Patent Application
20140342145
The present invention relates to molded products formed by molding polyamide resin compositions. Specifically, it relates to molded products having high chemical resistance, low water absorption rate and high dimensional stability. It also relates to processes for preparing such molded products.
Polyamide resins generally show excellent mechanical properties such as strength, impact resistance and abrasion resistance as well as high heat resistance and also show good impact resistance so that they are widely used in the fields of electrical/electronic equipment parts, automotive parts, office automation equipment parts, various machine parts, construction materials/housing equipment parts and the like.
Among others, aliphatic polyamide resins such as polyamide 6 and polyamide 66 are widely used as versatile engineering plastics because of their excellent properties and the ease of molding.
However, molded products formed by molding aliphatic polyamide resins have the disadvantages that they show high water absorption (hygroscopy) and low chemical resistance. Specifically, some of molded products formed by molding aliphatic polyamide resins are known to absorb about 5% by mass of water based on the total mass. In molded products formed from polyamide 66, the elastic modulus possibly causes decrease from about 3 GPa to less than 1 GPa upon water absorption. Further, most importantly, molded products of aliphatic polyamide resins have the disadvantage that they show low chemical resistance, and especially they suffer a significant weight loss resulting in a significant loss in strength and elastic modulus in the presence of an acid or alkali or the like.
In addition, molded products obtained by molding aliphatic polyamide resins also have the disadvantage that they show low dimensional stability. Especially, aliphatic polyamide resins are crystalline resins so that the resulting molded products undergo considerable dimensional changes or warpage, which may impair assembling with or fitting to other parts especially in molded products that are becoming increasingly thinner and smaller such as chassis. The molded products thus obtained also had the disadvantage that they were poor in dimensional stability for use as precision parts because they swelled or deformed when they absorbed moisture.
To compensate the disadvantages of molded products using such crystalline aliphatic polyamide resins, proposals have been made to use them in combination with semi-crystalline polyamide resins.
For example, patent document 1 proposes using a polyamide resin composition comprising (A) a polycaproamide resin or a polyhexamethylene adipamide resin, (B) a semi-aromatic polyamide resin derived from an aliphatic diamine with isophthalic acid and terephthalic acid, (C) an inorganic filler and (D) a saturated aliphatic carboxylic acid. Further, patent document 2 proposes using a polyamide resin composition comprising (A) an aliphatic polyamide resin, (B) a semi-aromatic polyamide resin, (C) an inorganic filler and (D) an oxanilide stabilizer, and mentions specific examples of the semi-aromatic polyamide resin including polyamide resins derived from m- or p-xylylenediamine with adipic acid, and polyamide resins derived from hexamethylenediamine with iso- and terephthalic acids.
However, the polyamide resin compositions proposed in these documents improved in water absorption, but their chemical resistance and dimensional stability during molding were not always sufficient and needed further improvements.
Further, it has been known that biaxially oriented films are made from a resin composition comprising an aliphatic polyamide resin and a polyamide resin synthesized from m-xylylenediamine and a dicarboxylic acid such as sebacic acid (patent document 3). However, films are different from molded products used as machine parts and the like because they have a thickness as small as 0.25 mm or less.
On the other hand, a resin composition comprising a polyamide resin synthesized from m-xylylenediamine and sebacic acid as well as a little amount of an aliphatic polyamide resin has been known (patent document 4). Such a composition was excellent in water absorption and chemical resistance, but sometimes poor in crystallinity.
Patent document 1: JP-A H3-269056;
Patent document 2: JP-A2010-189467;
Patent document 3: JP-A S48-54176;
Patent document 4: JP-A S63-137955.
An object of the present invention is to solve the problems of the prior art described above and to provide molded products showing low water absorption, high chemical resistance, high crystallinity index and high dimensional stability while retaining the excellent mechanical properties and the like intrinsic to aliphatic polyamide resins. Another object is to prepare molded products of aliphatic polyamide resins showing low water absorption, high chemical resistance and high crystallinity index with high dimensional stability.
As a result of careful studies to attain the above objects, we surprisingly found that molded products showing remarkably reduced water absorption, high chemical resistance, e.g., a reduced weight loss and therefore a remarkably reduced loss in strength and elastic modulus in the presence of an acid or alkali, as well as high crystallinity index can be obtained while retaining the excellent mechanical properties and the like intrinsic to aliphatic polyamides when they are formed by using a polyamide resin composition comprising (A) an aliphatic polyamide resin and a specific proportion in the range of 1 to 50% by mass of (B) a polyamide resin derived from a diamine including 70 mol % of xylylenediamine and a dicarboxylic acid including 50 mol % or more of sebacic acid.
Specifically, the problems described above were solved by the means shown below in [1], preferably [2] to [9].
[1] A molded product formed from a polyamide resin composition containing 50 to 99 parts by mass of (A) an aliphatic polyamide resin and 50 to 1 parts by mass of (B) a polyamide resin including 70 mol % or more of a diamine structural unit derived from xylylenediamine and 50 mol % or more of a dicarboxylic acid structural unit derived from sebacic acid, provided that the total of (A) and (B) is 100 parts by mass.
[2] The molded product according to [1], wherein the aliphatic polyamide resin (A) is polyamide 6 or polyamide 66.
[3] The molded product according to [1] or [2], wherein the xylylenediamine is m-xylylenediamine, p-xylylenediamine or a mixture thereof.
[4] The molded product according to anyone of [1] to [3], wherein the polyamide resin (B) is a poly(m-xylylene sebacamide) resin, a poly(p-xylylene sebacamide) resin, or a poly(m-/p-xylylene sebacamide) resin.
[5] The molded product according to any one of [1] to [4], wherein the polyamide resin composition further contains 1 to 230 parts by mass of (C) a filler per 100 parts by mass of the total of the polyamide resin (A) and the polyamide resin (B).
[6] The molded product according to any one of [1] to [5], which has a thinnest part having thickness of 0.5 mm or more.
