Thermoplastic polyester elastomer resin composition for resin tape material and resin tape molded body

Abstract

According to the present application, a polyester elastomer resin composition for resin belt material having high resin strength, excellent bending fatigue resistance and molding properties is obtained. The present application is a thermoplastic polyester elastomer resin composition for resin belt material, characterized by containing: 80 to 92.99% by weight of a thermoplastic polyester elastomer (A); 7 to 19.99% by weight of glass fiber (B); and 0.01 to 5.0% by weight of a crystallization nucleating agent (C), the thermoplastic polyester elastomer (A) being a polyester block copolymer, the polyester block copolymer containing: 40 to 70% by weight of a high-melting crystalline polymer segment (a1) containing a crystalline aromatic polyester unit; and 30 to 60% by weight of a low-melting polymer segment (a2) containing an aliphatic polyether unit, the thermoplastic polyester elastomer resin composition for resin belt material having a melt flow rate of 1.0 g / 10 min or more and less than 10.0 g / 10 min, measured according to ASTM D1238 at 230°C under a load of 2160 g.

Description

Technical Field

[0001] This invention relates to thermoplastic polyester elastomer resin compositions and resin tape molded bodies for use in resin tape materials with high resin strength, excellent moldability, excellent flexural fatigue resistance, and especially good flexural fatigue resistance at low temperatures. Background Technology

[0002] Polyester block copolymers, which use crystalline aromatic polyester units as hard segments and aliphatic polyether units such as poly(oxyethylene) glycol and / or aliphatic polyester units such as polylactone as soft segments, are widely used in the automotive, electrical / electronic components, and consumer materials industries due to their excellent mechanical properties such as strength, impact resistance, elastic recovery, and softness, as well as their low-temperature and high-temperature properties. Furthermore, they are easy to mold and process due to their thermoplasticity.

[0003] Due to its excellent strength, flexibility, and resistance to flexural fatigue, as well as its ease of molding and processing, it is used as a material for resin belts. One example of a resin belt is a toothed belt, which has a structure in which teeth mesh with gears, and the belt slides by the rotation of the gears. Because of the repeated sliding motion during use, the strength and resistance to flexural fatigue of the belt are particularly important in this application method.

[0004] Generally, there is a problem that increasing resin strength reduces flexural fatigue resistance, while increasing flexural resistance reduces resin strength. Furthermore, the strength of the belt is affected by the dimensions of the molded belt, thus it is necessary to suppress the formation of shrinkage marks in the molded article. Therefore, it is known to improve the flexural fatigue resistance of the resin by adding glass fibers to the thermoplastic elastomer to increase the resin strength and increase the molecular weight.

[0005] (Patent Document 1)

[0006] Existing technical documents

[0007] Patent documents

[0008] Patent Document 1: Japanese Patent Application Publication No. 2017-172794 Summary of the Invention

[0009] The problem that the invention aims to solve

[0010] Resin tapes are widely used in electrochemical components and automotive parts, where the operating environment spans a wide temperature range from low temperatures (-40°C) to high temperatures (80°C). Therefore, the resin tape material is required to have good properties over this wide temperature range. However, in the case of the method in Patent Document 1, particularly at low temperatures, flexibility and resistance to bending fatigue decrease, suggesting that the resin tape may break during use.

[0011] Therefore, the objective of this invention is to solve the problems in the prior art described above, and to provide a thermoplastic polyester elastomer resin composition for resin tape materials that has a good balance between resin strength and flexural fatigue resistance at both room temperature and low temperature, and excellent impact resistance, as well as resin tape molded bodies formed therefrom.

