JP2009127024A - Wholly aromatic polyester and polyester resin composition - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide a wholly aromatic polyester easily melt moldable at a low temperature while excellent in heat resistance and having less generation of gas such as phenol. <P>SOLUTION: This wholly aromatic polyester showing optical anisotropy on melting is provided by containing a constituting unit including (I) hydroxynaphthoic acid, (II) terephthalic acid, (III) dihydroxybiphenyl and (IV) naphthalene dicarboxylic acid and/or dihydroxybenzene as an essential constituting component, and also having a 35 to 75 mol% constituting unit (I), a 12.5 to 32.5 mol% constituting unit (II), a 12.5 to 32.5 mol% constituting unit (III) and a 1 to 8 mol% constituting unit (IV) based on the whole constituting units. <P>COPYRIGHT: (C)2009,JPO&INPIT

Description

  The present invention relates to a wholly aromatic polyester that is excellent in heat resistance, can be produced by a normal polymerization apparatus, and is easily melt-molded.

  What is currently marketed as a fully aromatic polyester is based on 4-hydroxybenzoic acid. However, since the homopolymer of 4-hydroxybenzoic acid has a melting point higher than the decomposition point, it is necessary to lower the melting point by copolymerizing various components.

  Fully aromatic polyester using 1,4-phenylenedicarboxylic acid, 1,4-dihydroxybenzene, 4,4'-dihydroxybiphenyl, etc. as a copolymerization component has a high melting point of 350 ° C or higher and is melted in a general-purpose device. Too expensive for processing. In addition, various methods have been tried to lower the melting point of such a high melting point to a temperature that can be processed by a general-purpose melting processing machine. There is a problem that the mechanical strength in the vicinity) cannot be maintained.

  In order to solve this problem, Patent Document 1 proposes a copolyester in which 6-hydroxy-2-naphthoic acid, a diol component, and a dicarboxylic acid component are combined. This polyester has a solidification rate upon cooling. There was a problem that the polymer was easily solidified at the outlet of the polymerization kettle quickly. Patent Document 2 proposes a copolyester in which 6-hydroxy-2-naphthoic acid, 4-hydroxybenzoic acid, a diol component, and a dicarboxylic acid component are combined, but there are difficulties in heat resistance and melt processability. It was.

There is a trade-off between heat resistance and moldability (melt processability). Higher heat resistant polymers require higher molding processing temperatures, so the degradation of the polymer during molding is severe and the molded product swells due to polymer decomposition gas. There are problems such as (blister deformation), deterioration of the hue of the molded product (generation of striped pattern), and easy corrosion due to the gas components generated by the molding machine, and it is difficult to have both heat resistance and moldability well.
In order to solve this problem, the present inventors have proposed a wholly aromatic polyester having a specific structure into which a small amount of 4-hydroxybenzoic acid is introduced (Patent Document 3). However, since 4-hydroxybenzoic acid causes generation of phenol gas, there has been a demand for wholly aromatic polyesters that do not contain 4-hydroxybenzoic acid and have both good properties of heat resistance and moldability.
JP-A-56-10526 Japanese Patent Laid-Open No. 55-144024 JP 2002-179776 A

  An object of the present invention is to provide a wholly aromatic polyester that solves the above-described problems and that is excellent in heat resistance but is easy to be melt-molded at a low temperature and generates less gas such as phenol.

  As a result of intensive studies to achieve the above object, the present inventors have found that in a polymer composed of a 6-hydroxy-2-naphthoic acid unit, a diol component unit, and a dicarboxylic acid component unit, 6-hydroxy-2-naphthoic acid and It has been found that combining specific aromatic dicarboxylic acid units and / or aromatic diol units in a specific limited ratio is effective for achieving the above object, and the present invention has been completed.

  That is, the present invention includes structural units represented by the following general formulas (I), (II), (III), and (IV) as essential structural components, and the structural unit of (I) is included in all structural units. 35 to 75 mol%, the structural unit (II) is 12.5 to 32.5 mol%, the structural unit (III) is 12.5 to 32.5 mol%, and the structural unit (IV) is 1 to 8 mol%. It is a wholly aromatic polyester that exhibits optical anisotropy when melted.

