WO2011052464A1

WO2011052464A1 - Copolymerized polyamide

Info

Publication number: WO2011052464A1
Application number: PCT/JP2010/068560
Authority: WO
Inventors: 順一中尾; 貴司清水; 秀和吉田; 岳丸山
Original assignee: 東洋紡績株式会社
Priority date: 2009-10-27
Filing date: 2010-10-21
Publication date: 2011-05-05
Also published as: JPWO2011052464A1; TW201122019A

Abstract

Provided is a nylon-6T that, in addition to having a high melting point of at least 300°C and low water absorption, has each of the following three properties to a high degree: moldability, resistance to heat aging, and gas barrier functionality. The provided nylon-6T is a copolymerized polyamide characterized by comprising: (a) between 55 and 75 mol% of a constituent unit obtained from a molar equivalent salt of hexamethylenediamine and terephthalic acid; and (b) between 25 and 45 mol% of a constituent unit obtained from 11-aminoundecanoic acid or undecanelactam.

Description

Copolyamide

The present invention relates to a novel polyamide highly satisfying all three properties of moldability, heat aging resistance and gasoline barrier property in addition to high melting point and low water absorption.

As a polyamide used for molding materials, sliding materials and the like, 6T nylon synthesized by a co-condensation polymerization reaction of hexamethylenediamine (6) and terephthalic acid (T) has been well known. 6T nylon is a polyamide with a good balance of resin properties such as heat resistance, mechanical properties, chemical resistance, slidability, gas barrier properties and gasoline barrier properties, but 6T nylon that is not copolymerized has a melting point exceeding 360 ° C. Therefore, it has a drawback that it is difficult to polymerize the polymer and to mold the obtained polymer.

In order to impart the moldability of 6T nylon, there has been a means for reducing the melting point from 290 ° C. to 330 ° C. by copolymerizing caprolactam, adipic acid, isophthalic acid, and 2-methyl-1,5-pentanediamine. It has been made industrially. However, when caprolactam or adipic acid is copolymerized, the water absorption rate is high, and it has been a problem to cause a significant decrease in physical properties under moisture absorption. On the other hand, when isophthalic acid or 2-methyl-1,5-pentanediamine is copolymerized, the crystallization speed is reduced by copolymerization while maintaining a high glass transition temperature. In some cases, crystallization does not proceed sufficiently, causing molding difficulties such as insufficient mold release, and in subsequent use, crystallization proceeds at high temperatures and deformation due to secondary shrinkage is a problem.

A copolyamide obtained by copolymerizing 6T nylon with another component in order to impart other characteristics while utilizing the characteristics of 6T nylon is also known. For example, Patent Document 1 discloses that 6I nylon is copolymerized with 6I nylon (nylon synthesized by a co-condensation polymerization reaction of hexamethylenediamine and isophthalic acid), and further 11 nylon (a monomer having 11 carbon atoms such as undecane lactam). (Nylon synthesized by polycondensation reaction) or 12 nylon (nylon synthesized by polycondensation reaction of a monomer having 12 carbon atoms such as lauryl lactam) is disclosed. This copolymerized polyamide has the advantage of being excellent in transparency, but has the disadvantage that the glass transition temperature is 130 ° C. or higher and the moldability is poor.

Patent Document 2 discloses a binary copolymer polyamide obtained by copolymerizing 12 nylon with 6T nylon. This copolymerized polyamide has the advantage of being excellent in heat resistance for a short time, impact resistance and sliding properties, but has the disadvantage of being inferior in heat aging resistance and gasoline barrier properties.

Patent Document 3 discloses a binary copolymer polyamide obtained by copolymerizing a relatively large amount of 11 nylon or 12 nylon with 6T nylon. This copolymerized polyamide has the advantages of low water absorption and excellent mechanical properties, but has the disadvantage of being inferior in moldability, heat aging resistance and gasoline barrier properties.

As described above, none of the conventionally known 6T nylons have a high degree of satisfaction with all of the three characteristics of moldability, heat aging resistance, and gasoline barrier properties while maintaining a high melting point and low water absorption. .

Japanese Examined Patent Publication No. 46-24249 JP 62-156130 A JP-A-5-310925

The present invention was devised in view of the current state of the prior art, and its purpose is to provide three types of moldability, heat aging resistance, and gasoline barrier properties in addition to a high melting point of 300 ° C. or higher and low water absorption. The object is to provide 6T nylon that satisfies all of the properties.

In order to achieve the above object, the present inventor has intensively studied the types and amounts of components copolymerized with 6T nylon, and as a result, by copolymerizing 11 nylon at a specific ratio, In addition to low water absorption, it has been found that 6T nylon that satisfies all three properties of moldability, heat aging resistance, and gasoline barrier properties can be provided, and the present invention has been completed.

That is, according to the present invention, (a) 55 to 75 mol% of a structural unit obtained from an equimolar salt of hexamethylenediamine and terephthalic acid, and (b) a composition obtained from 11-aminoundecanoic acid or undecanactam There is provided a copolyamide characterized by comprising 45 to 25 mol% of units.

According to a preferred embodiment of the present invention, the copolymer polyamide is (c) a structural unit obtained from an equimolar salt of diamine and dicarboxylic acid other than the structural unit of (a), or other than the structural unit of (b). The structural unit obtained from the aminocarboxylic acid or lactam is up to 20 mol%, the melting point (Tm) of the copolyamide is 300 to 330 ° C., and the temperature rising crystallization temperature (Tc1) is 90 to 140 ° C. is there.

In the copolymerized polyamide of the present invention, 11 nylon is copolymerized at a specific ratio with 6T nylon as a main component, and therefore, the high temperature of 300 ° C. or higher is achieved while taking advantage of the properties of 6T nylon such as mechanical properties and slidability. In addition to melting point and low water absorption, moldability, heat aging resistance, and gasoline barrier property can be highly satisfied.

