Resin composition and molded article using the same

Abstract

To provide a resin composition which is excellent in long-term low wear property, exhibits a low friction coefficient in sliding, and is excellent in supply property to a molding machine in injection molding of a pellet of the resin composition, and a molded body using the same.SOLUTION: A resin composition contains, with respect to 100 pts.wt. of (A) a thermoplastic polyester resin or a polyarylene sulfide resin (component A), 4-25 pts.wt. of (B) at least one sliding material (component B) selected from the group consisting of polytetrafluoroethylene, and a polyethylene resin having a viscosity average molecular weight of 100,000 to 1,000,000, 5-30 pts.wt. of (C) a wholly aromatic polyamide fiber (component C), and 0.5-15 pts.wt. of (D) at least one polyamide resin (component D) selected from the group consisting of aliphatic polyamide and semi-aromatic polyamide.SELECTED DRAWING: None

Description

[Technical Field]

[0001] The present invention relates to a resin composition that exhibits excellent long-term low wear properties, a low coefficient of friction during sliding, and excellent feedability of pellets of the resin composition into a molding machine during injection molding, and to a molded article using the same. [Background technology]

[0002] Thermoplastic polyester resins and polyarylene sulfide resins have traditionally been expected to be used in sliding components requiring precision, such as various gears and bearings, due to their excellent low water absorption, which minimizes environmental changes in mechanical properties and dimensional change. Furthermore, they can easily be made slidable by adding lubricating components. For example, JIS K7218 Method A describes a method for evaluating the slidability of plastic materials, which involves determining the amount of wear from the weight loss of a test specimen after sliding it for a specified distance under a specified load and speed. However, the sliding distance was 3 km, which is shorter than expected for actual use. Even if low wear is observed initially, the amount of wear and the coefficient of friction may increase as the sliding distance increases. Therefore, to determine whether a material can withstand actual use, it is necessary to conduct tests over longer distances to evaluate its sliding stability.

[0003] Patent Document 1 proposes a resin material with improved long-term wear resistance, which is made of polyarylene sulfide resin, fluororesin, fibrous filler, and inorganic filler, and Patent Document 2 proposes a bearing with excellent long-term wear resistance, which is made of polyarylene sulfide resin, polytetrafluoroethylene, aramid fiber, and flake graphite. However, the specific wear rate of these materials is 10 -6 mm 3 / N·m order, and further reduction in wear is necessary to meet the current need for longer life. Patent Document 3 proposes a low-wear chain sliding member made of thermoplastic resin, fibrous filler, and solid lubricant, but the specific wear amount is 10 -7 mm 3 / N·m order from late 10 -6 mm 3 / N·m order, and the friction coefficient is high, so further improvement is necessary.

[0004] Furthermore, pellets of a resin composition containing aramid fibers may have a problem in that the aramid fibers on the surface interfere with each other, and the pellets remain piled up in the hopper of the injection molding machine and are not fed. Patent Document 4 proposes a material that improves the feedability of pellets made of a polyarylene sulfide resin, a fluororesin, an aramid fiber, and an epoxy compound, but does not describe sliding properties. [Prior art documents] [Patent documents]

[0005] [Patent Document 1] Japanese Patent Publication No. 2021-134243 [Patent Document 2] Japanese Patent Application Laid-Open No. 2007-25434 [Patent Document 3] Japanese Patent Application Laid-Open No. 2015-124056 [Patent Document 4] Japanese Patent Application Publication No. 2020-41019 Summary of the Invention [Problem to be solved by the invention]

[0006] An object of the present invention is to provide a resin composition that exhibits excellent long-term low wear properties, a low coefficient of friction during sliding, and excellent feedability of pellets of the resin composition to a molding machine during injection molding, and to provide a molded article using the same. [Means for solving the problem]

[0007] As a result of extensive research into solving the above-mentioned problems, the present inventors discovered that the above-mentioned object can be achieved by blending a thermoplastic polyester resin or a polyarylene sulfide resin with at least one sliding material selected from the group consisting of polytetrafluoroethylene and a specific polyethylene resin, a wholly aromatic polyamide fiber, and a specific polyamide resin in specific proportions, and thus arrived at the present invention.

[0008] That is, the above problem is achieved by a resin composition characterized by containing, per 100 parts by weight of (A) a thermoplastic polyester resin or a polyarylene sulfide resin (component A), 4 to 25 parts by weight of (B) at least one sliding material (component B) selected from the group consisting of polytetrafluoroethylene and a polyethylene resin having a viscosity-average molecular weight of 100,000 to 1,000,000, 5 to 30 parts by weight of (C) wholly aromatic polyamide fiber (component C), and 0.5 to 15 parts by weight of (D) at least one polyamide resin (component D) selected from the group consisting of aliphatic polyamide and semi-aromatic polyamide.

Advantages of the Invention

[0009] According to the present invention, there are provided a resin composition excellent in long-term low wear property, exhibiting a low coefficient of friction during sliding, and excellent in the supplyability to a molding machine during injection molding of pellets of the resin composition, and a molded body using the same. The molded body obtained from the resin composition of the present invention can be suitably used for sliding members used in, for example, the fields of electric and electronic, semiconductor, automobile, industrial machinery, OA equipment, and architecture.

Modes for Carrying Out the Invention

[0010] Hereinafter, the details of the present invention will be further described.

[0011] <Regarding Component A> The thermoplastic polyester resin as component A of the present invention can be produced using a dicarboxylic acid component mainly composed of a dicarboxylic acid and / or an ester-forming derivative of a dicarboxylic acid, and a glycol component mainly composed of a diol.