[0012] Methods for solving problems

[0013] To solve the above-mentioned problems, the present invention employs the following means. Specifically, the thermoplastic polyester elastomer resin composition for resin tape materials of the present invention is characterized by containing: 80-92.99% by weight of thermoplastic polyester elastomer (A); 7-19.99% by weight of glass fiber (B); and 0.01-5.0% by weight of a crystallizing nucleating agent (C). The thermoplastic polyester elastomer (A) is a polyester block copolymer, which comprises: 40-70% by weight of a high-melting-point crystalline polymer segment (a1) containing crystalline aromatic polyester units; and 30-60% by weight of a low-melting-point polymer segment (a2) containing aliphatic polyether units. The melt flow rate of the thermoplastic polyester elastomer resin composition for resin tape materials, measured according to ASTM D1238 at 230°C and a load of 2160g, is 1.0 g / 10 min or more and less than 10.0 g / 10 min.

[0014] Furthermore, the resin tape molded body of the present invention is characterized in that it is formed from such a resin tape material using a thermoplastic polyester elastomer resin composition.

[0015] The effects of the invention

[0016] According to the present invention, as described below, a thermoplastic polyester elastomer resin composition for resin tape materials can be obtained that has a good balance between resin strength and flexural fatigue resistance at both room temperature and low temperature, and excellent impact resistance. Detailed Implementation

[0017] The present invention will now be described.

[0018] The thermoplastic polyester elastomer (A) used in this invention is a polyester block copolymer composed of high-melting-point crystalline polymer segments (a1) mainly formed of crystalline aromatic polyester units and low-melting-point polymer segments (a2) mainly formed of aliphatic polyether units. The high-melting-point crystalline polymer segments are mainly formed of crystalline aromatic polyester units, that is, polyesters mainly formed of aromatic dicarboxylic acids or their ester-forming derivatives and diols or their ester-forming derivatives.

[0019] Examples of aromatic dicarboxylic acids or their ester-forming derivatives include terephthalic acid, isophthalic acid, phthalic acid, naphthalene-2,6-dicarboxylic acid, naphthalene-2,7-dicarboxylic acid, anthracene dicarboxylic acid, biphenyl-4,4'-dicarboxylic acid, diphenoxyethane dicarboxylic acid, 4,4'-diphenyl ether dicarboxylic acid, 5-sulfoisophthalic acid, and sodium 3-sulfoisophthalate. In this invention, the aforementioned aromatic dicarboxylic acids are primarily used, but a portion of these aromatic dicarboxylic acids may be replaced with alicyclic dicarboxylic acids such as 1,4-cyclohexanedicarboxylic acid, cyclopentanedicarboxylic acid, and 4,4'-dicyclohexyldicarboxylic acid, as well as aliphatic dicarboxylic acids such as adipic acid, succinic acid, oxalic acid, sebacic acid, dodecanoic acid, and dimer acids. Furthermore, ester-forming derivatives of dicarboxylic acids, such as lower alkyl esters, aryl esters, carbonates, and acyl halides, can also be used equivalently.

[0020] Aromatic dicarboxylic acids or their ester-forming derivatives that are dicarboxylic acid components are preferably terephthalic acid or dimethyl terephthalate, and more preferably terephthalic acid.

[0021] As the aforementioned diols or their ester-forming derivatives, diols with a molecular weight of 400 or less are preferred, such as aliphatic diols like 1,4-butanediol, ethylene glycol, 1,3-propanediol, 1,5-pentanediol, 1,6-hexanediol, neopentanediol, and 1,10-decanediol; alicyclic diols like 1,1-cyclohexanediethanol, 1,4-dicyclohexanediethanol, and tricyclodecanediethanol; benzenediethanol; bis(p-hydroxy)biphenyl; bis(p-hydroxy)diphenylpropane; 2,2'-bis[4-(2-hydroxyethoxy)phenyl]propane; bis[4-(2-hydroxyethoxy)phenyl]sulfone; 1,1-bis[4-(2-hydroxyethoxy)phenyl]cyclohexane; 4,4'-dihydroxy-p-terphenyl; and 4,4'-dihydroxy-p-tetraphenyl. Such diols can also be used in the form of ester-forming derivatives such as acetyl groups or alkali metal salts.