Hereinafter, the copolymerized polyamide of the present invention will be described in detail. The copolymerized polyamide of the present invention contains (a) component corresponding to 6T nylon and (b) component corresponding to 11 nylon in a specific ratio, and has moldability and high water absorption which are disadvantages of 6T nylon. Is not only improved, but also has a feature of high satisfaction in heat aging resistance and gasoline barrier properties.

The component (a) corresponds to 6T nylon obtained by co-condensation polymerization of hexamethylenediamine (6) and terephthalic acid (T) in an equimolar amount, and specifically, the following formula (I) It is represented by

The component (a) is a main component of the copolymerized polyamide of the present invention, and has a role of imparting excellent heat resistance, mechanical properties, chemical resistance, slidability, gas barrier properties and the like to the copolymerized polyamide. The blending ratio of the component (a) in the copolymerized polyamide is 55 to 75 mol%, preferably 60 to 70 mol%, more preferably 62 to 68 mol%. When the blending ratio of the component (a) is less than the above lower limit, 6T nylon, which is a crystal component, is subject to crystal inhibition by the copolymerization component, which may lead to a decrease in moldability and high temperature characteristics. Since melting | fusing point becomes high too much and there exists a possibility of decomposing | disassembling at the time of a process, it is unpreferable.

The component (b) corresponds to 11 nylon obtained by polycondensation of 11-aminoundecanoic acid or undecane lactam, and is specifically represented by the following formula (II).

The component (b) is for improving the drawbacks of the component (a), and lowers the melting point and temperature rising crystallization temperature of the copolymerized polyamide to improve the moldability and reduce the water absorption rate. It has the role of improving troubles caused by changes in physical properties and dimensions during water absorption. The blending ratio of the component (b) in the copolymerized polyamide is 45 to 25 mol%, preferably 40 to 30 mol%, more preferably 38 to 32 mol%. When the blending ratio of the component (b) is less than the above lower limit, the melting point of the copolyamide is not sufficiently lowered, the moldability may be insufficient, and the effect of reducing the water absorption rate of the obtained resin is insufficient. In addition, there is a risk of instability of physical properties such as deterioration of mechanical properties at the time of water absorption. When the above upper limit is exceeded, the melting point of the copolyamide is too low, the crystallization rate is slow, the moldability may be adversely affected, and the amount of the component (a) corresponding to 6T nylon is reduced, Mechanical properties and slidability may be insufficient, which is not preferable.

The copolymerized polyamide of the present invention includes (c) a structural unit obtained from an equivalent molar salt of diamine and dicarboxylic acid other than the structural unit of (a) above, in addition to the above components (a) and (b), or the above A structural unit obtained from aminocarboxylic acid or lactam other than the structural unit of (b) may be copolymerized at a maximum of 20 mol%. The component (c) has a role of imparting other characteristics not obtainable with 6T nylon or 11 nylon to the copolymerized polyamide or further improving the characteristics obtained with 6T nylon or 11 nylon. Specifically, the following copolymerization components may be mentioned. The amine component includes 1,2-ethylenediamine, 1,3-trimethylenediamine, 1,4-tetramethylenediamine, 1,5-pentamethylenediamine, 2-methyl-1,5-pentamethylenediamine, 1,6 -Hexamethylenediamine, 1,7-heptamethylenediamine, 1,8-octamethylenediamine, 1,9-nonamethylenediamine, 2-methyl-1,8-octamethylenediamine, 1,10-decamethylenediamine, 1 , 11-Undecamethylenediamine, 1,12-dodecamethylenediamine, 1,13-tridecamethylenediamine, 1,16-hexadecamethylenediamine, 1,18-octadecamethylenediamine, 2,2,4 (or 2,4,4) -aliphatic diamines such as trimethylhexamethylenediamine, piperazine Cyclohexanediamine, bis (3-methyl-4-aminohexyl) methane, bis- (4,4'-aminocyclohexyl) methane, cycloaliphatic diamines such as isophoronediamine, metaxylylenediamine, paraxylylenediamine, para Examples thereof include aromatic diamines such as phenylenediamine and metaphenylenediamine, and hydrogenated products thereof. As the acid component of the polyamide, the following polyvalent carboxylic acids or acid anhydrides can be used. Examples of the polyvalent carboxylic acid include terephthalic acid, isophthalic acid, orthophthalic acid, 1,5-naphthalenedicarboxylic acid, 2,6-naphthalenedicarboxylic acid, 4,4′-diphenyldicarboxylic acid, and 2,2′-diphenyl. Aromatic dicarboxylic acids such as dicarboxylic acid, 4,4'-diphenyl ether dicarboxylic acid, 5-sulfonic acid sodium isophthalic acid, 5-hydroxyisophthalic acid, fumaric acid, maleic acid, succinic acid, itaconic acid, adipic acid, azelaic acid, Sebacic acid, 1,11-undecanedioic acid, 1,12-dodecanedioic acid, 1,14-tetradecanedioic acid, 1,18-octadecanedioic acid, 1,4-cyclohexanedicarboxylic acid, 1,3-cyclohexanedicarboxylic acid 1,2-cyclohexanedicarboxylic acid, 4-methyl-1,2-cyclohex Njikarubon acid, and an aliphatic or alicyclic dicarboxylic acids such as dimer acid. Further, lactams such as ε-caprolactam and 12-lauryl lactam, and aminocarboxylic acids having a structure in which they are ring-opened can be used.