[7] The molded product according to anyone of [1] to [6], wherein the amount of the polyamide resin (B) contained in the polyamide resin composition is 20 to 50 parts by mass per 100 parts by mass of the total of (A) and (B).
[8] The molded product according to any one of [1] to [7], which is, formed by any one of injection molding, compression molding, vacuum molding, press molding and direct blow molding.
[9] A process for preparing a molded product, comprising molding a polyamide resin composition containing 50 to 99 parts by mass of (A) an aliphatic polyamide resin and 50 to 1 parts by mass of (B) a polyamide resin including 70 mol % or more of a diamine structural unit derived from xylylenediamine and 50 mol % or more of a dicarboxylic acid structural unit derived from sebacic acid (provided that the total of (A) and (B) is 100 parts by mass) by any one of injection molding, compression molding, vacuum molding, press molding and direct blow molding.
The present invention made it possible to provide molded products having high chemical resistance, low water absorption, high crystallinity index, and high dimensional stability.
The present invention will now be explained in detail below. As used herein, the term “to” between two values means to include the values indicated before and after it as lower and upper limits unless otherwise specified.
Molded products formed by molding polyamide resin compositions according to the present invention (hereinafter sometimes referred to as “molded products of the present invention”) are obtained by molding a polyamide resin composition comprising 50 to 99 parts by mass of (A) an aliphatic polyamide resin and 50 to 1 parts by mass of (B) a polyamide resin including 70 mol % or more of a diamine structural unit derived from xylylenediamine and 50 mol % or more of a dicarboxylic acid structural unit derived from sebacic acid, provided that the total of (A) and (B) is 100 parts by mass.
[(A) Aliphatic Polyamide Resin]
The aliphatic polyamide resin (A) used in the present invention is an aliphatic polyamide resin obtained by polycondensing a lactam containing three or more ring members, a polymerizable ω-amino acid or an aliphatic dicarboxylic acid with an aliphatic diamine or the like.
As used herein, the term “aliphatic” means to also include alicyclic compounds.
Such lactams include, for example, amino acids such as 6-aminocaproic acid, 11-aminoundecanoic acid, 12-aminododecanoic acid and the like; ε-caprolactam, ω-laurolactam and the like. ω-Amino acids include ε-aminocaproic acid, 7-aminoheptanoic acid, 9-aminononanoic acid, 11-aminoundecanoic acid, 12-aminododecanoic acid and the like.
Further, aliphatic dicarboxylic acids include, for example, aliphatic dicarboxylic acids such as oxalic acid, malonic acid, succinic acid, glutaric acid, adipic acid, pimelic acid, suberic acid, azelaic acid, sebacic acid, undecanoic diacid, dodecanoic diacid, brassylic acid, tetradecanoic diacid, pentadecanoic diacid and octadecanoic diacid; and alicyclic dicarboxylic acids such as cyclohexanedicarboxylic acid.
Further, aliphatic diamines include, for example, aliphatic diamines such as ethylenediamine, 1,3-diaminopropane, 1,4-diaminobutane, 1,5-diaminopentane (pentamethylene diamine), 1,6-diaminohexane, 1,7-diaminoheptane, 1,8-diaminooctane, 1,9-diaminononane, 1,10-diaminodecane, 1,11-diaminoundecane, 1,12-diaminododecane, 1,13-diaminotridecane, 1,14-diaminotetradecane, 1,15-diaminopentadecane, 1,16-diaminohexadecane, 1,17-diaminoheptadecane, 1,18-diaminooctadecane, 1,19-diaminononadecane, 1,20-diaminoeicosane and 2-methyl-1,5-diaminopentane; and alicyclic diamines such as cyclohexanediamine.
Specifically, aliphatic polyamide resins (A) preferably include polyamide 4, polyamide 6, polyamide 46, polyamide 7, polyamide 8, polyamide 11, polyamide 12, polyamide 66, polyamide 69, polyamide 610, polyamide 611, polyamide 612, polyamide 6/66, polyamide 6/12 and the like. These may be used in combination. Among others, especially preferred aliphatic polyamide resins (A) include polyamide 6, polyamide 66, and polyamide 6/66.
The aliphatic polyamide resin (A) preferably has a number average molecular weight (Mn) of 5,000 to 50,000. If the average molecular weight is too low, the mechanical strength of the resulting resin composition tends to be insufficient, but if it is too high, its moldability tends to decrease. More preferably, those having a number average molecular weight of 10,000 to 35,000 are used, most preferably 20,000 to 29,000.
[(B) Polyamide Resin]
The polyamide resin (B) used in the present invention is a polyamide resin composed of a diamine structural unit (a structural unit derived from a diamine) and a dicarboxylic acid structural unit (a structural unit derived from a dicarboxylic acid) wherein 70 mol % or more of the diamine structural unit is derived from xylylenediamine and 50 mol % or more of the dicarboxylic acid structural unit is derived from sebacic acid.
The polyamide resin (B) is obtained by polycondensing a diamine component including 70 mol % or more, preferably 80 mol % or more of xylylenediamine with a dicarboxylic acid component including 50 mol % or more, preferably 70 mol % or more, more preferably 80 mol % or more of sebacic acid.
If xylylenediamine here is less than 70 mol %, the polyamide resin composition finally obtained will be insufficient in barrier properties, while if sebacic acid is less than 50 mol %, the polyamide resin composition forming the molded products of the present invention will be hard so that moldability decreases.
The xylylenediamine used is preferably m-xylylenediamine, p-xylylenediamine or a mixture thereof. When the mixture is used, any mixing ratio can be used, but the mixture is preferably composed of 0 to 50 mol % of m-xylylenediamine and 50 to 100 mol % of p-xylylenediamine if more importance is attached to heat resistance, while it is preferably composed of 50 to 100 mol % of m-xylylenediamine and 0 to 50 mol % of p-xylylenediamine if more importance is attached to moldability.
