublayer, and then a heat-forming product was obtained.
  • Table 1 shows the results of the 85 ° C. luminance retention rate of the obtained molded product.
  • Example 12 30 parts by weight of talc (SG-95, nominal particle size 2.8 ⁇ m) manufactured by Nippon Talc Co., Ltd., together with 300 parts by volume of ethylene glycol and 300 parts by volume of glass beads (average particle size 50 ⁇ m), 1 at 1000 rpm with a jet agitator The mixture was stirred at high speed for a period of time, and the glass beads were removed with a membrane filter to obtain a talc EG slurry (average particle size: 2.0 ⁇ m).
  • talc SG-95, nominal particle size 2.8 ⁇ m
  • a polyester resin was obtained in the same manner as in Example 9 except that the talc EG slurry to be added was changed to this slurry and the addition amount was changed.
  • Table 1 shows the IV, solution haze, and thermal characteristics of the obtained polyester resin.
  • Example 2 A three-layer laminated film was obtained in the same manner as in Example 1 except that this polyester resin was used as a sublayer, and then a heat-forming product was obtained.
  • Table 1 shows the results of the 85 ° C. luminance retention rate of the obtained molded product.
  • Example 13 10 parts by weight of alumina particles having an average particle size of 0.07 ⁇ m and 90 parts by weight of ethylene glycol were stirred with a dissolver at room temperature for 2 hours to obtain an ethylene glycol slurry of alumina particles.
  • the charged monomers were weighed at a ratio of 87.8 parts by weight of dimethyl terephthalate, 16.5 parts by weight of spiroglycol, and 56.1 parts by weight of ethylene glycol (2 moles of the dicarboxylic component), and charged into the transesterification reactor. After melting the product at 150 ° C., 0.06 part by weight of manganese acetate tetrahydrate as a catalyst and 0.002 part by weight of titanium catalyst prepared in Reference Example were added and stirred.
  • the temperature was raised to 190 ° C. over 60 minutes, further raised to 200 ° C. over 60 minutes, and then methanol was distilled while raising the temperature to 240 ° C. over 90 minutes.
  • an ethylene glycol solution containing 0.04 part by weight of trimethyl phosphoric acid as a catalyst deactivator was added and stirred for 5 minutes to stop the transesterification reaction.
  • alumina particles was added to an alumina EG slurry containing 0.3 part by weight.
  • a polymerization reaction was carried out in the same manner as in Example 1 to obtain a polyester resin.
  • Table 1 shows the IV, solution haze, and thermal characteristics of the obtained polyester resin.
  • Example 2 A three-layer laminated film was obtained in the same manner as in Example 1 except that this polyester resin was used as a sublayer, and then a heat-forming product was obtained.
  • Table 1 shows the results of the 85 ° C. luminance retention rate of the obtained molded product.
  • Example 14 A polyester resin was obtained in the same manner as in Example 13 except that the copolymer composition was changed and the alumina slurry was not added. Table 1 shows the IV, solution haze, and thermal characteristics of the obtained polyester resin.
  • Example 2 A three-layer laminated film was obtained in the same manner as in Example 1 except that this polyester resin was used as a sublayer, and then a heat-forming product was obtained.
  • Table 1 shows the results of the 85 ° C. luminance retention rate of the obtained molded product.
  • Example 15 A polyester resin was obtained in the same manner as in Example 9 except that the copolymer composition ratio was changed. Table 1 shows the IV, solution haze, and thermal characteristics of the obtained polyester resin.
  • Example 2 A three-layer laminated film was obtained in the same manner as in Example 1 except that this polyester resin was used as a sublayer, and then a heat-forming product was obtained.
  • Table 1 shows the results of the 85 ° C. luminance retention rate of the obtained molded product.
  • Example 16 A polyester resin was obtained in the same manner as in Example 9 except that the copolymer composition ratio was changed. Table 1 shows the IV, solution haze, and thermal characteristics of the obtained polyester resin.
  • Example 2 A three-layer laminated film was obtained in the same manner as in Example 1 except that this polyester resin was used as a sublayer, and then a heat-forming product was obtained.
  • Table 1 shows the results of the 85 ° C. luminance retention rate of the obtained molded product.
  • Example 17 The charged monomers were 89.1 parts by weight of dimethyl terephthalate, 2.0 parts by weight of dimethyl isophthalate, 10.0 parts by weight of dimethyl 2,6-naphthalenedicarboxylate, 63.2 parts by weight of ethylene glycol (2 mols of the dicarboxylic acid component). Were mixed in a transesterification apparatus, and the contents were melted at 150 ° C. Then, 0.06 parts by weight of manganese acetate tetrahydrate and 0.02 parts by weight of antimony trioxide were added as a catalyst and stirred. did.
  • the temperature was raised to 190 ° C. over 60 minutes, further raised to 200 ° C. over 60 minutes, and then methanol was distilled while raising the temperature to 240 ° C. over 90 minutes.
  • methanol was distilled while raising the temperature to 240 ° C. over 90 minutes.
  • an ethylene glycol solution containing 0.04 part by weight of triethylphosphonoacetate was added as a catalyst deactivator, and after stirring for 5 minutes, 0.02 part by weight of sodium acetate was added for 5 minutes.
  • the transesterification reaction was stopped by stirring.
  • Example 1 Thereafter, a polymerization reaction was carried out in the same manner as in Example 1 to obtain a polyester resin.
  • Table 1 shows the IV, solution haze, and thermal characteristics of the obtained polyester resin.