[0012] Examples of dicarboxylic acid components include aromatic dicarboxylic acids such as 2,6-naphthalenedicarboxylic acid, 2,7-naphthalenedicarboxylic acid, terephthalic acid, isophthalic acid, 4,4'-diphenyldicarboxylic acid, diphenoxyethane-4,4'-dicarboxylic acid, diphenylsulfone-4,4'-dicarboxylic acid, and diphenylether-4,4'-dicarboxylic acid; aliphatic dicarboxylic acids such as adipic acid, sebacic acid, succinic acid, and oxalic acid; and alicyclic dicarboxylic acids such as cyclohexanedicarboxylic acid. One or more of these may be used, and can be selected arbitrarily depending on the purpose. When two or more dicarboxylic acids are used, the amount of the dicarboxylic acid serving as the main component is preferably 70 mol% or more, more preferably 80 mol% or more, based on the total acid components. Examples of ester-forming derivatives of dicarboxylic acids include lower dialkyl esters of aromatic dicarboxylic acids such as 2,6-naphthalenedicarboxylic acid, 2,7-naphthalenedicarboxylic acid, terephthalic acid, isophthalic acid, 4,4'-diphenyldicarboxylic acid, diphenoxyethane-4,4'-dicarboxylic acid, diphenylsulfone-4,4'-dicarboxylic acid, and diphenylether-4,4'-dicarboxylic acid; lower dialkyl esters of alicyclic dicarboxylic acids such as cyclohexanedicarboxylic acid; and lower dialkyl esters of aliphatic dicarboxylic acids such as adipic acid, sebacic acid, succinic acid, and oxalic acid. One or more of these may be used, and can be selected arbitrarily depending on the purpose. When two or more dicarboxylic acid ester-forming derivatives are used, the amount of the dicarboxylic acid ester-forming derivative that serves as the main component is preferably 70 mol% or more, more preferably 80 mol% or more, based on the total dicarboxylic acid ester-forming derivative components.

[0013] A small amount of a tri- or higher functional dicarboxylic acid component such as trimellitic acid, an acid anhydride such as trimellitic anhydride, or a small amount of a hydroxycarboxylic acid or an alkyl ester thereof such as lactic acid or glycolic acid may also be used, and these can be selected arbitrarily depending on the purpose.

[0014] The glycol component may be, for example, one or more alkylene glycols such as ethylene glycol, 1,4-butanediol, 1,3-propylene glycol, 1,2-propylene glycol, neopentylene glycol, hexamethylene glycol, decamethylene glycol, cyclohexanedimethanol, diethylene glycol, triethylene glycol, poly(oxy)ethylene glycol, poly(oxy)tetramethylene glycol, and poly(oxy)methylene glycol, and can be selected arbitrarily depending on the purpose. A small amount of a polyhydric alcohol component such as glycerin may also be used. The amount of the glycol component that serves as the main component is preferably 70 mol% or more, more preferably 80 mol% or more, based on the total glycol components.

[0015] The amount of the glycol component used is preferably 1.1 to 1.4 times by mole relative to the dicarboxylic acid or ester-forming derivative of the dicarboxylic acid. If the amount of the glycol component used is less than 1.1 times by mole, the esterification or transesterification reaction may not proceed sufficiently, which is not preferred. If the amount of the glycol component used is more than 1.4 times by mole, the reaction rate may slow down, although the reason is unclear, and the excess glycol component may produce a large amount of by-products such as tetrahydrofuran, which is also not preferred.

[0016] In the production of thermoplastic polyester resins, known polymerization catalysts can be used, such as titanium compounds, antimony compounds, germanium compounds, manganese compounds, and aluminum compounds, with titanium compounds being preferred. The titanium compounds used as polymerization catalysts are preferably tetraalkyl titanates, specifically tetra-n-propyl titanate, tetraisopropyl titanate, tetra-n-butyl titanate, tetra-sec-butyl titanate, tetra-t-butyl titanate, tetra-n-hexyl titanate, tetracyclohexyl titanate, tetraphenyl titanate, and tetrabenzyl titanate, and may also be used as mixed titanates. Among these titanium compounds, tetra-n-propyl titanate, tetraisopropyl titanate, and tetra-n-butyl titanate are particularly preferred, with tetra-n-butyl titanate being most preferred. The amount of titanium compound added is preferably 10 ppm to 60 ppm, more preferably 15 ppm to 30 ppm, in terms of the titanium atom content in the resulting thermoplastic polyester resin. A titanium atom content of more than 60 ppm in the resulting thermoplastic polyester resin is undesirable because it may result in a decrease in the color tone and thermal stability of the resin composition of the present invention. On the other hand, a titanium atom content of less than 10 ppm is undesirable because it may not be possible to obtain a thermoplastic polyester resin with a sufficiently high intrinsic viscosity due to poor polymerization activity. The thermoplastic polyester resin of the present invention is preferably produced via an esterification or transesterification reaction step between a dicarboxylic acid component, primarily a dicarboxylic acid and / or its ester-forming derivative, and a glycol component in the presence of a polymerization catalyst, followed by a polycondensation reaction step. The temperature at the end of the esterification or transesterification reaction is preferably in the range of 180°C to 230°C, more preferably 180°C to 220°C. A temperature above 230°C at the end of the esterification or transesterification reaction increases the reaction rate, but may result in an increase in the production of by-products such as tetrahydrofuran, which is undesirable. If the temperature is lower than 180°C, the reaction may not proceed.The reaction product (bisglycol ether and / or its oligomer) obtained by the esterification or transesterification reaction is preferably polycondensed at a temperature of from the melting point of the thermoplastic polyester resin to 290°C under a reduced pressure of 0.4 kPa (3 Torr) or less. A polycondensation reaction temperature exceeding 290°C is undesirable because it may slow down the reaction rate and cause significant coloration.

[0017] One or more thermoplastic polyester resins may be used, and can be selected arbitrarily depending on the purpose. When two or more types are used, the feeding method is not particularly limited. For example, pelletized or powdered thermoplastic polyester resins may be thoroughly mixed in a blender before feeding into an extruder, or each may be fed individually. The use of a thermoplastic polyester resin can improve the long-term low wear and low friction coefficient of a molded article. Typical thermoplastic polyester resins include polybutylene naphthalate, polyethylene naphthalate, polyethylene terephthalate, polybutylene terephthalate, and copolymers thereof. The above-mentioned dicarboxylic acid components and glycol components can be used as copolymerization components. However, polybutylene naphthalate resin, copolymers of polybutylene naphthalate resin, and mixtures of polybutylene naphthalate resin with other thermoplastic polyester resins are particularly preferred, with polybutylene naphthalate resin being even more preferred. The use of these preferred thermoplastic polyester resins may further improve the long-term low wear of a molded article.

[0018] The polyarylene sulfide resin used as component A in the present invention may be any resin that falls within the category known as polyarylene sulfide resin. Use of the polyarylene sulfide resin can improve the long-term low wear properties and low coefficient of friction of the molded article.

[0019] Examples of polyarylene sulfide resins include those composed of constituent units such as p-phenylene sulfide units, m-phenylene sulfide units, o-phenylene sulfide units, phenylene sulfone units, phenylene sulfide ketone units, phenylene sulfide ether units, diphenylene sulfide units, phenylene sulfide units containing a substituent, and phenylene sulfide units containing a branched structure. Of these, those containing 70 mol % or more, particularly 90 mol % or more of p-phenylene sulfide units are preferred, and poly(p-phenylene sulfide) is more preferred.