Specific examples of the component (c) include polycaproamide (nylon 6), polydodecanamide (nylon 12), polytetramethylene adipamide (nylon 46), polyhexamethylene adipamide (nylon 66), polyun Decamethylene adipamide (nylon 116), polymetaxylylene adipamide (nylon MXD6), polyparaxylylene adipamide (nylon PXD6), polytetramethylene sebamide (nylon 410), polyhexamethylene sebacamide (Nylon 610), polydecamethylene adipamide (nylon 106), polydecamethylene sebamide (nylon 1010), polyhexamethylene dodecamide (nylon 612), polydecamethylene dodecamide (nylon 1012), polyhexamethylene Isophthalamide (Nai 6I), polytetramethylene terephthalamide (nylon 4T), polypentamethylene terephthalamide (nylon 5T), poly-2-methylpentamethylene terephthalamide (nylon M-5T), polyhexamethylene hexahydroterephthalamide (nylon 6T) (H)) Polynonamethylene terephthalamide (nylon 9T), polydecamethylene terephthalamide (nylon 10T), polyundecamethylene terephthalamide (nylon 11T), polydodecamethylene terephthalamide (nylon 12T), polybis (3-methyl) -4-aminohexyl) methane terephthalamide (nylon PACMT), polybis (3-methyl-4-aminohexyl) methane isophthalamide (nylon PACMI), polybis (3-methyl-4- Minohekishiru) methane dodecamide (nylon PACM12), polybis (3-methyl-4-amino-hexyl) methane tetra deca (nylon PACM14) and the like.

Among the structural units, examples of the preferred component (c) include polyhexamethylene adipamide for imparting high crystallinity to the copolymer polyamide, and polydecamethylene terephthalamide for imparting further low water absorption. And polymetaxylene adipamide for improving gasoline barrier properties. The blending ratio of the component (c) in the copolymerized polyamide is preferably up to 20 mol%, more preferably 10 to 20 mol%. When the proportion of the component (c) is less than the above lower limit, the effect of the component (c) may not be sufficiently exhibited. When the proportion exceeds the above upper limit, the amount of the essential component (a) or component (b) is small. Therefore, the originally intended effect of the copolymerized polyamide of the present invention may not be sufficiently exhibited, which is not preferable.

The copolymerized polyamide of the present invention preferably has a melting point (Tm) of 300 to 330 ° C. and a temperature rising crystallization temperature (Tc1) of 90 to 140 ° C. When Tm exceeds the above upper limit, the processing temperature required when the copolymerized polyamide is molded by an injection molding method or the like becomes extremely high, so that it may be decomposed during processing and the desired physical properties and appearance may not be obtained. On the other hand, when Tm is less than the above lower limit, the crystallization rate becomes slow, and in both cases, molding becomes difficult. Further, when Tc1 exceeds the above upper limit, not only the mold temperature required for molding the copolymer polyamide by an injection molding method becomes high and molding becomes difficult, but in a short cycle of injection molding, In some cases, crystallization does not proceed sufficiently, causing molding difficulties such as insufficient mold release, and in subsequent use, crystallization proceeds at high temperatures and deformation due to secondary shrinkage becomes a problem. Conversely, when Tc1 is less than the above lower limit, it is necessary to inevitably lower the glass transition temperature as a resin composition. Since Tc1 is generally a temperature higher than the glass transition temperature, when Tc1 is less than 90 ° C., a low value is required as the glass transition temperature. In that case, there is a large decrease in physical properties or physical properties after water absorption. Problems such as inability to maintain. Since Tg needs to be kept relatively high, Tc1 needs to be at least 90 ° C. or higher.

In the copolymerized polyamide of the present invention, a specific amount of 11 nylon components are copolymerized with 6T nylon, so that not only the properties such as high melting point and low water absorption, but also the balance of moldability, heat aging resistance, and gasoline barrier properties. An excellent resin is obtained. In molding electronic parts, in addition to a high melting point of 300 ° C. or higher and low water absorption, thin-walled, high-cycle molding is required. In the hexamethylene terephthalamide / polyhexamethylene adipamide copolymer (PA6T / 66), although the moldability is good, the water absorption is very high. Therefore, in the reflow soldering process performed by surface mounting or the like, there is a problem that blisters are generated in a molded product. On the other hand, polynonamethylene terephthalamide has low water absorption, but Tc1 may be 150 ° C. or higher, and the mold temperature at the time of molding requires 150 ° C. or higher. Even if it can be molded with a low temperature mold, secondary shrinkage due to crystallization during use becomes a problem. From the above background, a resin having a high melting point of 300 ° C. or higher, low water absorption, and easy moldability is required. In the copolymerized polyamide of the present invention, 6T nylon is copolymerized with a specific amount of 11 nylon. As a result, not only has a high melting point and low water absorption, Tc1 can be kept low, and the processability of injection molding can be greatly improved. In addition, when considering the expansion of 6T nylon to automobile parts, not only molding processability and low water absorption are required, but also heat aging resistance to the temperature in the engine room and barriers such as gasoline to prevent fuel volatilization. Sex is important. So far, an example of copolymerizing 12 nylon with 6T nylon has been reported, but 12 nylon has a smaller amount of amide bonds than 11 nylon, and it is considered that hydrogen bonds between amide bonds provide a shielding effect on gas components. And it is disadvantageous for the gasoline barrier property. In addition, 11 nylon has a structure that is easier to form hydrogen bonds than 12 nylon when it takes a zigzag structure and easily forms hydrogen bonds, whereas 12 nylon has difficulty in taking hydrogen bonds and has weak hydrogen bondability. . The improvement of hydrogen bonding property is preferable from the viewpoint of heat aging resistance and gasoline barrier property because it improves the glass transition temperature and the shielding effect of gasoline components. From the above, although 11 nylon component is a copolymer component superior to 12 nylon component and has excellent characteristics, 11 nylon has been copolymerized with 6T nylon and has a melting point of 300 ° C. No specific copolyamide has been reported.