  • Example 2 A three-layer laminated film was obtained in the same manner as in Example 1 except that this polyester resin was used as a sublayer, and then a heat-forming product was obtained.
  • Table 1 shows the results of the 85 ° C. luminance retention rate of the obtained molded product.
  • Example 18 A polyester resin was obtained in the same manner as in Example 2 except that the polymerization target torque was changed for the purpose of changing IV.
  • Table 1 shows the IV, solution haze, and thermal characteristics of the obtained polyester resin.
  • Example 2 A three-layer laminated film was obtained in the same manner as in Example 1 except that this polyester resin was used as a sublayer, and then a heat-forming product was obtained.
  • Table 1 shows the results of the 85 ° C. luminance retention rate of the obtained molded product.
  • Comparative Example 1 A polyester resin was obtained in the same manner as in Example 1 except that the copolymer composition ratio was changed and the press temperature was 115 ° C. Table 1 shows the IV, solution haze, and thermal characteristics of the obtained polyester resin.
  • Example 2 A three-layer laminated film was obtained in the same manner as in Example 1 except that this polyester resin was used as a sublayer, and then a heat-forming product was obtained.
  • Table 1 shows the results of the 85 ° C. luminance retention rate of the obtained molded product.
  • the Tm of the resin was high and the heat-forming formability was poor due to insufficient heat treatment.
  • Comparative Example 2 A three-layer laminated film was obtained in the same manner as in Example 1 except that a PET / N copolymer (NOPLA KE831) manufactured by Kolon Co., Ltd. was used as a sublayer as a resin, followed by heat shaping. Since the IV of the resin was too high, the heat formability was poor.
  • a PET / N copolymer NOPLA KE831 manufactured by Kolon Co., Ltd.
  • Comparative Example 3 A polyester resin was obtained in the same manner as in Example 1 except that the amount of diantimony trioxide added was changed and solid phase polymerization was carried out after chipping for the purpose of increasing IV. Table 1 shows the IV, solution haze, and thermal characteristics of the obtained polyester resin.
  • a three-layer laminated film was obtained in the same manner as in Example 1 except that this polyester resin was used as a sublayer, and then a heat-forming product was obtained. Since the IV of the resin was too high, the heat formability was poor.
  • Comparative Example 4 A polyester resin was obtained in the same manner as in Example 1 except that the copolymer composition ratio was changed. Table 1 shows the IV, solution haze, and thermal characteristics of the obtained polyester resin.
  • Example 2 A three-layer laminated film was obtained in the same manner as in Example 1 except that this polyester resin was used as a sublayer, and then a heat-forming product was obtained.
  • Table 1 shows the results of the 85 ° C. luminance retention rate of the obtained molded product.
  • the luminance retention was low because the resin was amorphous.
  • Comparative Example 5 A polyester resin was obtained in the same manner as in Example 1 except that the copolymer composition was changed and the press temperature was changed to 110 ° C. Table 1 shows the IV, solution haze, and thermal characteristics of the obtained polyester resin.
  • Example 2 A three-layer laminated film was obtained in the same manner as in Example 1 except that this polyester resin was used as a sublayer, and then a heat-forming product was obtained.
  • Table 1 shows the results of the 85 ° C. luminance retention rate of the obtained molded product.
  • the resin Tg was low and the luminance retention was low.
  • Comparative Example 6 A polyester resin was obtained in the same manner as in Example 6 except that the amount of sodium acetate added was changed. Table 1 shows the IV, solution haze, and thermal characteristics of the obtained polyester resin.
  • Example 2 A three-layer laminated film was obtained in the same manner as in Example 1 except that this polyester resin was used as a sublayer, and then a heat-forming product was obtained.
  • Table 1 shows the results of the 85 ° C. luminance retention rate of the obtained molded product.
  • Comparative Example 7 A polyester resin was obtained in the same manner as in Example 1 except that the copolymer composition was changed. Table 1 shows the IV, solution haze, and thermal characteristics of the obtained polyester resin.
  • Example 2 A three-layer laminated film was obtained in the same manner as in Example 1 except that this polyester resin was used as a sublayer, and then a heat-forming product was obtained.
  • Table 1 shows the results of the 85 ° C. luminance retention rate of the obtained molded product.
  • the resin Tg was low and the luminance retention was low.
  • Example A three-layer laminated film was obtained in the same manner as in Example 1 except that the temperature of the heat treatment zone was 220 ° C., and then a heat-formed product was obtained. Since appropriate film forming conditions were not taken, the obtained molded product had poor moldability.

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  • General Physics & Mathematics (AREA)
  • Optics & Photonics (AREA)
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PCT/JP2009/053141 2008-03-05 2009-02-23 熱賦形光学フィルム用ポリエステル樹脂およびそれを用いた二軸配向ポリエステルフィルム WO2009110337A1 (ja)

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WO2011077742A1 (ja) * 2009-12-25 2011-06-30 三井化学株式会社 偏光性拡散フィルムおよびその製造方法、ならびに偏光性拡散フィルムを含む液晶表示装置
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JP6291448B2 (ja) * 2015-03-31 2018-03-14 富士フイルム株式会社 白色ポリエステルフィルム及びその製造方法、太陽電池用バックシート並びに太陽電池モジュール
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CN110382602B (zh) 2017-03-01 2022-05-27 东洋纺株式会社 具有呋喃二甲酸单元的聚酯膜的制造方法
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