[0020] The terminal functional groups of the polyarylene sulfide resin are not particularly limited, but a polyarylene sulfide resin composed of 10 to 100% by weight of a polyarylene sulfide resin (component A-1) having at least one functional group selected from the group consisting of a hydroxy group, an amino group, and a carboxy group at its terminal and 0 to 90% by weight of a polyarylene sulfide resin (component A-2) not having the functional group at its terminal is preferred.

[0021] The method for producing a polyarylene sulfide resin is not particularly limited, and polymerization can be performed by a known method, but particularly suitable polymerization methods include those described in U.S. Patent Nos. 4,746,758 and 4,786,713, JP-A-2013-522385, JP-A-2012-233210, and Japanese Patent No. 5167276. These production methods involve directly heating a diiodoaryl compound and solid sulfur without a polar solvent to polymerize them.

[0022] The production method includes an iodization step and a polymerization step. In the iodization step, an aryl compound is reacted with iodine to obtain a diiodoaryl compound. In the subsequent polymerization step, the diiodoaryl compound is polymerized with solid sulfur using a polymerization terminator to produce a polyarylene sulfide resin. Iodine is generated in this step in a gaseous state and recovered for reuse in the iodization step. Iodine essentially serves as a catalyst.

[0023] A typical example of solid sulfur used in the above-mentioned production method is cyclooctasulfur (S8), which has eight atoms bonded together at room temperature. However, the sulfur compound used in the polymerization reaction is not limited, and any form that is solid or liquid at room temperature can be used.

[0024] Representative diiodoaryl compounds used in the production method include at least one selected from the group consisting of diiodobenzene, diiodonaphthalene, diiodobiphenyl, diiodobisphenol, and diiodobenzophenone. Derivatives of iodoaryl compounds, to which alkyl or sulfonic groups are bonded, or to which oxygen or nitrogen is introduced, are also used. Iodoaryl compounds are classified into different isomers depending on the bonding position of the iodine atom. Preferred examples of these isomers are compounds in which the iodines are symmetrically located at both ends of the aryl compound molecule, such as p-diiodobenzene, 2,6-diiodonaphthalene, and p,p'-diiodobiphenyl. The content of the iodoaryl compound is preferably 500 to 10,000 parts by weight per 100 parts by weight of the solid sulfur. This amount is determined taking into account the formation of disulfide bonds.

[0025] Representative polymerization terminators used in the production method include monoiodoaryl compounds, benzothiazoles, benzothiazole sulfenamides, thiurams, dithiocarbamates, and aromatic sulfide compounds. Preferred examples of monoiodoaryl compounds include at least one selected from the group consisting of iodobiphenyl, iodophenol, iodoaniline, and iodobenzophenone. Preferred examples of benzothiazoles include at least one selected from the group consisting of 2-mercaptobenzothiazole and 2,2'-dithiobisbenzothiazole. Preferred examples of benzothiazole sulfenamides include at least one selected from the group consisting of N-cyclohexylbenzothiazole 2-sulfenamide, N,N-dicyclohexyl-2-benzothiazole sulfenamide, 2-morpholinothiobenzothiazole, benzothiazole sulfenamide, dibenzothiazole disulfide, and N-dicyclohexylbenzothiazole 2-sulfenamide. A preferred example of the thiuram is at least one selected from the group consisting of tetramethylthiuram monosulfide and tetramethylthiuram disulfide. A preferred example of the dithiocarbamates is at least one selected from the group consisting of zinc dimethyldithiocarbamate and zinc diethyldithiocarbamate. A preferred example of the aromatic sulfide compound is at least one selected from the group consisting of diphenyl sulfide, diphenyl disulfide, diphenyl ether, biphenyl, and benzophenone. In addition, in any of the polymerization terminators, one or more functional groups may be substituted on the conjugated aromatic ring skeleton. Examples of the functional group include a hydroxy group, a carboxy group, a mercapto group, an amino group, a cyano group, a sulfo group, and a nitro group. Preferred examples include a hydroxy group, an amino group, and a carboxy group. More preferred examples are those having a peak in the FT-IR spectrum of 3200 to 3600 cm. -1 , 1600~1800cm -1 and 3300-3500 cm -1Examples include a hydroxy group, an amino group, and a carboxy group that indicate peaks. The content of the polymerization terminator is preferably 1 to 30 parts by weight with respect to 100 parts by weight of the solid sulfur. This amount is determined in consideration of the formation of disulfide bonds.

[0026] In the above production method, a polymerization reaction catalyst may be used. Representative polymerization reaction catalysts include nitrobenzene-based catalysts. Preferred examples of nitrobenzene-based catalysts include at least one selected from the group consisting of 1,3-diiodo-4-nitrobenzene, 1-iodo-4-nitrobenzene, 2,6-diiodo-4-nitrophenol, iodonitrobenzene, and 2,6-diiodo-4-nitroamine. The content of the polymerization reaction catalyst is preferably 0.01 to 20 parts by weight with respect to 100 parts by weight of the solid sulfur. This amount is determined in consideration of the formation of disulfide bonds.

[0027] By using this polymerization method, it is not necessary to substantially reduce the chlorine content and sodium content, and a polyphenylene sulfide resin excellent in cost performance can be obtained.

[0028] The polyphenylene sulfide resin of the present invention may also contain a polyphenylene sulfide resin obtained by other polymerization methods.

[0029] <Regarding Component B> The present invention includes at least one sliding material selected from the group consisting of polytetrafluoroethylene and a polyethylene resin having a viscosity average molecular weight of 100,000 to 1,000,000 as Component B. By using these sliding materials, the long-term low wear resistance and low friction coefficient of the molded body can be improved.