Examples of diamines other than xylylenediamine may include aliphatic diamines such as tetramethylenediamine, pentamethylenediamine, 2-methylpentanediamine, hexamethylenediamine, heptamethylenediamine, octamethylenediamine, nonamethylenediamine, decamethylenediamine, dodecamethylenediamine, 2,2,4-trimethylhexamethylenediamine, and 2,4,4-trimethylhexamethylenediamine; alicyclic diamines such as 1,3-bis(aminomethyl)cyclohexane, 1,4-bis(aminomethyl)cyclohexane, 1,3-diaminocyclohexane, 1,4-diaminocyclohexane, bis(4-aminocyclohexyl)methane, 2,2-bis(4-aminocyclohexyl)propane, bis(aminomethyl)decalin (including structural isomers thereof), and bis(aminomethyl)tricyclodecane (including structural isomers thereof); diamines having an aromatic ring such as bis(4-aminophenyl)ether, p-phenylenediamine, and bis(aminomethyl)naphthalene (including structural isomers thereof) and the like; and they can be used alone or as a mixture of two or more of them.
When a diamine other than xylylenediamine is used as a diamine component, it should be used at a proportion of less than 30 mol %, preferably 1 to 25 mol %, especially preferably 5 to 20 mol % of the diamine structural unit.
Sebacic acid is used at a proportion of 50 mol % or more, preferably 70 mol % or more, more preferably 80 mol % or more of the dicarboxylic acid structural unit. The proportion of the sebacic acid component is preferably higher because compatibility with the aliphatic polyamide resin (A) tends to improve.
Dicarboxylic acid components other than sebacic acid that can be used preferably include straight chain aliphatic α,ω-dicarboxylic acids containing 4 to 20 carbon atoms excluding sebacic acid, examples of which include, for example, aliphatic dicarboxylic acids such as adipic acid, succinic acid, glutaric acid, pimelic acid, suberic acid, azelaic acid, undecanoic diacid, and dodecanoic diacid; and they can be used alone or as a mixture of two or more of them.
If a straight chain aliphatic α,ω-dicarboxylic acid excluding sebacic acid is to be used, it is preferably adipic acid or succinic acid, especially adipic acid.
Aromatic dicarboxylic acids can also be used as dicarboxylic acid components other than sebacic acid, and examples include phthalic acid compounds such as isophthalic acid, terephthalic acid and orthophthalic acid; isomeric naphthalenedicarboxylic acids such as 1,2-naphthalenedicarboxylic acid, 1,3-naphthalenedicarboxylic acid, 1,4-naphthalenedicarboxylic acid, 1,5-naphthalenedicarboxylic acid, 1,6-naphthalenedicarboxylic acid, 1,7-naphthalenedicarboxylic acid, 1,8-naphthalenedicarboxylic acid, 2,3-naphthalenedicarboxylic acid, 2,6-naphthalenedicarboxylic acid and 2,7-naphthalenedicarboxylic acid and the like; and they can be used alone or as a mixture of two or more of them. Further, these can also be used in combination with monocarboxylic acids such as benzoic acid, propionic acid and butyric acid; polycarboxylic acids such as trimellitic acid and pyromellitic acid; carboxylic anhydrides such as trimellitic anhydride and pyromellitic anhydride and the like.
If a dicarboxylic acid other than the straight chain aliphatic α,ω-dicarboxylic acids containing 4 to 20 carbon atoms is to be used as a dicarboxylic acid component other than sebacic acid, it is preferably isophthalic acid because of the moldability and barrier properties. The proportion of isophthalic acid is preferably less than 30 mol %, more preferably in the range of 1 to 25 mol %, especially preferably 5 to 20 mol % of the dicarboxylic acid structural unit.
Especially preferred polyamide resins (B) are poly(m-xylylene sebacamide) resins derived from m-xylylenediamine with sebacic acid, poly(p-xylylene sebacamide) resins derived from p-xylylenediamine with sebacic acid, and poly(m-/p-xylylene sebacamide) resins derived from m-xylylenediamine and p-xylylenediamine with sebacic acid.
The melting point of the polyamide resin (B) is preferably in the range of 150 to 310° C., more preferably 160 to 300° C., even more preferably 170 to 290° C. The melting point is preferably in the above ranges because its processability tends to improve. The glass transition point of the polyamide resin (B) is preferably in the range of 50 to 130° C. The glass transition point is preferably in the above range because its barrier properties tend to improve.
As used herein, the melting point and glass transition point of the aliphatic polyamide resin (A) and polyamide resin (B) refer to the melting point and glass transition point that can be determined by differential scanning calorimetry (DSC) by melting a sample by heating it once to eliminate the influence of thermal history on crystallinity and then heating it again. Specifically, a test sample is, for example, melted by heating from 30° C. to a temperature equal to or higher than an expected melting point at a rate of 10° C./min, then held at that temperature for 2 minutes and then cooled to 30° C. at a rate of 20° C./min. Then, the sample is heated to a temperature equal to or higher than the melting point at a rate of 10° C./min, whereby the melting point and glass transition point can be determined.
The polyamide resin (B) also preferably has a terminal amino group concentration of less than 100 μeq/g, more preferably 5 to 75 μeq/g, even more preferably 10 to 50 μeq/g and preferably has a terminal carboxyl group concentration of less than 100 μeq/g, more preferably 10 to 90 μeq/g, even more preferably 10 to 50 μeq/g.
The polyamide resin (B) also preferably has a relative viscosity of 1.7 to 4, more preferably 1.9 to 3.8 as determined at a resin concentration of 1 g/100 cc in 96% sulfuric acid at a temperature of 25° C.
Further, the number average molecular weight of the polyamide resin (B) is preferably 6,000 to 50,000, more preferably 10,000 to 43,000. When it is in the above ranges, its mechanical strength and moldability improve.
The polyamide resin (B) is composed of a diamine component including 70 mol % or more of xylylenediamine and a dicarboxylic acid component including 50 mol % or more of sebacic acid, and it is prepared by using any of previously known processes and polymerization conditions including, but not specifically limited to, atmospheric pressure melt polymerization, high pressure melt polymerization and the like.