Examples of the catalyst used for producing the copolymerized polyamide of the present invention include phosphoric acid, phosphorous acid, hypophosphorous acid or a metal salt, ammonium salt and ester thereof. Specific examples of the metal species of the metal salt include potassium, sodium, magnesium, vanadium, calcium, zinc, cobalt, manganese, tin, tungsten, germanium, titanium, and antimony. As the ester, ethyl ester, isopropyl ester, butyl ester, hexyl ester, isodecyl ester, octadecyl ester, decyl ester, stearyl ester, phenyl ester and the like can be added. Moreover, it is preferable to add sodium hydroxide from the viewpoint of improving the melt residence stability.

The relative viscosity (RV) of the copolymerized polyamide of the present invention measured at 20 ° C. in 96% concentrated sulfuric acid is 0.4 to 4.0, preferably 1.0 to 3.5, more preferably 1.5 to 3.0. Examples of a method for setting the relative viscosity of the polyamide within a certain range include a means for adjusting the molecular weight.

The copolymer polyamide of the present invention can adjust the end group amount and molecular weight of the polyamide by a method of polycondensation by adjusting the molar ratio of the amino group amount to the carboxyl group or a method of adding a terminal blocking agent. . When polycondensation is performed at a constant ratio of the molar ratio of the amino group and the carboxyl group, the molar ratio of all diamines to all dicarboxylic acids used is diamine / dicarboxylic acid = 1.00 / 1.05 to 1.10 / It is preferable to adjust to the range of 1.00.

Examples of the timing for adding the end-capping agent include starting raw materials, starting polymerization, late polymerization, or finishing polymerization. The end capping agent is not particularly limited as long as it is a monofunctional compound having reactivity with the amino group or carboxyl group at the end of the polyamide, but acid anhydrides such as monocarboxylic acid or monoamine, phthalic anhydride, Monoisocyanates, monoacid halides, monoesters, monoalcohols and the like can be used. Examples of the end capping agent include aliphatic monoacids such as acetic acid, propionic acid, butyric acid, valeric acid, caproic acid, caprylic acid, lauric acid, tridecanoic acid, myristic acid, palmitic acid, stearic acid, pivalic acid, and isobutyric acid. Alicyclic monocarboxylic acids such as carboxylic acid and cyclohexanecarboxylic acid, benzoic acid, toluic acid, α-naphthalenecarboxylic acid, β-naphthalenecarboxylic acid, methylnaphthalenecarboxylic acid, aromatic monocarboxylic acid such as phenylacetic acid, maleic anhydride Acid, phthalic anhydride, acid anhydrides such as hexahydrophthalic anhydride, methylamine, ethylamine, propylamine, butylamine, hexylamine, octylamine, decylamine, stearylamine, dimethylamine, diethylamine, dipropylamine, dibutylamine, etc. Aliphatic monoamines, Examples thereof include alicyclic monoamines such as cyclohexylamine and dicyclohexylamine; aromatic monoamines such as aniline, toluidine, diphenylamine and naphthylamine.

The acid value and amine value of the copolymerized polyamide of the present invention are preferably 0 to 200 eq / ton and 0 to 100 eq / ton, respectively. When the terminal functional group is 200 eq / ton or more, not only gelation and deterioration are promoted during melt residence, but also problems such as coloring and hydrolysis are caused in the use environment. On the other hand, when a reactive compound such as glass fiber or maleic acid-modified polyolefin is compounded, the acid value and / or amine value is preferably 5 to 100 eq / ton in accordance with the reactivity and the reactive group.

Various conventional additives for polyamide can be used for the copolymerized polyamide of the present invention. Additives include fibrous reinforcements / fillers, stabilizers, impact modifiers, flame retardants, mold release agents, slidability improvers, colorants, plasticizers, crystal nucleating agents, and copolymerized polyamides of the present invention. Are different polyamides, thermoplastic resins other than polyamide, and the like.

Examples of the fibrous reinforcing material include glass fiber, carbon fiber, metal fiber, ceramic fiber, organic fiber, whisker, etc. Among them, glass fiber is preferable. These fibrous reinforcing materials may be used not only alone but also in combination of several kinds. As the glass fibers used here, chopped strands or continuous filament fibers having a length of 0.1 mm to 100 mm can be used. As the cross-sectional shape of the glass fiber, a glass fiber having a circular cross section and a non-circular cross section can be used. As the cross-sectional shape of the glass fiber, a glass fiber having a non-circular cross-section is preferable from the viewpoint of physical properties. Non-circular cross-section glass fibers include those that are substantially elliptical, substantially oval, or substantially bowl-shaped in a cross section perpendicular to the length direction of the fiber length, and have a flatness of 1.5 to 8 It is preferable that Here, the flatness is assumed to be a rectangle with the smallest area circumscribing a cross section perpendicular to the longitudinal direction of the glass fiber, the length of the long side of the rectangle is the major axis, and the length of the short side is the minor axis. It is the ratio of major axis / minor axis. The thickness of the glass fiber is not particularly limited, but the minor axis is about 1 to 50 μm and the major axis is about 2 to 100 μm. Further, glass fibers that are chopped strands cut into fiber bundles and having a fiber length of about 1 to 20 mm can be preferably used. An optimum amount of the fibrous reinforcing material may be selected, but 0 to 250 parts by weight, preferably 20 to 150 parts by weight can be added to 100 parts by weight.