[0022] These dicarboxylic acids, their derivatives, diol components and their derivatives can be used in combination in more than two types.

[0023] A preferred example of such a high-melting-point crystalline polymer segment (a1) is a material comprising polybutylene terephthalate units derived from terephthalic acid or dimethyl terephthalate and 1,4-butanediol, and polybutylene isophthalate units derived from isophthalic acid or dimethyl isophthalate and 1,4-butanediol. The copolymerization amount of the high-melting-point crystalline polymer segment (a1) is typically 40–70% by weight, preferably 50–70% by weight.

[0024] Regarding the copolymerization amount of the high-melting-point crystalline polymer segment (a1), for example, in the case where the constituent component of the high-melting-point crystalline polymer segment (a1) is polybutylene terephthalate unit, it is the total of the mass percentages of terephthalic acid and 1,4-butanediol.

[0025] The low-melting-point polymer segments (a2) used in the thermoplastic polyester elastomer (A) used in this invention are mainly formed from aliphatic polyethers.

[0026] Specific examples of such aliphatic polyethers include poly(ethylene oxide) glycol, poly(propylene oxide) glycol, poly(trimethylene oxide) glycol, poly(tetramethylene oxide) glycol, poly(hexamethylene oxide) glycol, copolymers of ethylene oxide and propylene oxide, ethylene oxide adducts of poly(propylene oxide) glycol, and copolymers of ethylene oxide and tetrahydrofuran. Among these, poly(tetramethylene oxide) glycol and / or ethylene oxide adducts of poly(propylene oxide) glycol and / or copolymers of ethylene oxide and tetrahydrofuran are preferred.

[0027] The copolymerization amount of the low-melting-point polymer segment (a2) of the thermoplastic polyester elastomer used in this invention is typically 30-60% by weight, preferably 30-50% by weight.

[0028] Regarding the copolymerization amount of the low-melting-point crystalline polymer segment (a2), for example, in the case where the constituent component of the low-melting-point crystalline polymer segment (a2) is poly(tetramethylene oxide) glycol units, it is the mass of poly(tetramethylene oxide) glycol.

[0029] The thermoplastic polyester elastomer (A) used in this invention can be manufactured by known methods. Specific examples include: a method of transesterifying a lower alcohol diester of a dicarboxylic acid, an excess of a low molecular weight diol, and a low-melting-point polymer segment in the presence of a catalyst, followed by melt polycondensation of the resulting reaction product; and a method of esterifying a dicarboxylic acid with an excess of a diol and a low-melting-point polymer segment in the presence of a catalyst, followed by melt polycondensation of the resulting reaction product, etc.

[0030] The thermoplastic polyester elastomer (A) obtained by polycondensation is then subjected to solid-phase polycondensation. Solid-phase polycondensation is carried out at a temperature where the thermoplastic polyester elastomer (A), which has been granulated after melt polycondensation, does not melt, typically within a temperature range of 140°C to 220°C. Pre-crystallization and drying processes are desirable before solid-phase polycondensation. Furthermore, solid-phase polycondensation is carried out under high vacuum or an inert gas flow. Under high vacuum, a reduced pressure of 665 Pa or less is preferred, and more preferably 133 Pa or less is further preferred. Under an inert gas flow, nitrogen gas is typically preferred, and the pressure is not particularly limited, but atmospheric pressure is preferred. As the reaction vessel, a rotatable vacuum dryer, a tower dryer capable of carrying inert gases, or the like is preferred.

[0031] The amount of thermoplastic polyester elastomer (A) is 80 to 92.99% by weight relative to the total amount of thermoplastic polyester elastomer (A), glass fiber (B), and crystallizing nucleating agent (C) contained in the thermoplastic polyester elastomer resin composition for resin tape materials.