[0030] The polyethylene resin (Component B) of the present invention can be a known one, including high-density polyethylene, low-density polyethylene, ultra-high-molecular-weight polyethylene, polyethylene obtained by multistage polymerization of ultra-high-molecular-weight polyethylene with high- or low-molecular-weight polyethylene, and modified products thereof. One or more of these may be mixed and used. Various known methods can be used to modify the polyethylene, including a method in which air is introduced into the polyethylene in a molten state at 140 to 180°C to introduce functional groups through an oxidation reaction; a method in which the polyethylene is suspended or dissolved in a solvent, and then a modifying monomer and a radical polymerization initiator are added and mixed at a temperature of typically 80 to 200°C to perform graft copolymerization; and a method in which the modifying monomer is brought into contact with a radical polymerization initiator while melt-kneading at a temperature above the melting point, for example, 180 to 300°C. Examples of modifying monomers include acrylic acid, methacrylic acid, maleic acid, fumaric acid, itaconic acid, citraconic acid, crotonic acid, and nadic acid (endo-cis-bicyclo[2.2]hept-5-ene-2,3-dicarboxylic acid). Derivatives thereof include acid halides, esters, amides, imides, and anhydrides, such as malenyl chloride, maleimide, acrylic acid amide, methacrylic acid amide, glycidyl methacrylate, maleic anhydride, citraconic anhydride, monomethyl maleate, dimethyl maleate, and glycidyl maleate. When a thermoplastic polyester resin is used as component A, a modified polyethylene resin modified with at least one compound selected from the group consisting of maleic acid and maleic anhydride is preferred, and a modified polyethylene resin modified with maleic anhydride is particularly preferred. When a polyarylene sulfide resin is used as component A, a polyethylene resin without a polar group is preferred. Use of these preferred polyethylene resins may result in improved low wear of the molded article and improved feedability of pellets of the resin composition to a molding machine during injection molding.

[0031] The viscosity-average molecular weight (Mv) of the polyethylene resin is in the range of 100,000 to 1,000,000, preferably 200,000 to 900,000, and more preferably 300,000 to 800,000. If the viscosity-average molecular weight is less than 100,000, the wear amount and friction coefficient increase during long-term sliding, while if it exceeds 1,000,000, the dispersion during extrusion is insufficient, causing component B to separate, resulting in strand breakage and making pelletization difficult. The viscosity-average molecular weight of the polyethylene resin can be calculated from the following general formula (1) using the intrinsic viscosity [η] measured in decaphosphoric acid solvent at 135°C: Mv=5.37×10 4 [η] 1.37 ···(1)

[0032] The polytetrafluoroethylene used as component B of the present invention can be any known polytetrafluoroethylene, and either calcined or uncalcined polytetrafluoroethylene can be used. However, since polytetrafluoroethylene is prone to reagglomeration, powdered polytetrafluoroethylene that has been subjected to calcination or other treatment to prevent reagglomeration is preferred, and polytetrafluoroethylene calcined at a calcination temperature of 360°C or higher is particularly preferred. The melting point of polytetrafluoroethylene, as measured by DSC, is preferably 320 to 335°C, more preferably 325 to 335°C, to prevent reagglomeration. The average particle size of polytetrafluoroethylene, as measured by a light transmission method using a dispersion of polytetrafluoroethylene dispersed in perchloroethylene, is preferably 0.1 μm to 100 μm, more preferably 1 μm to 40 μm, and even more preferably 1 μm to 20 μm. The average particle size referred to here is the weight-average particle size measured using a laser diffraction / scattering method (MICOTRAC). The number-average molecular weight of this polytetrafluoroethylene is preferably 100,000 or more, more preferably 200,000 or more. Examples of such polytetrafluoroethylene are commercially available from Kitamura Co., Ltd. as KTL-620, KTL-450A, KT-600M, and KT-400M, and are readily available.

[0033] The content of Component B is 4 to 25 parts by weight, preferably 7 to 22 parts by weight, more preferably 10 to 20 parts by weight with respect to 100 parts by weight of Component A. When the content is less than 4 parts by weight, the wear amount and the friction coefficient during long-term sliding increase. When it exceeds 25 parts by weight, the wear amount during long-term sliding increases and the supplyability to the molding machine during injection molding of the resin composition pellets is impaired, making continuous molding difficult.

[0034] <Regarding Component C> As the wholly aromatic polyamide fiber used as Component C of the present invention, any fiber belonging to the category called wholly aromatic aramid fiber may be used. By using the wholly aromatic polyamide fiber, excellent low wear properties can be exhibited. Examples of the wholly aromatic aramid fiber include meta-aramid fiber, para-aramid fiber, etc., and among them, para-aramid fiber is preferable.

[0035] The wholly aromatic polyamide constituting the fiber of the present invention is substantially obtained by one or more aromatic diamines and one or more aromatic dicarboxylic acid halides. However, a condensing agent represented by a system such as triphenyl phosphite and pyridine can also be added to one or more aromatic diamines and one or more aromatic dicarboxylic acids. The wholly aromatic polyamide may be para-type or meta-type, but para-type is more preferable. Preferable aromatic diamines include p-phenylenediamine, benzidine, 4,4”-diamino-p-terphenyl, 2,7-diaminofluorene, 3,4-diaminodiphenyl ether, 4,4´-diaminodiphenyl ether, 1,4-bis-(4-aminophenoxy)benzene, 4,4´-bis-(4-aminophenoxy)biphenyl, 9,10-bis-(4-aminophenyl)anthracene, etc. Acid chloride is particularly preferable as the aromatic dicarboxylic acid halide, and examples include terephthalic acid chloride, 2,6-naphthalenedicarboxylic acid chloride, 4,4´-diphenyldicarboxylic acid chloride, and those containing one or more non-reactive functional groups such as a lower alkyl group, lower alkoxy group, halogeno group, nitro group, etc. on its aromatic ring. Furthermore, when an aromatic dicarboxylic acid is used, examples thereof include terephthalic acid, 2,6-naphthalenedicarboxylic acid, 4,4'-diphenyldicarboxylic acid, and those containing one or more non-reactive functional groups on the aromatic ring, such as lower alkyl groups, lower alkoxy groups, halogeno groups, nitro groups, etc. Furthermore, the structure of a wholly aromatic polyamide preferred in the present invention is one whose main skeleton is represented by the following formula:

[0036] [ka]

[0037] (Here, Ar1 and Ar2 represent at least one aromatic residue selected from the group consisting of the following general formulas [I] to [IV]. Ar1 and Ar2 may be the same or different. In addition, some of the hydrogen atoms of these aromatic residues may be substituted with halogen atoms or lower alkyl groups.)

[0038] [ka]

[0039] In particular, when the sum of Ar1 and Ar2 is taken as 100 mol%, the sum of general formula [I] and general formula [II], the sum of general formula [I] and general formula [III], the sum of general formula [I] and general formula [IV], or general formula [I] is preferably 80 mol% or more. More preferably, the sum of general formula [I] and general formula [II], or the sum of general formula [I] and general formula [III] is 80 mol% or more. Even more preferably, the sum of general formula [I] and general formula [II], or the sum of general formula [I] and general formula [III] is 80 mol% or more, and general formula [II] or general formula [III] is 1 to 20 mol%.