For example, it is prepared by heating a polyamide salt composed of xylylenediamine and sebacic acid in the presence of water under pressure to polymerize it in the molten state while removing the water added and condensed water. It may also be prepared by directly adding xylylenediamine to sebacic acid in the molten state to polycondense them at atmospheric pressure. In the latter case, polycondensation proceeds by continuously adding xylylenediamine while heating the reaction system to a reaction temperature equal to or higher than the melting points of the produced oligoamide and polyamide to prevent the reaction system from solidifying.
When the polyamide resin (B) is to be obtained by polycondensation, the polycondensation reaction system may be supplied with lactams such as ε-caprolactam, ω-laurolactam and ω-enantolactam; amino acids such as 6-aminocaproic acid, 7-aminoheptanoic acid, 11-aminoundecanoic acid, 12-aminododecanoic acid, 9-aminononanoic acid and p-aminomethylbenzoic acid and the like so far as the performance is not affected.
The polyamide resin (B) can also be used after it is further heat-treated to increase the melt viscosity.
Heat treatment methods include, for example, gently heating in the presence of water in an inert gas atmosphere or under reduced pressure using a batch heater such as a rotating drum to induce crystallization while avoiding fusion, and then further heating; or heating in an inert gas atmosphere using a groove stirrer/heater to induce crystallization, and then heating in an inert gas atmosphere using a heater in the form of a hopper; or using a groove stirrer/heater to induce crystallization, and then heating with a batch heater such as a rotating drum.
Among others, the method using a batch heater for crystallization and heat treatments is preferred. Preferred conditions for crystallization treatment are as follows: heating a polyamide resin obtained by melt polymerization to 70 to 120° C. over 0.5 to 4 hours in the presence of 1 to 30% by mass of water to crystallize it, then heating the crystallized resin at a temperature in the range of [the melting point of the polyamide resin obtained by melt polymerization minus 50° C.] to [the melting point of the polyamide resin obtained by melt polymerization minus 10° C.] for 1 to 12 hours in an inert gas atmosphere or under reduced pressure.
[Combination of (A) an Aliphatic Polyamide Resin and (B) a Polyamide Resin]
Polyamide resin compositions forming the molded products of the present invention comprise 50 to 99 parts by mass of (A) an aliphatic polyamide resin and 50 to 1 parts by mass of (B) a polyamide resin per 100 parts by mass of the total of the aliphatic polyamide resin (A) and the polyamide resin (B), and such ranges allow water absorption to be reduced and chemical resistance and dimensional stability to be improved. If the polyamide resin (B) exceeds 50 parts by mass, flexibility decreases. The maximum amount of the polyamide resin (B) should preferably be less than 50 parts by mass, more preferably 45 parts by mass or less, even more preferably 40 parts by mass or less, especially 35 parts by mass or less, while the minimum amount should preferably be 3 parts by mass or more, more preferably 5 parts by mass or more, even more preferably 10 parts by mass or more, especially 20 parts by mass or more. Further, the difference between the melting points of the aliphatic polyamide resin (A) and the polyamide resin (B) is preferably more than 50° C. Although the underlying mechanism has been so far unknown, there is a tendency that molding shrinkage can be reduced by selecting a partner polyamide resin (B) so that the difference in melting point may be 50° C. or more even if the same aliphatic polyamide resin (A) is used. In the present invention, the difference between the melting points of the aliphatic polyamide resin (A) and the polyamide resin (B) is more preferably more than 50° C. and 80° C. or less.
[(C) Filler]
Polyamide resin compositions forming the molded products of the present invention preferably contain (C) a filler, and the filler (C) is not specifically limited so far as it is one of those conventionally used in this type of compositions, and inorganic fillers in the form of powders, fibers, granules and platelets as well as resin fillers or natural fillers can preferably be used.
Fillers in the form of powders and granules that can be used preferably have a particle size of 100 μm or less, more preferably 80 μm or less, and include kaolinite, silica; carbonates such as calcium carbonate and magnesium carbonate; sulfates such as calcium sulfate and magnesium sulfate; alumina, glass beads, carbon black, sulfides and metal oxides and the like. Fillers in the form of fibers that can be used include glass fibers, whiskers of potassium titanate or calcium sulfate, wollastonite, carbon fibers, mineral fibers, and alumina fibers and the like. Fillers in the form of platelets include glass flakes, mica, talc, clay, graphite, sericite and the like.
Resin fillers include liquid crystalline aromatic polyester resins, wholly aromatic polyamide resins, acrylic fibers, poly(benzimidazole) fibers and the like.
Natural fillers include kenaf, pulp, hemp pulp, wood pulp and the like.
Among them, glass fibers and carbon fibers are preferred, especially glass fibers.
The content of the filler (C) is preferably 1 to 230 parts by mass per 100 parts by mass of the total of the polyamide resin (A) and the polyamide resin (B). Polyamide resin compositions containing the filler (C) in such a range greatly improve in rigidity, strength, heat resistance and the like. If it exceeds 230 parts by mass, the flowability of the polyamide resin composition decreases to cause difficulty in melt kneading, molding and the like.
More preferably, the content of the filler (C) is 180 parts by mass or less, even more preferably 100 parts by mass or less, while the content is more preferably at least 10 parts by mass or more, even more preferably 20 parts by mass or more, especially 30 parts by mass or more.
[(D) Carbodiimide Compound]
Polyamide resin compositions forming the molded products of the present invention also preferably contain (D) a carbodiimide compound. Such carbodiimide compounds (D) preferably include aromatic, aliphatic or alicyclic polycarbodiimide compounds prepared by various processes. Among them, aliphatic or alicyclic polycarbodiimide compounds are preferred because of melt kneadability during extrusion or the like, and alicyclic polycarbodiimide compounds are more preferably used.