[0032] The glass fiber (B) used in this invention is a chopped filament type or a roving type glass fiber. Preferably, it is a glass fiber treated with a silane coupling agent such as an aminosilane compound or an epoxy silane compound and / or a bundler containing one or more epoxy compounds such as bisphenol A diglycidyl ether or phenolic varnish epoxy compounds.

[0033] The average fiber diameter of the glass fiber (B) is preferably 5 to 20 μm. There is no particular limitation on the average fiber length of the glass fiber (B), but it is preferably 0.1 to 20 mm, and more preferably 0.1 to 5 mm.

[0034] The amount of glass fiber (B) is 7 to 19.99% by weight relative to the total amount of thermoplastic polyester elastomer (A), glass fiber (B), and nucleating agent (C) contained in the thermoplastic polyester elastomer composition for resin tape material.

[0035] The nucleating agent (C) used in this invention is not particularly limited as long as it does not melt during melt processing and can become a nucleus for crystallization during cooling, but it is preferably an inorganic material, and plate-shaped filler materials and granular filler materials are preferred. Specific examples of plate-shaped filler materials include talc, mica, and glass flakes, and specific examples of granular filler materials include calcium carbonate, clay, barium sulfate, and glass beads.

[0036] The amount of crystallizing nucleating agent (C) is 0.01 to 5% by weight relative to the total amount of thermoplastic polyester elastomer (A), glass fiber (B), and crystallizing nucleating agent (C) contained in the thermoplastic polyester elastomer composition for resin tape material.

[0037] Furthermore, the strength of the tape can be improved by further adding polyester resin (D) to the thermoplastic polyester elastomer resin composition for the resin tape material of the present invention.

[0038] The so-called polyester resin (D) used in this invention is obtained by polycondensation of at least one acid component selected from terephthalic acid, 2,6-naphthalenedicarboxylic acid, isophthalic acid, etc., and at least one diol component selected from ethylene glycol, propylene glycol, butanediol, hexanediol, etc. Specifically, in addition to polybutylene terephthalate (PBT), polypropylene terephthalate (PPT), polyethylene terephthalate (PET), polyhexanediol terephthalate (PHT), polyethylene naphthalate, polybutylene naphthalate (PBN), polycyclohexane-1,4-dimethylol terephthalate, etc., copolyesters such as polyethylene glycol isophthalate / terephthalate (PET / I) and polybutylene glycol (terephthalate / isophthalate) (PET / I) can also be cited.

[0039] Among these polyester resins, polyethylene terephthalate, polybutylene terephthalate, polybutylene naphthalate, and polybutylene glycol (terephthalate / isophthalate) are preferred, and polybutylene terephthalate is even more preferred.

[0040] The amount of polyester resin (D) is preferably 5 to 30 by weight relative to the total amount of the thermoplastic polyester elastomer resin composition for resin tape material, namely thermoplastic polyester elastomer (A), glass fiber (B), crystal nucleating agent (C) and polyester resin (D).

[0041] Furthermore, in the thermoplastic polyester elastomer resin composition for the resin tape material of the present invention, antioxidants, ultraviolet absorbers, light stabilizers, antistatic agents, lubricants, dyes, pigments, plasticizers, flame retardants, mold release agents, silicone oils and other additives may be added as needed within a range that does not impair the purpose.

[0042] The thermoplastic polyester elastomer composition for resin tape materials of the present invention has a melt flow rate of 1.0 g / 10 min or more and less than 10.0 g / 10 min, as measured according to ASTM D1238 at 230°C and a load of 2160 g. As mentioned above, it is important to use a thermoplastic elastomer (A) obtained by solid-state polycondensation. By having a melt flow rate of 1.0 g / 10 min or more and less than 10.0 g / 10 min, a thermoplastic polyester elastomer resin composition for resin tape materials with an excellent balance between resin strength and flexural fatigue resistance not only at room temperature but also at low temperatures, and resin tape molded articles formed therefrom, can be provided.