[0040] The aromatic polyamide dope used as the spinning solution may be obtained by solution polymerization or by dissolving a separately obtained wholly aromatic polyamide in a solvent, but solution polymerization is preferred. A small amount of inorganic salt may be added as a solubilizer to improve solubility. Examples of such inorganic salts include lithium chloride and calcium chloride.

[0041] As the polymerization solvent or re-dissolving solvent, a generally known aprotic organic polar solvent is used, examples of which include N-methyl-2-pyrrolidone, N-ethyl-2-pyrrolidone, N,N-dimethylformamide, N,N-dimethylacetamide, N,N-diethylacetamide, N,N-dimethylpropionamide, N,N-butylamide, N,N-dimethylisobutyramide, N-methylcaprolactam, N,N-dimethylmethoxyacetamide, N-acetylpyrrolidine, N-acetylpiperidine, N-methylpiperidone-2,N,N'-dimethylethyleneurea, N,N'-dimethylpropyleneurea, N,N,N',N'-tetramethylmalonamide, N-acetylpyrrolidone, N,N,N',N'-tetramethylurea, and dimethyl sulfoxide. Further, as the re-dissolving solvent, a strong acid such as concentrated sulfuric acid or methanesulfonic acid can be used.

[0042] Although there is no particular limitation on the degree of polymerization of the wholly aromatic polyamide, a higher degree of polymerization is preferable if it dissolves in a solvent. When the wholly aromatic polyamide is solution-polymerized, the acid component and the diamine component are reacted in a substantially equimolar ratio, but either component can be used in excess to control the degree of polymerization. Furthermore, a monofunctional acid component or an amine component can be used as an end-capping agent.

[0043] When forming a wholly aromatic polyamide into a fiber, a method of wet forming a wholly aromatic polyamide dope is usually used, either by directly discharging the dope into a coagulation bath or by discharging the dope into the coagulation bath via an air gap. A poor solvent for the wholly aromatic polyamide is used in the coagulation bath, and a good solvent is usually added to adjust the coagulation rate so that the solvent of the wholly aromatic polyamide dope does not escape too quickly and cause defects in the wholly aromatic polyamide fiber. In general, it is preferable to use water as the poor solvent and the solvent of the wholly aromatic polyamide dope as the good solvent. The ratio of good solvent / poor solvent is preferably 15 / 85 to 40 / 60, depending on the solubility and coagulation properties of the wholly aromatic polyamide.

[0044] Although such wholly aromatic polyamide fibers are effective regardless of whether they are bundled or not, bundled fibers are preferred because they are easier to handle. Examples of binders for bundling include polyester resins, polyurethane resins, and polyethersulfone resins. Among these, polyester resins and polyurethane resins are preferred, and polyester resins are even more preferred. In the present invention, such wholly aromatic polyamide fibers can be used alone or as a mixture of two or more types.

[0045] Furthermore, such wholly aromatic polyamide fibers preferably have an average fiber length of 2 to 6 mm, more preferably 2 to 5 mm, before being added to component A. If the average fiber length is less than 2 mm, the reinforcing effect may be insufficient, and the improvement in long-term low abrasion properties may be insufficient. If the average fiber length is more than 6.0 mm, handling during production may be difficult, and the fluidity of the composition may be poor, resulting in poor moldability. The average fiber length can be measured, for example, by taking any single fiber from a fiber bundle, measuring the fiber lengths of 50 fibers under magnification with a microscope, and taking the average of the measured fiber lengths as the fiber length.

[0046] Also, the form of such wholly aromatic polyamide fibers is not particularly limited, and any form can be used, but it is preferably twisted from the viewpoint of handling during the production of the resin composition. By using a fiber bundle with a large number of twists, the supply of the wholly aromatic polyamide fibers to the extruder may be stabilized. The preferred number of twists of the wholly aromatic polyamide fibers is 10 to 500 turns / m, more preferably 50 to 450 turns / m, and even more preferably 100 to 400 turns / m.

[0047] The content of the C component is 5 to 30 parts by weight, preferably 7 to 28 parts by weight, more preferably 9 to 26 parts by weight, and particularly preferably 12 to 24 parts by weight with respect to 100 parts by weight of the A component. When the content of the C component exceeds 30 parts by weight, handling during production becomes difficult, the supplyability to the molding machine during injection molding of the pellets of the resin composition is impaired, and continuous molding becomes difficult. On the other hand, when the content is less than 5 parts by weight, the wear amount during long-term sliding increases.

[0048] <Regarding the D component> The polyamide resin used as component D in the present invention may be any one belonging to the category called aliphatic polyamides and semi-aromatic polyamides, and one kind or a mixture of plural kinds may be used. The aliphatic polyamide contains a dicarboxylic acid component and a diamine component as constituent components and does not contain an aromatic component in the main chain. For example, poly ε-capramide (polyamide 6), polytetramethylene adipamide (polyamide 46), polyhexamethylene adipamide (polyamide 66), polyhexamethylene sebacamide (polyamide 610), polyhexamethylene dodecamide (polyamide 612), polyundecamethylene adipamide (polyamide 116), polyundecanamide (polyamide 11), polydodecanamide (polyamide 12), and polyamide copolymers containing at least two different polyamide components among these are exemplified. The semi-aromatic polyamide contains a dicarboxylic acid component and a diamine component as constituent components, contains an aromatic dicarboxylic acid in the dicarboxylic acid component, and contains an aliphatic diamine in the diamine component. The dicarboxylic acid component preferably contains terephthalic acid (T). Examples of the semi-aromatic polyamide resin include polyamide 8T, polyamide 9T, polyamide 10T, polyamide 11T, and polyamide 12T. Among these polyamide resins, polyamide 6, polyamide 66, polyamide 10T, and mixtures thereof are preferred, and polyamide 6, polyamide 66, and mixtures thereof are particularly preferred, which may further improve long-term low wear properties.

[0049] The content of component D is 0.5 to 15 parts by weight, preferably 0.5 to 12 parts by weight, more preferably 0.5 to 8 parts by weight, and particularly preferably 1 to 5 parts by weight with respect to 100 parts by weight of component A. When the content of component D exceeds 15 parts by weight and is less than 0.5 parts by weight, the wear amount during long-term sliding increases, and the supplyability to the molding machine during injection molding of the pellets of the resin composition is impaired, making continuous molding difficult. When the content is less than 0.5 parts by weight, the friction coefficient during long-term sliding further increases.