As fillers (fillers), reinforcing fillers, conductive fillers, magnetic fillers, flame retardant fillers, thermal conductive fillers and the like are listed according to purpose. Specifically, glass beads, glass flakes, glass balloons, silica, talc , Kaolin, wollastonite, mica, alumina, hydrotalcite, montmorillonite, hydroxyapatite, graphite, carbon nanotube, fullerene, zinc oxide, indium oxide, tin oxide, iron oxide, titanium oxide, magnesium oxide, aluminum hydroxide, water Magnesium oxide, red phosphorus, calcium carbonate, potassium titanate, lead zirconate titanate, barium titanate, aluminum nitride, boron nitride, zinc borate, aluminum borate, barium sulfate, magnesium sulfate, zinc sulfide, iron, aluminum, copper, Etc. The. These fillers may be used not only alone but also in combination of several kinds. Although it does not specifically limit as a shape, Needle shape, spherical shape, plate shape, an indeterminate form, etc. can be used. The optimum amount of filler may be selected, but it is possible to add 250 parts by weight or less, preferably 20 to 150 parts by weight of filler with respect to 100 parts by weight of the copolymer polyamide. Moreover, in order to improve the affinity with the polyamide resin, the fibrous reinforcing material and the filler are preferably used in combination with a coupling agent-treated or coupling agent. As the coupling agent, a silane coupling agent is used. Any of titanate coupling agents and aluminum coupling agents may be used, and among them, aminosilane coupling agents and epoxysilane coupling agents are particularly preferable.

Stabilizers include organic antioxidants such as hindered phenol antioxidants, sulfur antioxidants, phosphorus antioxidants, heat stabilizers, light stabilizers such as hindered amines, benzophenones, and imidazoles. Examples include ultraviolet absorbers, metal deactivators, and copper compounds. Copper compounds include cuprous chloride, cuprous bromide, cuprous iodide, cupric chloride, cupric bromide, cupric iodide, cupric phosphate, cupric pyrophosphate, Copper salts of organic carboxylic acids such as copper sulfide, copper nitrate, and copper acetate can be used. Further, as a component other than the copper compound, an alkali metal halide compound is preferably contained. Examples of the alkali metal halide compound include lithium chloride, lithium bromide, lithium iodide, sodium fluoride, sodium chloride, bromide. Examples thereof include sodium, sodium iodide, potassium fluoride, potassium chloride, potassium bromide, potassium iodide and the like. These additives may be used alone or in combination of several kinds. An optimum amount of the stabilizer may be selected, but 0 to 5 parts by weight can be added to 100 parts by weight of the copolymer polyamide.

The copolymerized polyamide of the present invention may be a polymer blend of a polyamide having a composition different from that of the copolymerized polyamide of the present invention. The polyamide having a composition different from that of the copolymerized polyamide of the present invention is not particularly limited, but polycaproamide (nylon 6), polyundecanamide (nylon 11), polydodecanamide (nylon 12), polytetramethylene adipamide (Nylon 46), polyhexamethylene adipamide (nylon 66), polymetaxylylene adipamide (nylon MXD6), polyparaxylylene adipamide (nylon PXD6), polytetramethylene sebacamide (nylon 410), Polyhexamethylene sebamide (nylon 610), polydecamethylene adipamide (nylon 106), polydecamethylene sebamide (nylon 1010), polyhexamethylene dodecamide (nylon 612), polydecamethylene dodecamide (nylon) 1012), Polyhe Samethylene terephthalamide (nylon 6T), polyhexamethylene isophthalamide (nylon 6I), polytetramethylene terephthalamide (nylon 4T), polypentamethylene terephthalamide (nylon 5T), poly-2-methylpentamethylene terephthalamide (nylon) M-5T), polyhexamethylene hexahydroterephthalamide (nylon 6T (H)), poly-2-methyl-octamethylene terephthalamide, polynonamethylene terephthalamide (nylon 9T), polydecamethylene terephthalamide (nylon 10T), Polyundecamethylene terephthalamide (Nylon 11T), Polydodecamethylene terephthalamide (Nylon 12T), Polybis (3-methyl-4-aminohexyl) methane terephthalamide ( Iron PACMT) polybis (3-methyl-4-aminohexyl) methane isophthalamide (nylon PACMI), polybis (3-methyl-4-aminohexyl) methane dodecamide (nylon PACM12), polybis (3-methyl-4-amino) Hexyl) methane tetradecamide (nylon PACM14), polyalkyl ether copolymerized polyamide or the like, or these copolymerized polyamides may be used alone or in combination of two or more. Among these, nylon 66, nylon 6T66, or the like may be polymer blended in order to improve the crystallization speed. The addition amount of the polyamide having a composition different from that of the copolymerized polyamide of the present invention may be selected, but 0 to 50 parts by weight can be added to 100 parts by weight of the copolymerized polyamide.

The thermoplastic polyamide of the present invention may contain a thermoplastic resin other than polyamide having a composition different from that of the copolymerized polyamide of the present invention. Polymers other than polyamide include polyphenylene sulfide (PPS), liquid crystal polymer (LCP), aramid resin, polyetheretherketone (PEEK), polyetherketone (PEK), polyetherimide (PEI), thermoplastic polyimide, polyamideimide (PAI), polyether ketone ketone (PEKK), polyphenylene ether (PPE), polyether sulfone (PES), polysulfone (PSU), polyarylate (PAR), polyethylene terephthalate, polybutylene terephthalate, polyethylene naphthalate, polybutylene Phthalate, polycarbonate (PC), polyoxymethylene (POM), polypropylene (PP), polyethylene (PE), polymethylpentene (TPX), polystyrene ( S), polymethyl methacrylate, acrylonitrile-styrene copolymer (AS), acrylonitrile-butadiene-styrene copolymer (ABS), and if compatibility is poor, add compatibilizers such as reactive compounds and block polymers Alternatively, it is important to modify a polymer other than polyamide (particularly acid modification is preferred). These thermoplastic resins can be blended in a molten state by melt kneading. However, the thermoplastic resin may be made into a fiber or particle and dispersed in the copolymerized polyamide of the present invention. An optimum amount of the thermoplastic resin may be selected, but 0 to 50 parts by weight can be added to 100 parts by weight of the copolyamide.