[0043] The thermoplastic polyester elastomer composition for the resin tape material of the present invention preferably has a flexural modulus of 900 MPa or more at 23°C as determined by ASTM D790, and a flexural modulus of 2000 MPa or less at -30°C as determined by ASTM D790.

[0044] The resin tape molded body of the present invention is formed by molding the resin tape material of the present invention using a thermoplastic polyester elastomer composition. Since the resin tape molded body repeatedly slides during use, the strength and resistance to bending fatigue of the tape are particularly important, and the thermoplastic polyester elastomer composition of the resin tape material of the present invention is suitable for use in this application.

[0045] Example

[0046] The effects of the present invention are illustrated below through examples. The present invention can be implemented with appropriate modifications within the scope of its spirit. Furthermore, unless otherwise specified, all terms "%" and "parts" in the examples are based on weight. Additionally, the physical properties shown in the examples were determined by the following measurement methods.

[0047] [Melting point and crystallization temperature]

[0048] The crystallization temperature was determined using a DSC Q100 manufactured by Tier Ey Instrument Co., Ltd., under a nitrogen atmosphere, by heating from 40°C to 250°C at a heating rate of 20°C / min, holding at 250°C for 3 minutes, and then cooling to 40°C at a cooling rate of 10°C / min.

[0049] The peak temperature of the melting peak was further determined when heated to 250°C at a heating rate of 10°C / min.

[0050] [Mel flow rate]

[0051] The test was conducted according to ASTM D1238 at 230°C and a load of 2160g.

[0052] [Tensile breaking strength, tensile elongation at break]

[0053] Granules that have been dried in hot air at 90°C for more than 3 hours were used to form JIS K7113 No. 2 dumbbell test pieces using an injection molding machine (Nissei Resin Kogyo NEX-1000) under molding conditions of barrel temperature 240°C and mold temperature 50°C, and measured according to JIS K7113 (1995 edition).

[0054] [Flexural modulus]

[0055] Test pieces were prepared using granules that had been dried in hot air at 90°C for more than 3 hours, using an injection molding machine (Nissei Resin Kogyo NEX-1000), under molding conditions of barrel temperature 240°C and mold temperature 50°C, and were tested according to ASTM D790 in atmospheres at 23°C and -30°C.

[0056] [Bending fatigue performance (23℃, -30℃)]

[0057] Granules dried at 90°C for more than 3 hours were used to form a 120mm x 75mm x 2mm thick square plate using an injection molding machine (Nissei Resin Kogyo NEX-1000) at a barrel temperature of 240°C and a mold temperature of 50°C. Strips measuring 50mm x 6mm x 2mm thick were cut from these strips. Using a De Mattia bending fatigue testing machine in atmospheres of 23°C and -30°C, the number of bends required to reach fracture when the platen was stroked between 30mm and 20mm apart was determined.

[0058] [Izod Impact Strength (23℃, -30℃)]

[0059] Test pieces were prepared using granules that had been dried in hot air at 90°C for more than 3 hours, using an injection molding machine (Nissei Resin Kogyo NEX-1000), under molding conditions of barrel temperature 240°C and mold temperature 50°C, and were tested according to ASTM D256 at 23°C and -30°C atmospheres.

[0060] [Extrusion Molding Properties]

[0061] Granules dried in hot air at 90°C for more than 3 hours were used to form resin tapes using a single-screw extruder at temperatures ranging from 220 to 250°C. The dimensional characteristics of the tapes were measured. Evaluation was based on grades A: shrinkage of less than 0.5% in the central region of the tape, and B: shrinkage of less than 1% in the central region of the tape.