[0050] <Regarding component E> The resin composition of the present invention may contain an epoxy resin, which is preferable because it may improve low wear, ease of feeding pellets of the resin composition to a molding machine during injection molding, and mechanical properties.

[0051] Any epoxy resin may be used as long as it has an epoxy group in its molecular structure, but an epoxy resin having two or more epoxy groups per molecule is preferred. When an epoxy resin having two or more epoxy groups per molecule is used, the tensile strength at break may be further improved by the crosslinking reaction of the epoxy resin. Specific examples include bisphenol-type epoxy, novolac-type epoxy, cycloaliphatic-type epoxy, glycidyl ester-type epoxy, glycidylamine-type epoxy, trisphenolmethane-type epoxy, dicyclopentadiene-type epoxy, and biphenyl-type epoxy. Component E may be used alone or in combination with two or more compounds. Examples of such epoxy resins are readily available commercially, including jER154, jER1001, jER1010, jER1256, and YX4000 from Mitsubishi Chemical Corporation, EHPE3150 from Daicel Corporation, and NC-3000, NC-7000, XD-1000, EPPN-502H, and EOCN-104S from Nippon Kayaku Co., Ltd.

[0052] The epoxy equivalent of component E is preferably 100 to 10,000 g / eq, more preferably 125 to 9,500 g / eq, and even more preferably 150 to 9,000 g / eq. If the epoxy equivalent is less than 100 g / eq, thickening is likely to occur during kneading and extrusion, while if it exceeds 10,000 g / eq, the ease of feeding pellets of the resin composition into a molding machine during injection molding may not improve. The epoxy equivalent is measured in accordance with JIS K 7236.

[0053] The content of Component E is preferably 0.5 to 8 parts by weight, and more preferably 1 to 6 parts by weight, per 100 parts by weight of Component A. By including an epoxy resin in the above range, low abrasion properties, ease of feeding pellets of the resin composition to a molding machine during injection molding, and mechanical properties may be improved.

[0054] <Other ingredients> The resin composition of the present invention may contain other thermoplastic resins, and may contain additives such as antioxidants, impact modifiers, plasticizers, organic and inorganic fillers other than component C, flame retardants, colorants, light stabilizers, heat stabilizers, antistatic agents, antiblocking agents, lubricants other than component B, dispersants, flow modifiers, and crystal nucleating agents, as needed, within the scope of the present invention.

[0055] <Method of manufacturing resin composition> Any method can be used to produce the resin composition of the present invention. For example, the components and optionally other components can be premixed, followed by melt-kneading and pelletizing. Examples of premixing methods include a Nauta mixer, a V-blender, a Henschel mixer, a mechanochemical device, and an extrusion mixer. Premixing can also be performed using an extrusion granulator or briquetting machine. After premixing, the components are melt-kneaded in a melt mixer, typically a vented twin-screw extruder, and pelletized using a pelletizer or other device. Other examples of melt mixers include a Banbury mixer, a kneading roll, and a thermostatically stirred vessel. A vented twin-screw extruder is preferred. Alternatively, the components and optionally other components can be fed independently to a melt mixer, typically a twin-screw extruder, without premixing.

[0056] <About the molded body> Molded articles made from the resin composition of the present invention can be obtained by molding pellets produced as described above. Preferably, they are obtained by injection molding or extrusion molding. Injection molding can be performed using not only conventional molding methods but also injection compression molding, injection press molding, gas-assisted injection molding, foam molding (including methods involving the injection of supercritical fluids), insert molding, in-mold coating molding, heat-insulating mold molding, rapid heating and cooling mold molding, two-color molding, multi-color molding, sandwich molding, and ultra-high-speed injection molding. Molding can be performed using either a cold runner system or a hot runner system. In extrusion molding, molded articles can be obtained by extruding a round bar and then cutting it into a disk, or by extruding a thick sheet and then punching it into a desired shape. [Example]

[0057] Hereinafter, the present invention will be described in detail with reference to examples, but the present invention is not limited to these examples. Physical properties were evaluated by the following methods.

[0058] [Evaluation of Resin Composition] (1) Amount of wear The pellets obtained by the method described below were dried at 120°C for 7 hours and then injected into an injection molding machine (Toshiba Machine Co., Ltd., EC130SXII-4Y) at a cylinder temperature of 280-310°C and a mold temperature of 120-140°C to obtain hollow cylindrical test specimens with an outer diameter of 25.6 mm, an inner diameter of 20 mm, and a height of 15 mm according to JIS K7218A. The test specimens were then subjected to friction and wear testing under the same conditions as those of a carbon steel (S45C) at a surface pressure of 0.75 MPa, a sliding speed of 500 mm / s, and sliding distances of 3 km and 43 km using a friction and wear tester (EFM-3-G, Orientec Co., Ltd.). The weight loss of the test specimens after sliding was measured to the nearest 0.1 mg using an electronic balance, and the wear loss was calculated using the formula described in JIS K7218A. The test was performed three times, and the average value was used as the wear loss for the composition. Wear amount after sliding distance of 43km is 6mm 3 The following is required:

[0059] (2) Coefficient of kinetic friction The pellets obtained by the method described below were dried at 120°C for 7 hours and then molded into hollow cylindrical test specimens with an outer diameter of 25.6 mm, an inner diameter of 20 mm, and a height of 15 mm using an injection molding machine (Toshiba Machine Co., Ltd., EC130SXII-4Y) at a cylinder temperature of 280-310°C and a mold temperature of 120-140°C in accordance with JIS K7218A. The dynamic friction coefficient of the test specimen was measured when sliding it against a similarly shaped test specimen made of carbon steel (S45C) in accordance with JIS K7218A. The test was conducted using a friction and wear tester (EFM-3-G, Orientec Co., Ltd.) under conditions of a surface pressure of 0.75 MPa, a sliding speed of 500 mm / s, and a sliding distance of 43 km. The dynamic friction coefficient was measured at 10-second intervals over sliding distances of 0.3 to 43 km, and the average value was used as the dynamic friction coefficient. The dynamic friction coefficient must be less than 0.30.

[0060] (3) Pellets supply When test pieces for the sliding tests described in (1) and (2) were molded using an injection molding machine EC130SXII-4Y manufactured by Toshiba Machine Co., Ltd., the cases where the pellets in the hopper were supplied into the molding machine and continuous molding was possible while molding 10 pieces of test pieces continuously were marked as "○", and the cases where resin could not be supplied into the molding machine due to interference between pellets during molding and continuous molding was difficult were marked as "×".