  The wholly aromatic polyester having anisotropy at the time of melting comprising the specific structural unit obtained in the present invention and the composition thereof have good fluidity at the time of melting and excellent thermal stability, and have a moldable temperature. Since it is not so high, injection molding, extrusion molding and compression molding are possible without using a molding machine having a special structure, and it can be processed into various three-dimensional molded products, fibers, films and the like. In particular, it is suitable for molded products such as relay switch parts, bobbins, actuators, noise reduction filter cases, and heat fixing rolls of OA equipment.

  In order to embody the structural units (I) to (IV), various compounds having ordinary ester forming ability are used. Hereinafter, the raw material compounds necessary for forming the wholly aromatic polyester constituting the present invention will be described in detail step by step.

  The structural unit (I) is introduced from 6-hydroxy-2-naphthoic acid.

  The structural unit (II) is a dicarboxylic acid unit and is introduced from terephthalic acid.

  The structural unit (III) is a diol unit and is introduced from 4,4′-dihydroxybiphenyl.

  The structural unit (IV) is a structural unit introduced from resorcinol and / or naphthalenedicarboxylic acid (preferably 2,6-naphthalenedicarboxylic acid), and is introduced from a substituted product or derivative thereof. May be. The structural unit (IV) may be introduced from either resorcinol or 2,6-naphthalenedicarboxylic acid, or may be introduced from both.

In the present invention, the structural units (I) to (IV) are contained, and the structural unit (I) is 35 to 75 mol% (preferably 40 to 70 mol%, more preferably 45 to 65 mol%) with respect to all the structural units. Mol%) and (II) are 12.5 to 32.5 mol% (preferably 15 to 30 mol%, more preferably 17.5 to 27.5 mol%), and (III) is 12.5 to 32.5 mol% (preferably 15 to 30 mol%, more preferably 17.5 to 27.5 mol%), and the constituent unit of (IV) is in the range of 1 to 8 mol% (preferably 2 to 6 mol%, more preferably 2 to 5 mol%). It is necessary.
When the constituent unit of (I) is less than 35 mol%, the melting point is remarkably high, and in some cases, the polymer is solidified in the reactor at the time of production, which makes it impossible to produce a polymer having a desired molecular weight. On the other hand, if it exceeds 75 mol%, the heat resistance of the polymer with respect to the molding processing temperature is lowered, which is not preferable.
If the structural unit of (II) is less than 12.5 mol%, the heat resistance of the polymer with respect to the molding temperature is lowered, which is not preferable. On the other hand, if it exceeds 32.5 mol%, the melting point becomes remarkably high. In some cases, the polymer is solidified in the reactor at the time of production, which makes it impossible to produce a polymer having a desired molecular weight.
If the structural unit of (III) is less than 12.5 mol%, the heat resistance of the polymer with respect to the molding processing temperature is lowered, which is not preferable. On the other hand, if it exceeds 32.5 mol%, the melting point becomes remarkably high. In some cases, the polymer is solidified in the reactor at the time of production, which makes it impossible to produce a polymer having a desired molecular weight.
On the other hand, if the constituent unit of (IV) is less than 1 mol%, the solidification rate at the time of cooling the polymer is increased, the polymer is easily solidified at the outlet of the reactor, and the polymer discharge becomes unstable. Moreover, since it will become low in the heat resistance of the polymer with respect to a shaping | molding process temperature when it exceeds 8 mol%, it is unpreferable.

In addition, a small amount of other known structural units can be introduced into the wholly aromatic polyester of the present invention as long as the object of the present invention is not impaired. However, constitutional units space flexibility is introduced from a high compound SP ³ carbon is present, such as bisphenol A, since the heat resistance of the polymer to the molding processing temperature is lowered, preferably should not introduce.
In particular, it is preferable from the viewpoint of manufacturability to introduce 1 to 6 mol% of the structural unit represented by the following general formula (V) with respect to all the structural units. Here, the structural unit of (V) is preferably used in the sense of complementing the structural unit of (IV) when the structural unit of (IV) is a relatively small amount (1 to 2 mol%). The total of the structural units (V) is desirably 8 mol% or less with respect to all the structural units.

  As described above, JP-A-56-10526 discloses the structural units (I), (II), and (III) in proportions of 10 to 90 mol%, 5 to 45 mol%, and 5 to 45 mol%, respectively. Copolymerized polyesters have been proposed, but this polyester has a problem that the solidification rate at the time of cooling is high and the polymer is easily solidified at the outlet of the polymerization kettle. In the present invention, in order to solve this problem, to slow down the solidification rate during cooling, and to allow the polymer to be discharged from the polymerization vessel, 1 to 8 mol% of the structural unit (IV) is contained, and the structural unit (I ) To (III) were controlled within the above range.