[0062] [Manufacturing of Polyester Elastomer (A-1)]

[0063] 505 parts of terephthalic acid and 251 parts of 1,4-butanediol, which are high-melting-point crystalline polymer segments (a1), 354 parts of poly(tetramethylene oxide) glycol with a number-average molecular weight of approximately 1400, which is a low-melting-point polymer segment (a2), 0.3 parts of titanium tetrabutoxide, and 0.2 parts of mono-n-butyl-monohydroxytin oxide were added to a reaction vessel equipped with a ribbon-type stirring blade. The mixture was heated at 190–225°C for 3 hours, and esterification was carried out while distilling off the reaction water. 2.0 parts of titanium tetrabutoxide and 0.5 parts of "Iluganox" 1098 (a hindered phenolic antioxidant manufactured by Chibagaigi Co., Ltd.) were added to the reaction mixture, and the temperature was raised to 245°C. The pressure in the system was then reduced to 0.2 mmHg after 50 minutes, and melt polycondensation was carried out under these conditions for 2 hours and 45 minutes. The resulting polyester elastomer is discharged in water in strips and then cut into granules.

[0064] Polyester elastomer particles were added to a rotatable reaction vessel, and the pressure inside the system was reduced to 27 Pa. Solid-state polycondensation was carried out by heating at 170–180 °C for 48 hours while rotating the vessel. The melt flow rate of the resulting polyester elastomer (A-1) particles was 2 g / 10 min at 230 °C and a load of 2160 g. Furthermore, the weight percentage of the high-melting-point crystalline polymer segment (a1) was 65%, and the weight percentage of the low-melting-point polymer segment (a2) was 35%.

[0065] [Manufacturing of Polyester Elastomer (A-2)]

[0066] 420 parts of terephthalic acid and 196 parts of 1,4-butanediol, which are high-melting-point crystalline polymer segments (a1), 480 parts of poly(tetramethylene oxide) glycol with a number-average molecular weight of approximately 1400, which are low-melting-point polymer segments (a2), 0.3 parts of titanium tetrabutoxide, and 0.2 parts of mono-n-butyl-monohydroxytin oxide were added to a reaction vessel equipped with a ribbon-type stirring blade. The mixture was heated at 190–225°C for 3 hours while distilling off the reaction water to carry out the esterification reaction. 2.0 parts of titanium tetrabutoxide and 0.5 parts of "Iluganox" 1098 (a hindered phenolic antioxidant manufactured by Chibagaigi Co., Ltd.) were added to the reaction mixture, and the temperature was raised to 245°C. The pressure in the system was then reduced to 0.2 mmHg after 50 minutes, and melt polycondensation was carried out under these conditions for 2 hours and 45 minutes. The resulting polyester elastomer is discharged in water in strips and then cut into granules.

[0067] Polyester elastomer particles were added to a rotatable reaction vessel, and the pressure inside the system was reduced to 27 Pa. Solid-state polycondensation was carried out by heating at 170–180 °C for 48 hours while rotating the vessel. The melt flow rate of the resulting polyester elastomer (A-2) particles was 2 g / 10 min at 220 °C and a load of 2160 g. Furthermore, the weight percentage of the high-melting-point crystalline polymer segment (a1) was 52%, and the weight percentage of the low-melting-point polymer segment (a2) was 48%.

[0068] [Manufacturing of Polyester Elastomer (A-3)]

[0069] 593 parts of terephthalic acid and 307 parts of 1,4-butanediol, which are high-melting-point crystalline polymer segments (a1), 229 parts of poly(tetramethylene oxide) glycol with a number-average molecular weight of approximately 1400, which is a low-melting-point polymer segment (a2), 0.3 parts of titanium tetrabutoxide, and 0.2 parts of mono-n-butyl-monohydroxytin oxide were added to a reaction vessel equipped with a ribbon-type stirring blade. The mixture was heated at 190–225°C for 3 hours while distilling off the reaction water to carry out the esterification reaction. Then, 2.0 parts of titanium tetrabutoxide and 0.5 parts of "Iluganox" 1098 (a hindered phenolic antioxidant manufactured by Chibagaigi Co., Ltd.) were added to the reaction mixture. The temperature was raised to 245°C, and the pressure in the system was reduced to 0.2 mmHg after 50 minutes. Melt polycondensation was carried out under these conditions for 2 hours and 45 minutes. The resulting polyester elastomer (A-3) was discharged in water in strip form and then cut into granules. The weight percentage of the high-melting-point crystalline polymer segment (a1) was 78%, and the weight percentage of the low-melting-point polymer segment (a2) was 22%.