[0061] [Examples 1-14, Comparative Examples 1-10] According to the amounts shown in Table 1, components A, B, D, and E were separately fed into a twin-screw extruder through the first feed port. Here, the first feed port refers to the feed port at the base. Component C was separately fed through the second feed port using a side feeder. For extrusion, a vented twin-screw extruder with a diameter of 30 mm (TEX30α-31.5BW-2V, manufactured by The Japan Steel Works, Ltd.) was used. The extrusion was performed at a screw rotation speed of 200 rpm, a discharge rate of 20 kg / h, and a vent vacuum of 3 kPa to obtain pellets. The extrusion temperature was 290°C for Examples 1 to 12 and Comparative Examples 1 to 10, and 310°C for Examples 13 and 14.

[0062] (Component A) AI: Polybutylene naphthalate resin obtained in Production Example I <Manufacturing example I> 315.0 parts of 2,6-naphthalenedicarboxylic acid dimethyl ester, 200.0 parts of 1,4-butanediol, and 0.062 parts of tetra-n-butyl titanate were placed in an ester exchange reactor, and the ester exchange reaction was carried out for 150 minutes while the temperature of the ester exchange reactor was raised to 210°C. The resulting reaction product was then transferred to a polycondensation reactor to initiate the polycondensation reaction. The polycondensation reaction was carried out by gradually reducing the pressure in the polycondensation reactor from atmospheric pressure to 0.13 kPa (1 torr) or less over 40 minutes, while simultaneously raising the temperature to the predetermined reaction temperature of 260°C. Thereafter, the polycondensation reaction was carried out for 140 minutes while maintaining the polycondensation reaction temperature at 260°C and the pressure at 0.13 kPa (1 torr). After 140 minutes had elapsed, the polycondensation reaction was terminated, and the polybutylene naphthalate resin was extracted in the form of strands and cut into chips using a cutter while cooling with water. Next, the obtained polybutylene naphthalate resin was subjected to solid-state polymerization for 8 hours under conditions of a temperature of 213° C. and a pressure of 0.13 kPa (1 Torr) or less to obtain a polybutylene naphthalate resin.

[0063] A-II: Polyphenylene sulfide resin having a carboxyl group at the end obtained in Production Example II <Manufacturing example II> A 5L reactor equipped with a thermocouple for measuring the internal temperature, a nitrogen-filled reactor, and a vacuum line for applying a vacuum was heated to 180°C to completely melt and mix 5130 g of paradiiodobenzene (p-DIB), 450 g of sulfur, and 4 g of 1,3-diiodo-4-nitrobenzene as a reaction initiator. The polymerization reaction proceeded under stepwise temperature and pressure increases, starting from initial conditions of 220°C and 350 Torr, to a final reaction temperature of 300°C and a pressure of less than 1 Torr. When the polymerization reaction reached 80% completion (the degree of completion was determined by measuring the relative viscosity of the current viscosity to the target viscosity [(current viscosity / target viscosity) × 100(%)], the current viscosity was measured using a viscometer on a sample taken during the polymerization), 25 g of 2,2'-dithiobisbenzothiazole was added as a polymerization terminator, and the reaction was allowed to proceed for 1 hour. Next, when the polymerization reaction had progressed to 90%, 51 g of 4-iodobenzoic acid was added, and the reaction was allowed to proceed for 10 minutes under a nitrogen atmosphere. After that, a vacuum was gradually applied to 0.5 Torr or less, and the reaction was allowed to proceed for 1 hour. The reaction was then terminated, synthesizing a polyarylene sulfide resin having a carboxyl group at the end of the main chain. The resin after the reaction was then cut into pellets using a small strand cutter. The polyarylene sulfide resin was analyzed by FT-IR, and the spectrum showed a peak at approximately 1600-1800 cm. -1 The presence of a carboxyl group peak was confirmed in the FT-IR spectrum. -1 When the height intensity of the ring stretch peak that appears at about 1600 to 1800 cm is taken as 100%, -1 The relative height intensity of the peak was about 3.4%, and the weight average molecular weight was 71,000.

[0064] A-III: Polyphenylene sulfide resin having phenyl groups at its terminals obtained in Production Example III <Production example III> In a 5 L reactor equipped with a thermocouple capable of measuring the internal temperature of the reactor and a vacuum line capable of filling with nitrogen and applying a vacuum, reactants containing 5130 g of paradiiodobenzene (p-DIB), 450 g of sulfur, and 4 g of 1,3-diiodo-4-nitrobenzenemercaptobenzothiazole as a reaction initiator were heated to 180°C to completely melt and mix, and then the polymerization reaction was carried out while gradually increasing the temperature and decreasing the pressure, starting from initial reaction conditions of 220°C and 350 Torr, to a final reaction temperature of 300°C and a pressure of 1 Torr or less. When the polymerization reaction had progressed 80% (the degree of progress of the polymerization reaction was determined by measuring the relative ratio of the current viscosity to the target viscosity [(current viscosity / target viscosity) × 100 (%)]. The current viscosity was measured by taking a sample during the polymerization process and measuring it with a viscometer), 60 g of 2,2'-dithiobisbenzothiazole was added as a polymerization terminator, and the reaction was allowed to proceed for 10 minutes under a nitrogen atmosphere. After that, a vacuum was gradually applied to below 0.5 Torr until the target viscosity was reached, at which point the reaction was terminated, synthesizing a polyarylene sulfide resin having phenyl groups at the main chain terminals. The resin after the reaction was completed was pelletized using a small strand cutter. The weight-average molecular weight was 72,000.

[0065] (B component) BI: Maleic anhydride modified polyethylene resin obtained in Production Example IV <Manufacturing example IV> A polyethylene resin blend (100 parts by weight) consisting of 15% by weight of ultra-high molecular weight polyethylene (Hi-Zex Million 630M, manufactured by Mitsui Chemicals, Inc.) with an intrinsic viscosity of 31 dL / g measured in decalic acid at 135 °C and 85% by weight of polyethylene (Hi-Zex 2200J, manufactured by Prime Polymer Co., Ltd.) with an intrinsic viscosity of 2 dL / g measured in decalic acid at 135 °C, 1 part by weight of maleic anhydride, and 0.07 parts by weight of organic peroxide (Perhexine-25B, manufactured by Nippon Oil & Fats Co., Ltd.) was mixed in a Nauta mixer. The resulting mixture was melt-kneaded in a single-screw extruder (EXT40 mm extruder, manufactured by Isuzu Chemical Engineering Co., Ltd.) set at 250 °C to obtain a BI component. The intrinsic viscosity [η] of the resulting modified polyethylene resin measured in decalic acid at 135 °C was 5.5 dL / g, and the viscosity-average molecular weight Mv was 550,000.