  Further, in the present invention, in order to optimally control the crystallization state of the polymer in order to moderately slow the solidification rate during cooling, to allow the polymer to be discharged from the polymerization vessel, and to improve the heat resistance, By maintaining the ratio of units (I), (II), (III), and (IV) within the above range, all the problems that have been solved so far have been solved, and all of them have excellent heat resistance, manufacturability, and moldability. Aromatic polyester could be obtained.

The wholly aromatic polyester of the present invention is polymerized using a direct polymerization method or a transesterification method, and a melt polymerization method, a solution polymerization method, a slurry polymerization method, a solid phase polymerization method or the like is used for the polymerization.
In the present invention, at the time of polymerization, an acylating agent for the polymerization monomer or a monomer having terminal activated as an acid chloride derivative can be used. Examples of the acylating agent include acid anhydrides such as acetic anhydride.
In the polymerization, various catalysts can be used. Typical examples are dialkyl tin oxide, diaryl tin oxide, titanium dioxide, alkoxy titanium silicates, titanium alcoholates, alkali and alkaline earth of carboxylic acid. Metal salts, Lewis acid salts such as BF _{3 and} the like. The amount of catalyst used is generally about 0.001 to 1% by weight, particularly about 0.003 to 0.2% by weight, based on the total weight of the monomers.

  Moreover, when performing solution polymerization or slurry polymerization, as a solvent, liquid paraffin, a high heat resistant synthetic oil, an inert mineral oil, etc. are used.

  The reaction conditions are a reaction temperature of 200 to 380 ° C. and a final ultimate pressure of 0.1 to 760 Torr (that is, 13 to 101,080 Pa). Particularly in the melt reaction, the reaction temperature is 260 to 380 ° C., preferably 300 to 360 ° C., and the final ultimate pressure is 1 to 100 Torr (ie 133 to 13,300 Pa), preferably 1 to 50 Torr (ie 133 to 6,670 Pa).

  In the reaction, all the raw material monomers, the acylating agent and the catalyst can be charged in the same reaction vessel to start the reaction (one-step system), or the hydroxyl groups of the raw material monomers (I), (III) and (IV) are acylated. After acylating with an agent, it can also be reacted with the carboxyl group of (II) (two-stage system).

  The melt polymerization is performed after the inside of the reaction system has reached a predetermined temperature, and the pressure reduction is started to a predetermined pressure reduction degree. After the torque of the stirrer reaches a predetermined value, an inert gas is introduced, and the polymer is discharged from the reaction system through a normal pressure from a reduced pressure state to a predetermined pressure state.

  The polymer produced by the above-described polymerization method can be further increased in molecular weight by solid-phase polymerization which is heated at normal pressure or reduced pressure and in an inert gas. Preferred conditions for the solid state polymerization reaction are a reaction temperature of 230 to 350 ° C., preferably 260 to 330 ° C., and a final ultimate pressure of 10 to 760 Torr (ie, 1,330 to 10,080 Pa).

  The liquid crystalline polymer exhibiting optical anisotropy when melted is an indispensable element in the present invention in order to have both thermal stability and easy processability. The wholly aromatic polyester composed of the structural units (I) to (IV) may not form an anisotropic melt phase depending on the constituent components and the sequence distribution in the polymer, but the polymer according to the present invention is melted. Limited to wholly aromatic polyesters that sometimes exhibit optical anisotropy.

  The property of melt anisotropy can be confirmed by a conventional polarization inspection method using an orthogonal polarizer. More specifically, the melting anisotropy can be confirmed by melting a sample placed on a hot stage manufactured by Linkham using an Olympus polarizing microscope and observing it at a magnification of 150 times in a nitrogen atmosphere. The polymer is optically anisotropic and transmits light when inserted between crossed polarizers. If the sample is optically anisotropic, for example, polarized light is transmitted even in a molten stationary liquid state.

  As an index of processability of the present invention, liquid crystallinity and melting point (liquid crystallinity expression temperature) can be considered. Whether or not it exhibits liquid crystallinity is deeply related to the fluidity at the time of melting, and it is essential that the polyester of the present application exhibits liquid crystallinity in the molten state.