These carbodiimide compounds (D) can be prepared by decarboxylative condensation of organic polyisocyanates. For example, they can be synthesized by decarboxylative condensation of various organic polyisocyanates at a temperature of about 70° C. or more in an inert solvent or without using a solvent in the presence of a carbodiimidation catalyst. The isocyanate content is preferably 0.1 to 5% by mass, more preferably 1 to 3% by mass. The content in the above ranges tends to promote the reaction with the polyamide resins (A) and (B), thereby improving hydrolysis resistance.
Organic polyisocyanates that can be used as starting materials for synthesizing the carbodiimide compounds (D) include, for example, various organic diisocyanates such as aromatic diisocyanates, aliphatic diisocyanates and alicyclic diisocyanates and mixtures thereof.
Examples of organic diisocyanates specifically include 1,5-naphthalene diisocyanate, 4,4′-diphenylmethane diisocyanate, 4,4′-diphenyldimethylmethane diisocyanate, 1,3-phenylene diisocyanate, 1,4-phenylene diisocyanate, 2,4-tolylene diisocyanate, 2,6-tolylene diisocyanate, hexamethylene diisocyanate, cyclohexane-1,4-diisocyanate, xylylene diisocyanate, isophorone diisocyanate, dicyclohexylmethane-4,4′-diisocyanate, methylcyclohexane diisocyanate, tetramethylxylylene diisocyanate, 2,6-diisopropylphenyl isocyanate, 1,3,5-triisopropylbenzene-2,4-diisocyanate, methylenebis(4,1-cyclohexylene)diisocyanate and the like, and two or more of them can be used in combination. Among them, dicyclohexylmethane-4,4′-diisocyanate and methylenebis(4,1-cyclohexylene)diisocyanate are preferred.
To cap the ends of the carbodiimide compounds (D) to control their degree of polymerization, terminal blocking agents such as monoisocyanates are also preferably used. Monoisocyanates include, for example, phenyl isocyanate, tolyl isocyanate, dimethylphenyl isocyanate, cyclohexyl isocyanate, butyl isocyanate, naphthyl isocyanate and the like, and two or more of them can be used in combination.
The terminal blocking agents are not limited to the monoisocyanates mentioned above, but may be any active hydrogen compounds capable of reacting with isocyanates. Examples of such active hydrogen compounds may include aliphatic, aromatic or alicyclic compounds having an —OH group such as methanol, ethanol, phenol, cyclohexanol, N-methylethanolamine, polyethylene glycol monomethyl ether and polypropylene glycol monomethyl ether; secondary amines such as diethylamine and dicyclohexylamine;
primary amines such as butylamine and cyclohexylamine; carboxylic acids such as succinic acid, benzoic acid and cyclohexanecarboxylic acid; thiols such as ethyl mercaptan, allyl mercaptan and thiophenol; compounds having an epoxy group and the like, and two or more of them can be used in combination.
Carbodiimidation catalysts that can be used include, for example, phospholene oxides such as 1-phenyl-2-phospholene-1-oxide, 3-methyl-1-phenyl-2-phospholene-1-oxide, 1-ethyl-2-phospholene-1-oxide, 3-methyl-2-phospholene-1-oxide and 3-phospholene isomers thereof; metal catalysts such as tetrabutyl titanate and the like; among which 3-methyl-1-phenyl-2-phospholene-1-oxide is preferred because of reactivity. Two or more of the carbodiimidation catalysts may be used in combination.
The content of the carbodiimide compound (D) is preferably 0.1 to 2 parts by mass, more preferably 0.2 to 1.5 parts by mass, even more preferably 0.3 to 1.5 parts by mass per 100 parts by mass of the total of the polyamide resins (A) and (B). If it is less than 0.1 part by mass, the resulting resin composition will be insufficient in hydrolysis resistance so that uneven delivery is more likely to occur during melt kneading such as extrusion, resulting in insufficient melt kneading. If it exceeds 2 parts by mass, however, the viscosity of the resin composition during melt kneading tends to significantly increase, which may impair melt kneadability and moldability.
[(E) Stabilizer]
Polyamide resin compositions forming the molded products of the present invention also preferably contain (E) a stabilizer. Such stabilizers preferably include, for example, organic stabilizers such as phosphorus stabilizers, hindered phenol stabilizers, hindered amine stabilizers, organic sulfur stabilizers, oxanilide stabilizers and secondary aromatic amine stabilizers; and inorganic stabilizers such as copper compounds and halides. Phosphorus stabilizers preferably include phosphite compounds and phosphonite compounds.
Phosphite compounds include, for example, distearyl pentaerythritol diphosphite, dinonylphenyl pentaerythritol diphosphite, bis(2,4-di-t-butylphenyl)pentaerythritol diphosphite, bis(2,6-di-t-butyl-4-methylphenyl)pentaerythritol diphosphite, bis(2,6-di-t-butyl-4-ethylphenyl)pentaerythritol diphosphite, bis(2,6-di-t-butyl-4-isopropylphenyl)pentaerythritol diphosphite, bis(2,4,6-tri-t-butylphenyl)pentaerythritol diphosphite, bis(2,6-di-t-butyl-4-sec-butylphenyl)pentaerythritol diphosphite, bis(2,6-di-t-butyl-4-t-octylphenyl)pentaerythritol diphosphite, bis(2,4-dicumylphenyl)pentaerythritol diphosphite and the like, among which bis(2,6-di-t-butyl-4-methylphenyl)pentaerythritol diphosphite and bis(2,4-dicumylphenyl)pentaerythritol diphosphite are especially preferred.
Phosphonite compounds include, for example, tetrakis(2,4-di-t-butylphenyl)-4,4′-biphenylene diphosphonite, tetrakis(2,5-di-t-butylphenyl)-4,4′-biphenylene diphosphonite, tetrakis(2,3,4-trimethylphenyl)-4,4′-biphenylene diphosphonite, tetrakis(2,3-dimethyl-5-ethylphenyl)-4,4′-biphenylene diphosphonite, tetrakis(2,6-di-t-butyl-5-ethylphenyl)-4,4′-biphenylene diphosphonite, tetrakis(2,3,4-tributylphenyl)-4,4′-biphenylene diphosphonite, tetrakis(2,4,6-tri-t-butylphenyl)-4,4′-biphenylene diphosphonite and the like, among which tetrakis(2,4-di-t-butylphenyl)-4,4′-biphenylene diphosphonite is especially preferred.