[0066] B-II: Polyethylene resin having no polar groups obtained in Production Example V <Manufacturing example V> A polyethylene resin mixture consisting of 10% by weight of ultra-high molecular weight polyethylene (Hi-Zex Million 630M, manufactured by Mitsui Chemicals, Inc.) with an intrinsic viscosity of 31 dL / g measured in decaphosphoric acid at 135°C and 90% by weight of polyethylene (Hi-Zex 2200J, manufactured by Prime Polymer Co., Ltd.) with an intrinsic viscosity of 2 dL / g measured in decaphosphoric acid at 135°C was mixed in a Nauta mixer, and the resulting mixture was melt-kneaded in a single-screw extruder (EXT40 mm extruder, manufactured by Isuzu Chemical Engineering Co., Ltd.) set at 250°C to obtain Component B-II. The intrinsic viscosity [η] of the resulting polyethylene resin measured in decaphosphoric acid at 135°C was 4.3 dL / g, and the viscosity-average molecular weight Mv was 400,000. B-III: Polytetrafluoroethylene: KT-600M (product name) (Kitamura Co., Ltd., melting point 325-335°C, average particle size 14 μm) B-IV (Comparative Example): Polyethylene wax: Hiwax 310MP (product name) (manufactured by Mitsui Chemicals, Inc., viscosity average molecular weight Mv approximately 3,000) BV (comparison example): Ultra-high molecular weight polyethylene: Hi-Zex Million 240S (product name) (manufactured by Mitsui Chemicals, Inc., viscosity average molecular weight Mv approximately 2,000,000)

[0067] (C component) CI: Fully aromatic polyamide fiber: T322EK (product name) (Teijin Limited, para-aramid fiber, major diameter 12 μm, average fiber length 3 mm, polyester resin sizing agent, twist count 245 times / m) C-II: Fully aromatic polyamide fiber: T322UR (product name) (Teijin Limited, para-aramid fiber, major diameter 12 μm, average fiber length 3 mm, polyurethane resin sizing agent, twist count 60 times / m) C-III (Comparative Example): Glass fiber: CS 3PE944 (trade name) (manufactured by Nitto Boseki Co., Ltd., average fiber length 3 mm, major diameter 13 μm) C-IV (Comparative Example): Carbon fiber: PAN-based carbon fiber HT P722 (trade name) (manufactured by Teijin Limited, average fiber length 3 mm, major diameter 7 μm, polyimide-based sizing agent)

[0068] (D component) DI: Polyamide 6: UBE Nylon 1011FB (product name) (manufactured by Ube Industries, Ltd.) D-II: Polyamide 10T: Xecot XP500 (product name) (manufactured by Unitika Ltd.) D-III: Polyamide 66: Leona 1402S (product name) (manufactured by Asahi Kasei Corporation)

[0069] (E component) EI: Bisphenol A epoxy resin: jER1256 (product name) (manufactured by Mitsubishi Chemical Corporation, epoxy equivalent weight 7,500-8,500 g / eq) E-II: Trisphenolmethane epoxy resin: EPPN-501H (product name) (manufactured by Nippon Kayaku Co., Ltd., epoxy equivalent weight 158-178g / eq)

[0070] [Table 1]

[0071] <Examples 1 to 14> Because the resin composition is within the scope of the present invention, it exhibits excellent long-term low wear properties, a low coefficient of friction during sliding, and excellent feedability of pellets of the resin composition to a molding machine during injection molding.

[0072] <Comparative Example 1> Since the content of component B was below the lower limit, the wear amount and friction coefficient during long-term sliding were high. <Comparative Example 2> Because the content of component B exceeded the upper limit, the amount of wear during long-term sliding was high, and continuous molding was difficult due to poor pellet supply. <Comparative Example 3> Since the content of C component was below the lower limit, the wear amount during long-term sliding was high. <Comparative Example 4> Since the content of C component exceeded the upper limit, pellet supply was poor and continuous molding was difficult. <Comparative Example 5> Because the content of D component exceeded the upper limit, the amount of wear during long-term sliding was high, and continuous molding was difficult due to poor pellet supply. <Comparative Example 6> Because the content of component D was below the lower limit, the amount of wear and the coefficient of friction during long-term sliding were high, and continuous molding was difficult due to poor pellet supply. <Comparative Example 7> Since component C is glass fiber, the wear amount during long-term sliding was high. <Comparative Example 8> Because component C is carbon fiber, the wear amount and friction coefficient during long-term sliding were high. <Comparative Example 9> Because the viscosity average molecular weight of component B was below the lower limit, the amount of wear during long-term sliding was high. <Comparative Example 10> Because the viscosity average molecular weight of component B exceeded the upper limit, a large amount of component B separated during extrusion, causing strand breakage and making it impossible to obtain pellets.

Claims

1. A resin composition comprising 100 parts by weight of (A) a thermoplastic polyester resin (component A), 4 to 25 parts by weight of (B) a sliding material (component B) which is a polyethylene resin having a viscosity average molecular weight of 100,000 to 1,000,000, 5 to 30 parts by weight of (C) wholly aromatic polyamide fibers (component C), and 0.5 to 15 parts by weight of (D) at least one polyamide resin (component D) selected from the group consisting of aliphatic polyamides and semi-aromatic polyamides.

2. 2. The resin composition according to claim 1, wherein component D is at least one polyamide resin selected from the group consisting of polyamide 6 and polyamide 66.

3. 3. The resin composition according to claim 1, further comprising 0.5 to 8 parts by weight of an epoxy resin (E) having an epoxy equivalent of 100 to 10,000 g / eq per 100 parts by weight of component A.

4. A resin composition described in any one of claims 1 to 3, wherein component B is a modified polyethylene resin modified with maleic anhydride.

5. 5. The resin composition according to claim 1, wherein component A is a polybutylene naphthalate resin.

6. 6. The resin composition according to claim 1, wherein component C is a wholly aromatic polyamide fiber bundled with at least one sizing agent selected from the group consisting of polyester resins and polyurethane resins.

7. 7. The resin composition according to claim 1, wherein the average fiber length of component C before being added to component A is 2 to 6 mm.

8. 8. The resin composition according to claim 1, wherein component C is a para-type wholly aromatic polyamide fiber.

9. A molded article made of the resin composition according to any one of claims 1 to 8.

Images