[0070] [Manufacturing of Polyester Elastomer (A-4)]

[0071] Polyester elastomer (A-3) particles were added to a rotatable reaction vessel, and the pressure inside the system was reduced to 27 Pa. Solid-state polycondensation was carried out by heating at 170–180 °C for 48 hours while rotating the vessel. The melt flow rate of the resulting polyester elastomer (A-4) particles was 2 g / 10 min in a test conducted at 240 °C and a load of 2160 g.

[0072] [Manufacturing of Polyester Elastomer (A-5)]

[0073] 505 parts of terephthalic acid and 251 parts of 1,4-butanediol, which are high-melting-point crystalline polymer segments (a1), 354 parts of poly(tetramethylene oxide) glycol with a number-average molecular weight of approximately 1400, which is a low-melting-point polymer segment (a2), 0.3 parts of titanium tetrabutoxide, and 0.2 parts of mono-n-butyl-monohydroxytin oxide were added to a reaction vessel equipped with a ribbon-type stirring blade. The reaction was heated at 190–225°C for 3 hours while distilling off the reaction water. Then, 2.0 parts of titanium tetrabutoxide and 0.5 parts of "Iluganox" 1098 (a hindered phenolic antioxidant manufactured by Chibagaigi Co., Ltd.) were added to the reaction mixture. The temperature was raised to 245°C, and the pressure in the system was reduced to 0.2 mmHg after 50 minutes. Melt polycondensation was carried out under these conditions for 2 hours and 45 minutes. The resulting polyester elastomer (A-5) was discharged in water in strip form and then cut into granules. The weight percentage of the high-melting-point crystalline polymer segment (a1) was 65%, and the weight percentage of the low-melting-point polymer segment (a2) was 35%.

[0074] [Glass fiber (B)]

[0075] It uses short-cut glass fiber CS3J948 manufactured by Nittobo Corporation. The fiber diameter is approximately 10 μm.

[0076] [Crystallization nucleating agent (C)]

[0077] Hytron (hydrated magnesium silicate) manufactured by Takehara Chemical Industry Co., Ltd. was used. The average particle size was 4 μm.

[0078] [Polyester Resin (D)]

[0079] The resin used is TRECON 1100S (manufactured by Higashi Resha), which is a polybutylene terephthalate (PBT) resin.

[0080] [Examples 1-4]

[0081] Using a twin-screw extruder with a screw diameter of 45 mm, the polyester elastomers (A-1) and (A-2) shown in the reference example, along with the required crystallizing nucleating agent (C) and polyester resin (D), were mixed in the formulation shown in Table 1 and added from the main feed section. Furthermore, a side feeder was installed midway between the main feed section and the ventilation section, and glass fiber (B) was added in the same manner as described above, in the amounts shown in Table 1. The mixture was melt-mixed under extrusion conditions of a heating temperature of 250°C and a screw speed of 150 rpm, discharged in strip form, and granulated through a cooling bath and a wire pelletizer to obtain a thermoplastic polyester elastomer resin composition for resin tape materials.

[0082] The obtained granules were dried at 80°C for 5 hours, and then injection molded at a barrel temperature of 230°C–250°C and a mold temperature of 50°C to obtain test pieces for tensile breaking strength, tensile elongation at break, flexural modulus, flexural fatigue resistance, and Izod impact strength. Various tests were conducted using the obtained test pieces as resin tape molded bodies. The test results are shown in Table 1.