  Since a nematic liquid crystalline polymer causes a significant decrease in viscosity at a melting point or higher, generally exhibiting liquid crystallinity at a melting point or higher is an index of workability. The melting point (liquid crystallinity expression temperature) is preferably as high as possible from the viewpoint of heat resistance, but in consideration of thermal degradation during polymer melt processing, heating capability of the molding machine, etc., it may be 380 ° C. or lower. A good guide.

  In addition, since the melting point is 300 to 380 ° C. and the difference between the melting point and the softening temperature is 55 ° C. or less, softening hardly occurs to a high temperature at a relatively low molding temperature, and both high formability and heat resistance are achieved. A liquid crystalline polymer can be obtained. When the softening temperature is 55 ° C. or more lower than the melting point, satisfactory heat resistance cannot be obtained as compared with the molding temperature.

Furthermore, the melt viscosity at a shear rate of 1000 sec ⁻¹ at a temperature 10 to 40 ° C. higher than the melting point is preferably 1 × 10 ⁵ Pa · s or less. More preferably, it is 5 Pa · s or more and 1 × 10 ² Pa · s or less. These melt viscosities are generally realized by having liquid crystallinity.

  Next, the polyester of the present invention can be blended with various fibrous, powdery, and plate-like inorganic and organic fillers according to the purpose of use.

  Examples of fibrous fillers include glass fibers, asbestos fibers, silica fibers, silica / alumina fibers, alumina fibers, zirconia fibers, boron nitride fibers, silicon nitride fibers, boron fibers, potassium titanate fibers, and silicates such as wollastonite. Examples thereof include inorganic fibrous materials such as fibers, magnesium sulfate fibers, aluminum borate fibers, and metal fibrous materials such as stainless steel, aluminum, titanium, copper, and brass. A particularly typical fibrous filler is glass fiber. High melting point organic fibrous materials such as polyamide, fluororesin, polyester resin, and acrylic resin can also be used.

  On the other hand, as the granular filler, carbon black, graphite, silica, quartz powder, glass beads, milled glass fiber, glass balloon, glass powder, calcium oxalate, aluminum oxalate, kaolin, clay, diatomaceous earth, wollastonite Oxalates such as, iron oxide, titanium oxide, zinc oxide, antimony trioxide, metal oxides such as alumina, metal carbonates such as calcium carbonate and magnesium carbonate, metal sulfates such as calcium sulfate and barium sulfate Other examples include ferrite, silicon carbide, silicon nitride, boron nitride, and various metal powders.

  Examples of the plate-like filler include mica, glass flakes, talc and various metal foils.

  Examples of organic fillers include heat-resistant high-strength synthetic fibers such as aromatic polyester fibers, liquid crystalline polymer fibers, aromatic polyamides, and polyimide fibers.

  These inorganic and organic fillers can be used alone or in combination of two or more. The combined use of the fibrous filler and the granular or plate-like filler is a preferable combination particularly in combination of mechanical strength, dimensional accuracy, electrical properties and the like. The blending amount of the inorganic filler is 120 parts by weight or less, preferably 20 to 80 parts by weight with respect to 100 parts by weight of the wholly aromatic polyester.

  Particularly preferred are fibrous fillers, particularly glass fibers, and the blending amount is 30 to 80 parts by weight with respect to 100 parts by weight of wholly aromatic polyester. Further, the fiber length is preferably 200 μm or more. A composition containing such a glass fiber in the above blending amount is particularly remarkable in improving the heat distortion temperature and mechanical properties.

  In using these fillers, if necessary, a sizing agent or a surface treatment agent can be used.

  Furthermore, other thermoplastic resins may be added to the polyester of the present invention as long as they do not impair the intended purpose of the present invention.

  Examples of the thermoplastic resin used in this case are: Polyolefins such as polyethylene and polypropylene, aromatic polyesters such as polyethylene terephthalate and polybutylene terephthalate, aromatic polyesters such as diols, polyacetals (homo or copolymers), polystyrene , Polyvinyl chloride, polyamide, polycarbonate, ABS, polyphenylene oxide, polyphenylene sulfide, fluororesin and the like. These thermoplastic resins can be used in combination of two or more.