As impact modifiers, ethylene-propylene rubber (EPM), ethylene-propylene-diene rubber (EPDM), ethylene-acrylic acid copolymer, ethylene-acrylic acid ester copolymer, ethylene-methacrylic acid copolymer, ethylene- Polyolefin resins such as methacrylic acid ester copolymer, ethylene vinyl acetate copolymer, styrene-butadiene-styrene block copolymer (SBS), styrene-ethylene-butylene-styrene block copolymer (SEBS), styrene-isoprene -Styrene copolymer (SIS), vinyl polymer resin such as acrylate copolymer, polybutylene terephthalate or polybutylene naphthalate as hard segment, polytetramethylene glycol or polycaprolactone or poly Polyester block copolymer in which the turbo sulfonate diol as a soft segment, a nylon elastomer, urethane elastomer, silicone rubber, fluorinated rubber, and the like polymer particles having a core-shell structure constituted from two different polymers. An optimum amount of the impact modifier may be selected, but 0 to 30 parts by weight can be added to 100 parts by weight of the copolyamide.

When a thermoplastic resin other than the polyamide resin in the present invention and an impact resistance improving material are added to the copolymerized polyamide of the present invention, it is preferable that a reactive group capable of reacting with the polyamide is copolymerized. The functional group is a group capable of reacting with an amino group, a carboxyl group and a main chain amide group which are terminal groups of the polyamide resin. Specific examples include a carboxylic acid group, an acid anhydride group, an epoxy group, an oxazoline group, an amino group, an isocyanate group, etc. Among them, an acid anhydride group is most excellent in reactivity. There is also a report that the thermoplastic resin having a reactive group that reacts with the polyamide resin is finely dispersed in the polyamide and is finely dispersed, so that the distance between the particles is shortened and the impact resistance is greatly improved [ S, Wu: Polymer 26, 1855 (1985)].

As a flame retardant, a combination of a halogen flame retardant and a flame retardant aid is good. As a halogen flame retardant, brominated polystyrene, brominated polyphenylene ether, brominated bisphenol type epoxy polymer, brominated styrene maleic anhydride Polymers, brominated epoxy resins, brominated phenoxy resins, decabromodiphenyl ether, decabromobiphenyl, brominated polycarbonate, perchlorocyclopentadecane, brominated cross-linked aromatic polymers, etc. are preferred. Antimony compounds such as antimony, antimony pentoxide, and sodium antimonate, and zinc stannate are preferred. Among these, a combination of dibromopolystyrene and sodium antimonate and / or zinc stannate is preferable from the viewpoint of thermal stability. Non-halogen flame retardants include melamine cyanurate, red phosphorus, phosphinic acid metal salts, and nitrogen-containing phosphoric acid compounds. In particular, a combination of a phosphinic acid metal salt and a nitrogen-containing phosphoric acid compound is preferable. Examples of the nitrogen-containing phosphoric acid compound include melamine, a condensate of melamine such as melam and melon, and a reactive organism of polyphosphoric acid or those. A mixture of At that time, addition of a hydrotalcite-based compound is preferable for preventing metal corrosion of a mold or the like. Other flame retardants and flame retardant aids include zinc borate, zinc sulfide, molybdenum compounds, iron oxide, aluminum hydroxide, magnesium hydroxide, silicone resin, fluororesin, montmorillonite, silica, metal carbonate, etc. It is done. The optimum amount of the flame retardant may be selected, but 0 to 50 parts by weight can be added to 100 parts by weight of the copolymer polyamide.

Examples of the release agent include long chain fatty acids or esters thereof, metal salts, amide compounds, polyethylene wax, silicone, polyethylene oxide, and the like. The long chain fatty acid preferably has 12 or more carbon atoms, and examples thereof include stearic acid, 12-hydroxystearic acid, behenic acid, and montanic acid. Partial or total carboxylic acid is esterified with monoglycol or polyglycol. Or a metal salt may be formed. Examples of the amide compound include ethylene bisterephthalamide and methylene bisstearyl amide. These release agents may be used alone or as a mixture. The addition amount of the release material may be selected as an optimum amount, but 0 to 5 parts by weight can be added to 100 parts by weight of the copolymer polyamide.

Examples of the sliding property improving material include high molecular weight polyethylene, acid-modified high molecular weight polyethylene, fluorine resin powder, molybdenum disulfide, silicone resin, silicone oil, zinc, graphite, mineral oil, and the like. The resin slidability improving material can be added in a range not impairing the characteristics of the present invention, for example, 0.05 to 3 parts by weight.

The copolymerized polyamide of the present invention can be produced by a conventionally known method. For example, hexamethylene diamine and terephthalic acid which are raw material monomers of component (a), and 11- Aminoundecanoic acid or undecanactactam, and if necessary (c) a structural unit obtained from an equimolar salt of a diamine other than the structural unit of (a) and a dicarboxylic acid, an aminocarboxylic acid other than the structural unit of (b) or It can be easily synthesized by co-condensation of lactam. The order of the copolycondensation reaction is not particularly limited, and all the raw material monomers may be reacted at once, or a part of the raw material monomers may be reacted first, followed by the remaining raw material monomers. The polymerization method is not particularly limited, but from raw material charging to polymer production may proceed in a continuous process, and after producing an oligomer once, the polymerization is advanced by an extruder or the like in another process, or the oligomer is solidified. A method of increasing the molecular weight by phase polymerization may be used. By adjusting the charging ratio of the raw material monomer, the proportion of each structural unit in the copolymerized polyamide to be synthesized can be controlled.