Hindered phenol stabilizers include, for example, n-octadecyl-3-(3,5-di-t-butyl-4-hydroxyphenyl) propionate, 1,6-hexanediol-bis[3-(3,5-di-t-butyl-4-hydroxyphenyl) propionate], pentaerythritol tetrakis[3-(3,5-di-t-butyl-4-hydroxyphenyl) propionate], 3,9-bis[1,1-dimethyl-2-(β-(3-t-butyl-4-hydroxy-5-methylphenyl)propionyloxy)ethyl]-2,4,8,10-tetraoxaspiro[5,5]undecane, triethylene glycol-bis[3-(3-t-butyl-5-methyl-4-hydroxyphenyl) propionate], 3,5-di-t-butyl-4-hydroxybenzyl phosphonate diethyl ester, 1,3,5-trimethyl-2,4,6-tris(3,5-di-t-butyl-4-hydroxybenzyl)benzene, 2,2-thiodiethylene bis[3-(3,5-di-t-butyl-4-hydroxyphenyl) propionate], tris(3,5-di-t-butyl-4-hydroxybenzyl) isocyanurate, N,N′-hexamethylenebis(3,5-di-t-butyl-4-hydroxyhydrocinnamide) and the like.
Among them, n-octadecyl-3-(3,5-di-t-butyl-4-hydroxyphenyl) propionate, 1,6-hexanediol-bis[3-(3,5-t-butyl-4-hydroxyphenyl) propionate], pentaerythritol tetrakis[3-(3,5-di-t-butyl-4-hydroxyphenyl) propionate], 3,9-bis[1,1-dimethyl-2-{β-(3-t-butyl-4-hydroxy-5-methylphenyl)propionyloxy}ethyl]-2,4,8,10-tetraoxaspiro[5,5]undecane and N,N′-hexamethylene bis(3,5-di-t-butyl-4-hydroxyhydrocinnamide) are preferred.
Hindered amine stabilizers include, for example, well-known hindered amine compounds having a 2,2,6,6-tetramethylpiperidine skeleton.
Specific examples of hindered amine compounds include 4-acetoxy-2,2,6,6-tetramethylpiperidine, 4-stearoyloxy-2,2,6,6-tetramethylpiperidine, 4-acryloyloxy-2,2,6,6-tetramethylpiperidine, 4-phenylacetoxy-2,2,6,6-tetramethylpiperidine, 4-benzoyloxy-2,2,6,6-tetramethylpiperidine, 4-methoxy-2,2,6,6-tetramethylpiperidine, 4-stearyloxy-2,2,6,6-tetramethylpiperidine, 4-cyclohexyloxy-2,2,6,6-tetramethylpiperidine, 4-benzyloxy-2,2,6,6-tetramethylpiperidine, 4-phenoxy-2,2,6,6-tetramethylpiperidine, 4-ethylcarbamoyloxy-2,2,6,6-tetramethylpiperidine, 4-cyclohexylcarbamoyloxy-2,2,6,6-tetramethylpiperidine, 4-phenylcarbamoyloxy-2,2,6,6-tetramethylpiperidine, bis(2,2,6,6-tetramethyl-4-piperidyl) carbonate, bis(2,2,6,6-tetramethyl-4-piperidyl) oxalate, bis(2,2,6,6-tetramethyl-4-piperidyl) malonate, bis(2,2,6,6-tetramethyl-4-piperidyl) sebacate, bis(2,2,6,6-tetramethyl-4-piperidyl) adipate, bis(2,2,6,6-tetramethyl-4-piperidyl) terephthalate, 1,2-bis(2,2,6,6-tetramethyl-4-piperidyloxy) ethane, α,α′-bis(2,2,6,6-tetramethyl-4-piperidyloxy)-p-xylene, bis(2,2,6,6-tetramethyl-4-piperidyltolylene)-2,4-dicarbamate, bis(2,2,6,6-tetramethyl-4-piperidyl)hexamethylene-1,6-dicarbamate, tris(2,2,6,6-tetramethyl-4-piperidyl)benzene-1,3,5-tricarboxylate, tris(2,2,6,6-tetramethyl-4-piperidyl)benzene-1,3,4-tricarboxylate, 1-[2-{3-(3,5-di-t-butyl-4-hydroxyphenyl)propionyloxy}butyl]-4-[3-(3,5-di-t-butyl-4-hydroxyphenyl)propionyloxy]-2,2,6,6-tetramethylpiperidine, the condensation product of 1,2,3,4-butanetetracarboxylic acid and 1,2,2,6,6-pentamethyl-4-piperidinol and α,α,β′,β′-tetramethyl-3,9-[2,4,8,10-tetraoxaspiro(5,5) undecane]diethanol, the polycondensation product of dimethyl succinate and 1-(2-hydroxyethyl)-4-hydroxy-2,2,6,6-tetramethylpiperidine, 1,3-benzenedicarboxamide-N,N′-bis(2,2,6,6-tetramethyl-4-piperidyl) and the like.
Commercially available hindered amine compounds include “ADKSTABLA-52, LA-57, LA-62, LA-67, LA-63P, LA-68LD, LA-77, LA-82, LA-87” from ADEKA CORPORATION (all these designations enclosed within quotation marks above and below represent brand names (registered trademarks)); “TINUVIN 622, 944, 119, 770, 144” from Ciba Specialty Chemicals Inc.; “SUMISORB 577” from Sumitomo Chemical Company; “CYASORB UV-3346, 3529, 3853” from American Cyanamid Company; and “Nylostab S-EED” from Clariant (Japan) K.K., etc.