The present invention will be described in more detail with reference to the following examples, but the present invention is not limited thereto. In addition, the method of the physical property measurement in an Example is as follows.
[Melting point]
Measured with a DSC manufactured by TA Instruments.
[Softening temperature]
A 1mm thick disk is molded from the prepared polyester with a hot press, and heated at 10 ° C / min on a hot plate while applying a constant load of 1.82MPa to the molded product. The temperature when 5% of the thickness of the molded product reached 5% was defined as the softening temperature.
[Heat deformation temperature]
The measurement was performed at a measurement pressure of 1.8 MPa according to ISO75 / A.
[Bending strength]
It measured according to ISO178.
[Polymer discharge]
Behavior when the polymer is discharged from the lower part of the polymerization apparatus after the stirring torque of the polymerization apparatus reaches a predetermined value and nitrogen is introduced to form a pressurized state of 0.5 kg / cm ³ from normal pressure to normal pressure Was observed.
[Melt viscosity]
Measurement was performed with a capillograph manufactured by Toyo Seiki using an orifice having an inner diameter of 1 mm and a length of 20 mm under the conditions of the measurement temperature and the shear rate of 1000 sec ⁻¹ shown in Tables 1 and 2.

Example 1
A polymerization vessel equipped with a stirrer, a reflux column, a monomer inlet, a nitrogen inlet, and a pressure reduction / outflow line was charged with the following raw material monomer, metal catalyst, and acylating agent, and nitrogen substitution was started.
(I) 6-hydroxy-2-naphthoic acid 165 g (48 mol%) (HNA)
(II) Terephthalic acid 73g (24mol%) (TA)
(III) 4,4′-dihydroxybiphenyl 88 g (26 mol%) (BP)
(IV) 2,6-Naphthalenedicarboxylic acid 4 g (1 mol%) (NDA)
(V) 3 g (1 mol%) of isophthalic acid (IA)
Potassium acetate catalyst 45mg
Acetic anhydride 194g
After charging the raw materials, the temperature of the reaction system was raised to 140 ° C. and reacted at 140 ° C. for 2 hours. Thereafter, the temperature is further raised to 360 ° C. over 5.5 hours, and then the pressure is reduced to 10 Torr (ie, 1330 Pa) over 20 minutes, and melt polymerization is performed while distilling off acetic acid, excess acetic anhydride, and other low-boiling components. went. After the stirring torque reached a predetermined value, nitrogen was introduced and the pressure was changed from a reduced pressure state to a normal pressure, and the polymer was discharged from the lower part of the polymerization vessel.

  The obtained polymer had a melting point of 352 ° C. and a softening temperature of 315 ° C., and the difference between the melting point and the softening temperature was as small as 37 ° C. The melt viscosity was 13 Pa · s.

Examples 2-11
A polymer was obtained in the same manner as in Example 1 except that the type and amount of raw material monomer were as shown in Table 1. These results are shown in Table 1. Abbreviations of raw material monomers used are as follows.
RES: Resorcinol Bis-A: Bisphenol A
HBA: 4-hydroxybenzoic acid

Example 12
A polymerization vessel equipped with a stirrer, a reflux column, a monomer inlet, a nitrogen inlet, and a pressure reduction / outflow line was charged with the following raw material monomer, metal catalyst, and acylating agent, and nitrogen substitution was started.
(I) 6-hydroxy-2-naphthoic acid 1273 g (50 mol%) (HNA)
(II) terephthalic acid 562g (25mol%) (TA)
(III) 4,4'-dihydroxybiphenyl 579 g (23 mol%) (BP)
(IV) Resorcinol 30 g (2 mol%) (RES)
Potassium acetate catalyst 330mg
Acetic anhydride 1436g
After charging the raw materials, the temperature of the reaction system was raised to 140 ° C. and reacted at 140 ° C. for 2 hours. Thereafter, the temperature is further raised to 360 ° C. over 5.5 hours, and then the pressure is reduced to 5 Torr (ie, 667 Pa) over 40 minutes, and melt polymerization is performed while distilling off acetic acid, excess acetic anhydride, and other low-boiling components. went. After the stirring torque reached a predetermined value, nitrogen was introduced to change from a reduced pressure state to a normal pressure through a normal pressure, the polymer was discharged from the lower part of the polymerization vessel, and the strand was pelletized to pelletize.