Hereinafter, the present invention will be described more specifically with reference to examples, but the present invention is not limited to these examples. In addition, the measured value described in the Example is measured by the following method.

(1) Relative viscosity 0.25 g of polyamide resin was dissolved in 25 ml of 96% sulfuric acid and measured at 20 ° C. using an Ostwald viscometer.

(2) Amount of terminal amino groups 0.2 g of polyamide resin was dissolved in 20 ml of m-cresol and titrated with a 0.1 mol / l hydrochloric acid ethanol solution. Cresol red was used as the indicator. Expressed as equivalents (eq / ton) in 1 ton of resin.

(3) Melting point (Tm) and temperature rising crystallization temperature (Tc1)
10 mg of the polyamide dried under reduced pressure at 105 ° C. for 15 hours was weighed in an aluminum pan (TA Instruments, product number 900793.901) and sealed with an aluminum lid (TA Instruments, product number 900794.901). After preparing the sample, use a differential scanning calorimeter DSCQ100 (manufactured by TA INSTRUMENTS) to raise the temperature from room temperature to 20 ° C./min, hold at 350 ° C. for 3 minutes, take out the measurement sample pan, soak in liquid nitrogen, and quench rapidly I let you. Thereafter, the sample was taken out from liquid nitrogen and allowed to stand at room temperature for 30 minutes, and then again heated from room temperature at 20 ° C./minute using a differential scanning calorimeter DSCQ100 (manufactured by TA INSTRUMENTS) and held at 350 ° C. for 3 minutes. . At that time, the peak temperature of the crystallization exotherm at the time of temperature rise was defined as the crystallization temperature at the time of temperature rise (Tc1), and the endothermic peak temperature due to melting was defined as the melting point (Tm).

(4) Formability Using an injection molding machine EC-100 manufactured by Toshiba Machine, the cylinder temperature was set to the melting point of the resin + 20 ° C. As the mold, a mold for producing a flat plate having a length of 100 mm, a width of 100 mm, and a thickness of 1 mm was used. The mold temperature was set to 140 ° C., molding was performed at an injection speed of 50 mm / sec, a holding pressure of 30 MPa, an injection time of 10 seconds, and a cooling time of 10 seconds. The moldability was evaluated as follows.
○: Significant decomposition of the resin is not observed, and a molded product can be obtained without any problem.
X: Foaming due to decomposition is accompanied at the time of molding, or the releasability is insufficient, and the molded product sticks to the mold or deforms.

(5) Heat aging resistance For the heat aging resistance test, a compound obtained by compounding 0.02 part of cupric bromide and 0.15 part of potassium iodide to 100 parts of polyamide and using an injection molding machine for ISO. A dumbbell-shaped test piece based on the above was prepared. The molded product was subjected to a heat aging test for 1000 hours in a 160 ° C. gear oven, and a tensile test was performed according to ISO 527. The quality of heat aging resistance was evaluated according to the following criteria.
○: Retention rate of tensile strength or tensile yield strength after 1000 hours at 160 ° C. is 90% or more ×: Retention rate of tensile strength or tensile yield strength after 1000 hours at 160 ° C. is less than 90%

(6) Gasoline barrier property For the evaluation of gasoline barrier property, a fuel permeability test by the cup method was conducted. 4.6 g of fuel composed of 45/45/10 vol% of isooctane / toluene / ethanol was added to the cup. For the fuel permeability measurement, the polyamide of the present invention prepared on a film having a thickness of 100 μm by a heat press was used. The obtained film was placed on the cup to which the fuel was added so as not to contact the fuel (vapor phase method). Airtightness was maintained so that the fuel would not volatilize except from permeation through the film. The measurement was performed with a permeation area of 1.133 × 10 ⁻³ m ² , a test temperature of 60 ° C., and a test time of 240 hours, and the weight change before and after the measurement was measured. In addition, a blank experiment for taking into account the water absorption / release characteristics of the sample was performed and corrected to calculate the fuel permeation amount. Gasoline barrier properties were evaluated based on the following criteria.
○: Weight reduction amount is less than 100 mg ×: Weight reduction amount is 100 mg or more

(7) Saturated water absorption For evaluation of the saturated water absorption, a flat plate having a length of 100 mm, a width of 100 mm, and a thickness of 1 mm was prepared, immersed in 80 ° C. hot water, and obtained from the following formula.
Saturated water absorption (%) = (weight at saturated water absorption−weight at drying) / weight at drying × 100

<Example 1>
Hexamethylenediamine 7.54 kg, terephthalic acid 10.79 kg, 11-aminoundecanoic acid 7.04 kg, sodium diphosphite 9 g, terminal regulator 40 g acetic acid and 17.52 kg ion-exchanged water in a 50 liter autoclave The pressure was charged with N ₂ from normal pressure to 0.05 MPa, the pressure was released, and the pressure was returned to normal pressure. This operation was performed 3 times, N ₂ substitution was performed, and then uniform dissolution was performed at 135 ° C. and 0.3 MPa with stirring. Thereafter, the solution was continuously supplied by a liquid feed pump, heated to 240 ° C. with a heating pipe, and heated for 1 hour. Thereafter, the reaction mixture was supplied to the pressurized reaction can, heated to 290 ° C., and a part of water was distilled off so as to maintain the internal pressure of the can at 3 MPa to obtain a low-order condensate. Thereafter, this low-order condensate is directly supplied to a twin-screw extruder (screw diameter: 37 mm, L / D = 60) while maintaining the molten state, and the resin temperature is 330 ° C. while water is removed from three vents. Polycondensation proceeded under melting to obtain a copolymerized polyamide. Table 1 shows the charge ratio of raw material monomers and the characteristics of the obtained copolymer polyamide.