[0083] [Table 1]

[0084]

[0085] The results in Table 1 clearly demonstrate that the resin tape molded articles obtained from the thermoplastic polyester elastomer resin compositions of the resin tape materials shown in Examples 1-4 exhibit high resin strength and excellent flexural fatigue resistance and impact resistance at room temperature. Furthermore, they maintain flexibility even at -30°C, and also exhibit excellent flexural fatigue resistance and impact resistance at -30°C.

[0086] [Comparative Examples 1-5]

[0087] Using a twin-screw extruder with a screw diameter of 45 mm, the polyester elastomers (A-3), (A-4), and (A-5) shown in the reference examples, along with the required nucleating agent (C) and polyester resin (D), were mixed in the formulation shown in Table 2 and added from the main feed section. Furthermore, a side feeder was installed midway between the main feed section and the ventilation section, and glass fiber (B) was added in the same manner as described above, in the amounts shown in Table 2. The mixture was melt-mixed under extrusion conditions of a heating temperature of 250°C and a screw speed of 150 rpm, discharged in strip form, and granulated through a cooling bath and a wire pelletizer to obtain a thermoplastic polyester elastomer resin composition.

[0088] The obtained granules were dried at 80°C for 5 hours, and then injection molded at a barrel temperature of 230°C–250°C and a mold temperature of 50°C to obtain test pieces for tensile breaking strength, tensile elongation at break, flexural modulus, flexural fatigue resistance, and Izod impact strength. Various tests were conducted using the obtained test pieces as resin tape molded bodies. The test results are shown in Table 2.

[0089] [Table 2]

[0090]

[0091] The results in Table 2 clearly show that the resin tape molded articles obtained from the thermoplastic polyester elastomer resin compositions of Comparative Examples 1-5, which do not meet the conditions of the present invention, are inferior to the resin tape molded articles obtained from the thermoplastic polyester elastomer resin compositions for resin tape materials of the present invention in any of the following aspects: softness at -30°C, flexural fatigue resistance at 23°C, and flexural fatigue resistance at -30°C. In Comparative Examples 1 and 2, the softness at -30°C and flexural fatigue resistance at 23°C and -30°C are insufficient. In Comparative Examples 3 and 4, although the flexural fatigue resistance at 23°C is good, the softness and flexural fatigue resistance at -30°C are poor. Furthermore, in Comparative Example 5, although the softness at -30°C is good, the flexural fatigue resistance at 23°C and -30°C is poor.

Claims

1. A thermoplastic polyester elastomer resin composition for resin tape materials, characterized in that, contain: Thermoplastic polyester elastomer (A) 80–92.99% by weight; Glass fiber (B) 7–19.99% by weight; and Crystallization nucleating agent (C) 0.01–5.0% by weight The thermoplastic polyester elastomer (A) is a polyester block copolymer, and the polyester block copolymer comprises: The high-melting-point crystalline polymer segment (a1) containing crystalline aromatic polyester units comprises 65–70% by weight; and Low-melting-point polymer segments (a2) containing aliphatic polyether units, 30–35% by weight The thermoplastic polyester elastomer resin composition used for the resin tape material, as determined according to ASTM D1238, has a melt flow rate of ≥1.0 g / 10 min and <10.0 g / 10 min at 230°C and a load of 2160 g. The flexural modulus at 23°C, as determined by ASTM D790, is greater than 900 MPa, and the flexural modulus at -30°C, as determined by ASTM D790, is less than 2000 MPa.

2. The thermoplastic polyester elastomer resin composition for resin tape material according to claim 1, further comprising 5 to 30% by weight of polyester resin (D) relative to the thermoplastic polyester elastomer resin composition for resin tape material.

3. The thermoplastic polyester elastomer resin composition for resin tape materials according to claim 1 or 2, characterized in that, The nucleating agent (C) is an inorganic substance.

4. A resin strip molded body, characterized in that, The resin tape material according to any one of claims 1 to 3 is molded from a thermoplastic polyester elastomer resin composition.

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