  The obtained pellets were heat-treated at 300 ° C. for 6 hours under a nitrogen stream. The pellet had a melting point of 347 ° C and a softening temperature of 327 ° C, and the difference between the melting point and the softening temperature was as small as 20 ° C. The melt viscosity was 29 Pa · s.

  Further, 53.8 parts by weight of glass fiber (GL-P manufactured by Nippon Electric Glass Co., Ltd.) was blended and kneaded by a twin screw extruder with respect to 100 parts by weight of the pellets to obtain a pellet-shaped wholly aromatic polyester composition. When this wholly aromatic polyester composition was dried at 140 ° C. for 3 hours and then injection molded at a cylinder temperature of 380 ° C. using an injection molding machine, the moldability was good. The obtained test piece had a heat distortion temperature of 327 ° C. and a bending strength of 243 MPa, and showed good heat resistance.

Examples 13-14
A polymer was obtained in the same manner as in Example 12 except that the type and amount of raw material monomer were as shown in Table 1. These results are shown in Table 1.
Moreover, when the wholly aromatic polyester composition was prepared and injection-molded in the same manner as in Example 12, the moldability was good. The obtained test piece (Example 13) had a heat deformation temperature of 330 ° C. and a bending strength of 214 MPa, and the test piece (Example 14) had a heat deformation temperature of 314 ° C. and a bending strength of 243 MPa. It showed heat resistance.

Comparative Examples 1-9
A polymer was obtained in the same manner as in Example 1 except that the type and amount of raw material monomers were as shown in Table 2. These results are shown in Table 2. In Comparative Examples 1 and 2, the polymer was easily solidified at the outlet of the reactor, and it was difficult to discharge the polymer. Moreover, about the comparative example 3, the polymer solidified in the reactor at the time of manufacture, and the polymer of desired molecular weight was not able to be manufactured.

Claims (12)

Including the structural units represented by the following general formulas (I), (II), (III), and (IV) as essential structural components, the structural unit of (I) is 35 to 75 mol% with respect to all the structural units. The structural unit of (II) is 12.5 to 32.5 mol%, the structural unit of (III) is 12.5 to 32.5 mol%, and the structural unit of (IV) is 1 to 8 mol%. A wholly aromatic polyester exhibiting anisotropy.

Further, the structural unit represented by the following general formula (V) is contained in an amount of 1 to 6 mol% based on the total structural units, and the total of the structural units (IV) and (V) is based on the total structural units. The wholly aromatic polyester according to claim 1, which is 8 mol% or less.

The constituent unit of (I) is 40 to 70 mol%, the constituent unit of (II) is 15 to 30 mol%, the constituent unit of (III) is 15 to 30 mol%, and the constituent of (IV) is based on all constituent units The wholly aromatic polyester according to claim 1, wherein the unit is 2 to 6 mol%. 45 to 65 mol% of the structural unit of (I), 17.5 to 27.5 mol% of the structural unit of (II), 17.5 to 27.5 mol% of the structural unit of (III), and (IV) The wholly aromatic polyester according to claim 1, wherein the unit is 2 to 5 mol%. The wholly aromatic polyester according to any one of claims 1 to 4, wherein the melt viscosity at a shear rate of 1000 sec ^-1 is 1 x 10 ⁵ Pa · s or less at a temperature 10 to 40 ° C higher than the melting point of the wholly aromatic polyester. . The wholly aromatic polyester according to any one of claims 1 to 5, wherein the melting point is 300 to 380 ° C, and the difference between the melting point and the softening temperature is 55 ° C or less. A polyester resin composition comprising 120 parts by weight or less of an inorganic or organic filler based on 100 parts by weight of the wholly aromatic polyester according to claim 1. The polyester resin composition according to claim 7, wherein the inorganic filler is a fibrous filler, and the blending amount thereof is 30 to 80 parts by weight with respect to 100 parts by weight of the wholly aromatic polyester. A polyester molded article obtained by molding the wholly aromatic polyester according to any one of claims 1 to 6 or the polyester resin composition according to claim 7 or 8. The polyester molded product according to claim 9, wherein the molded product is a relay switch part, a bobbin, an actuator, a noise reduction filter case, or a heat fixing roll of OA equipment. The polyester molded article according to claim 9, wherein the molded article is a polyester fiber. The polyester molded article according to claim 9, wherein the molded article is a polyester film.