<Example 2>
The amount of hexamethylenediamine was changed to 8.12 kg, the amount of terephthalic acid was changed to 11.62 kg, the amount of 11-aminoundecanoic acid was changed to 6.03 kg, and the resin temperature of the twin screw extruder was 335 ° C. Changed to A copolymerized polyamide was synthesized in the same manner as in Example 1 except for these. Table 1 shows the charge ratio of raw material monomers and the characteristics of the obtained copolymer polyamide.

<Example 3>
In the same manner as in Example 1, except that the amount of hexamethylenediamine was changed to 6.96 kg, the amount of terephthalic acid was changed to 9.96 kg, and the amount of 11-aminoundecanoic acid was changed to 8.04 kg. Polymerized polyamide was synthesized. Table 1 shows the charge ratio of raw material monomers and the characteristics of the obtained copolymer polyamide.

<Example 4>
The amount of hexamethylenediamine was changed to 8.12 kg, the amount of terephthalic acid was changed to 9.96 kg, the amount of 11-aminoundecanoic acid was changed to 6.03 kg, and adipic acid (dicarboxylic acid other than terephthalic acid) A copolymerized polyamide was synthesized in the same manner as in Example 1 except that 1.46 kg was charged. Table 1 shows the charge ratio of raw material monomers and the characteristics of the obtained copolymer polyamide.

<Example 5>
A copolymerized polyamide was synthesized in the same manner as in Example 1 except that 7.04 kg of 11-aminoundecanoic acid was changed to 6.41 kg of undecane lactam. Table 1 shows the charge ratio of raw material monomers and the characteristics of the obtained copolymer polyamide.

<Comparative Example 1>
The amount of hexamethylenediamine was changed to 9.28 kg, the amount of terephthalic acid was changed to 13.28 kg, the amount of 11-aminoundecanoic acid was changed to 4.02 kg, and the resin temperature of the twin screw extruder was 350 ° C. Changed to A copolymerized polyamide was synthesized in the same manner as Example 1 except for these. Table 1 shows the charge ratio of raw material monomers and the characteristics of the obtained copolymer polyamide.

<Comparative Example 2>
In the same manner as in Example 1, except that the amount of hexamethylenediamine was changed to 5.22 kg, the amount of terephthalic acid was changed to 7.47 kg, and the amount of 11-aminoundecanoic acid was changed to 11.06 kg. Polymerized polyamide was synthesized. Table 1 shows the charge ratio of raw material monomers and the characteristics of the obtained copolymer polyamide.

<Comparative Example 3>
A copolymer polyamide was synthesized in the same manner as in Example 1 except that 7.44 kg of 11-aminoundecanoic acid was changed to 7.53 kg of 12-aminododecanoic acid. Table 1 shows the charge ratio of raw material monomers and the characteristics of the obtained copolymer polyamide.

<Comparative Example 4>
A copolymerized polyamide was synthesized in the same manner as in Example 1 except that 10.18 kg of hexamethylenediamine and 14.56 kg of terephthalic acid were used without using 11-aminoundecanoic acid. The synthesized polyamide had a decreased fluidity at the polymerization stage, and a polymer could not be obtained.

As is apparent from Table 1, the copolymer polyamides of Examples 1 to 5 highly satisfy all three characteristics of moldability, heat aging resistance, and gasoline barrier properties. Among these, Example 1 is most preferable in consideration of a balance between a high melting point, moldability (a lot of 6T components and Tc1 is preferably 140 ° C. or less), and a low water absorption (a lot of 11 components are better). On the other hand, the copolymerized polyamide of Comparative Example 1 in which the copolymerization amount of 11 nylon was too small had high Tm and Tc1, and was difficult to release. 11 The copolymerized polyamide of Comparative Example 2 with too much copolymerization of nylon has a low Tm, and the crystallization of the 6T component is inhibited by the aminoundecane component and the crystallinity is insufficient. It was inferior. Further, the copolymerized polyamide of Comparative Example 3 in which 12 nylon is copolymerized instead of 11 nylon is inferior in heat aging resistance and gasoline barrier property as compared with the copolymerized polyamide copolymerized with 11 nylon. Since the polyamide of Comparative Example 4 consisting only of 6T nylon had extremely high Tm and Tc1, the fluidity decreased at the polymerization stage, and a polymer could not be obtained.

In the copolymerized polyamide of the present invention, 11 nylon is copolymerized at a specific ratio with 6T nylon as a main component, and therefore, the high-melting point of 300 ° C. or higher, mechanical properties, slidability, etc. are utilized. On the other hand, low water absorption, moldability, heat aging resistance, and gasoline barrier properties can also be highly satisfied, so that it can be suitably used as molding materials and sliding materials for automobiles and electronic parts.

Claims

(A) Constituting units 55 to 75 mol% obtained from an equimolar molar salt of hexamethylenediamine and terephthalic acid, and (b) 45 to 25 mol% constituent units obtained from 11-aminoundecanoic acid or undecane lactam. Copolyamide characterized by that.
The copolymerized polyamide is obtained from (c) a structural unit obtained from an equivalent molar salt of a diamine other than the structural unit of (a) and a dicarboxylic acid, or an aminocarboxylic acid or lactam other than the structural unit of (b). The copolymerized polyamide according to claim 1, comprising up to 20 mol% of structural units.
The copolymerized polyamide according to claim 1 or 2, wherein the copolymerized polyamide has a melting point (Tm) of 300 to 330 ° C, and a temperature rising crystallization temperature (Tc1) of 90 to 140 ° C.