Organic sulfur stabilizers include, for example, organic thio acid compounds such as didodecyl thiodipropionate, ditetradecyl thiodipropionate, dioctadecyl thiodipropionate, pentaerythritol tetrakis(3-dodecylthiopropionate) and thiobis(N-phenyl-β-naphthylamine); mercaptobenzimidazole compounds such as 2-mercaptobenzothiazole, 2-mercaptobenzimidazole, 2-mercaptomethylbenzimidazole and metal salts of 2-mercaptobenzimidazole; dithiocarbamate compounds such as metal salts of diethyldithiocarbamic acid and metal salts of dibutyldithiocarbamic acid; and thiourea compounds such as 1,3-bis(dimethylaminopropyl)-2-thiourea and tributylthiourea; as well as tetramethylthiuram monosulfide, tetramethylthiuram disulfide, nickel dibutyl dithiocarbamate, nickel isopropyl xanthate, trilauryl trithiophosphite and the like.
Among them, mercaptobenzimidazole compounds, dithiocarbamate compounds, thiourea compounds and organic thio acid compounds are preferred, among which mercaptobenzimidazole compounds and organic thio acid compounds are more preferred. Especially, thioether compounds having a thioether structure can be conveniently used because they accept oxygen from oxidized materials to reduce it.
Specifically, 2-mercaptobenzimidazole, 2-mercaptomethylbenzimidazole, ditetradecyl thiodipropionate, dioctadecyl thiodipropionate and pentaerythritol tetrakis(3-dodecylthiopropionate) are more preferred, among which ditetradecyl thiodipropionate, pentaerythritol tetrakis(3-dodecylthiopropionate) and 2-mercaptomethylbenzimidazole are still more preferred, and pentaerythritol tetrakis(3-dodecylthiopropionate) is especially preferred.
The organic sulfur compounds typically, have a molecular weight of 200 or more, preferably 500 or more and typically up to 3,000.
Oxanilide stabilizers preferably include 4,4′-dioctyloxyoxanilide, 2,2′-diethoxyoxanilide, 2,2′-dioctyloxy-5,5′-di-tert-butoxanilide, 2,2′-didodecyloxy-5,5′-di-tert-butoxanilide, 2-ethoxy-2′-ethyloxanilide, N,N′-bis(3-dimethylaminopropyl)oxanilide, 2-ethoxy-5-tert-butyl-2′-ethoxanilide and its mixtures with 2-ethoxy-2′-ethyl-5,4′-di-tert-butoxanilide, mixtures of o- and p-methoxy-disubstituted oxanilides, mixtures of o- and p-ethoxy-disubstituted oxanilides and the like.
Secondary aromatic amine stabilizers preferably include compounds having a diphenylamine skeleton, compounds having a phenylnaphthylamine skeleton and compounds having a dinaphthylamine skeleton, more preferably compounds having a diphenylamine skeleton and compounds having a phenylnaphthylamine skeleton. Specifically, compounds having a diphenylamine skeleton include p,p′-dialkyldiphenylamine (wherein the alkyl group contains 8 to 14 carbon atoms), octylated diphenylamine, 4,4′-bis(α,α-dimethylbenzyl)diphenylamine, p-(p-toluenesulfonylamide)diphenylamine, N,N′-diphenyl-p-phenylenediamine, N-phenyl-N′-isopropyl-p-phenylenediamine, N-phenyl-N′-(1,3-dimethylbutyl)-p-phenylenediamine and N-phenyl-N′-(3-methacryloyloxy-2-hydroxypropyl)-p-phenylenedi amine; compounds having a phenylnaphthylamine skeleton include N-phenyl-1-naphthylamine and N,N′-di-2-naphtyl-p-phenylenediamine; and compounds having a dinaphthylamine skeleton include 2,2′-dinaphthylamine, 1,2′-dinaphthylamine and 1,1′-dinaphthylamine. Among them, 4,4′-bis(α,α-dimethylbenzyl)diphenylamine, N,N′-di-2-naphtyl-p-phenylenediamine and N,N′-diphenyl-p-phenylenediamine are more preferred, among which N,N′-di-2-naphtyl-p-phenylenediamine and 4,4′-bis(α,α-dimethylbenzyl)diphenylamine are especially preferred.
When the organic sulfur stabilizers or secondary aromatic amine stabilizers mentioned above are to be contained, they should preferably be used in combination. Polyamide resin compositions containing them in combination tend to improve heat aging resistance as compared with those in which either one is used.
More specific preferred combinations of organic sulfur stabilizers and secondary aromatic amine stabilizers include combinations of at least one organic sulfur stabilizer selected from ditetradecyl thiodipropionate, 2-mercaptomethylbenzimidazole and pentaerythritol tetrakis(3-dodecylthiopropionate) and at least one secondary aromatic amine stabilizer selected from 4,4′-bis(α,α-dimethylbenzyl)diphenylamine and N,N′-di-2-naphtyl-p-phenylenediamine. A combination of an organic sulfur stabilizer consisting of pentaerythritol tetrakis(3-dodecylthiopropionate) and a secondary aromatic amine stabilizer consisting of N,N′-di-2-naphtyl-p-phenylenediamine is more preferred.
When the organic sulfur stabilizers and secondary aromatic amine stabilizers mentioned above are to be used in combination, the ratio (mass ratio) of the amounts of the secondary aromatic amine stabilizers/organic sulfur stabilizers contained in the polyamide resin composition is preferably 0.05 to 15, more preferably 0.1 to 5, even more preferably 0.2 to 2. By selecting such a content ratio, heat aging resistance can be efficiently improved while maintaining barrier properties.
Inorganic stabilizers preferably include copper compounds and halides.
Copper compounds are copper salts of various inorganic or organic acids excluding the halides mentioned below. Copper may be either cuprous or cupric, and specific examples of copper salts include copper chloride, copper bromide, copper iodide, copper phosphate, copper stearate as well as natural minerals such as hydrotalcite, stichitite and pyrolite.
Halides used as inorganic stabilizers include, for example, alkali metal or alkaline earth metal halides; ammonium halides and quaternary ammonium halides of organic compounds; and organic halides such as alkyl halides and allyl halides, specific examples of which include ammonium iodide, stearyl triethyl ammonium bromide, benzyl triethyl ammonium iodide and the like. Among them, alkali metal halide salts such as potassium chloride, sodium chloride, potassium bromide, potassium iodide and sodium iodide are preferred.
The copper compounds are preferably used in combination with the halides, especially with the alkali metal halide salts because excellent effects are provided in the aspects of resistance to heat-induced discoloration and weatherability (light resistance). For example, when a copper compound is used alone, the molded product may be discolored in reddish brown by copper, which is not preferred for use in some applications. However, the discoloration in reddish brown can be prevented by combining the copper compound with a halide.
In the present invention, organic sulfur stabilizers, secondary aromatic amine stabilizers and inorganic stabilizers are especially preferred among the stabilizers described above because of processing stability during melt molding, heat aging resistance, the appearance of molded products and discoloration prevention.
The content of the stabilizer (E) is typically 0.01 to 1 part by mass, preferably 0.01 to 0.8 parts by mass per 100 parts by mass of the total of the polyamide resins (A) and (B). Heat discoloration and weatherability/light resistance can be sufficiently improved by selecting the content at 0.01 parts by mass or more, while the loss of mechanical properties can be reduced by selecting the content at 1 part by mass or less.
Polyamide resin compositions forming the molded products of the present invention can further contain other resins than the polyamide resin (A) and polyamide resin (B) so far as the benefits of the present invention are not affected. The other resins preferably include, for example, polyamide resins other than the polyamide resin (A) and polyamide resin (B), polyester resins, polycarbonate resins, polyimide resins, polyurethane resins, acrylic resins, polyacrylonitrile, ionomers, ethylene-vinyl acetate copolymers, fluorine resins, vinyl alcohol copolymers such as ethylene-vinyl alcohol, biodegradable resins and the like, and these can be used alone or as a mixture of two or more of them.
[Other Additives]
Polyamide resin compositions forming the molded products of the present invention may further contain additives other than those described above such as lubricants, matting agents, weather stabilizers, UV absorbers, nucleating agents, plasticizers, shock resistance improvers, flame retardants, conductive agents, antistatic agents, discoloration inhibitors, anti-gelling agents, pigments, dyes, dispersing agents and the like or a mixture of various materials not limited to the above list, so far as the benefits of the present invention are not affected.
Nucleating agents typically include inorganic nucleating agents such as finely powdered talc and boron nitride, but organic nucleating agents may also be added. The amount of the nucleating agents added is preferably 0.01 to 6 parts by mass, more preferably 0.03 to 1 parts by mass in the case of organic nucleating agents and boron nitride per 100 parts by mass of the resin components.
[Processes for Preparing Resin Compositions]
Processes for preparing polyamide resin compositions used in the present invention are not specifically limited, but they can be prepared by mixing a polyamide resin (A) and a polyamide resin (B) and optionally other components in any order to form a dry blend. They also can be prepared by further kneading the dry blend. Among others, they are preferably prepared by melt kneading using one of various conventional extruders such as a single or twin-screw extruder, especially preferably a twin-screw extruder because of productivity, versatility and the like. In this case, melt kneading is preferably performed under controlled conditions at a temperature of 200 to 300° C. for a residence time of 10 min or less by using a screw having at least one or more, preferably two or more reverse helix screw elements and/or kneading discs on which the blend partially stays. Insufficient extrusion kneading or resin breakdown tends to be less likely to occur by controlling the melt-kneading temperature in the above range.
Alternatively, compositions having a predetermined component ratio can be prepared by preliminarily melt-kneading polyamide resins with additives at high concentrations to prepare a master batch and then diluting it with the polyamide resins.
If fibrous materials such as glass fibers and carbon fibers are used, they are preferably supplied from a side feeder mounted halfway along the cylinder of the extruder.
[Processes for Preparing Molded Products]
Polyamide resin compositions forming the molded products of the present invention can be formed into molded products of various shapes by conventionally known molding processes. Examples of molding processes can include, but not limited to, injection molding, blow molding, extrusion molding, compression molding, vacuum molding, press molding, direct blow molding, rotational molding, sandwich molding and two-color molding and the like, for example, more preferably injection molding, compression molding, vacuum molding, press molding and direct blow molding. Especially preferred are injection molding, compression molding, vacuum molding, press molding and direct blow molding, among which injection molding is more preferred because the resulting molded products show very good dimensional stability and high chemical resistance.
Molded products obtained from the polyamide resin compositions described above can be conveniently used as various molded articles that are required to have low water absorption, high chemical resistance, and high crystallinity index, including various parts such as, for example, automotive parts (connectors), machine parts, electrical/electronic equipment parts and the like. Further, the molded products of the present invention may also be in the form of a sheet or tube so that they can be conveniently used as industrial, engineering and domestic goods. As used herein, the term “sheet” means those having a thickness of, for example, more than 0.25 mm.
The molded products of the present invention are especially useful when they have a thinnest thickness of 0.5 mm or more (preferably 1.0 to 2.5 mm), for example.
According to the processes for preparing molded products of the present invention, various molded products required to have low water absorption, high chemical resistance and high crystallinity index can be prepared with high dimensional stability.
The following Examples further illustrate the present invention, but the present invention should not be construed as being limited to these Examples/Comparative examples.
[Materials Used]
The materials used in the Examples and Comparative examples are as follows:
The following commercially available products were used as aliphatic polyamide resins (A).
The product available from Ube Industries, Ltd. as grade 1024B having a molecular weight of 28,000, a melting point of 225° C., and a glass transition point of 48° C.
The product available from Toray Industries, Inc. as grade CM3001N having a molecular weight of 25,000, a melting point of 265° C., and a glass transition point of 50° C.
<(B) Polyamide Resins>
The polyamide resins prepared in the following preparation examples 1 to 4 were used as polyamide resins (B).
In a reaction vessel, sebacic acid (TA grade available from Itoh Oil Chemicals Co., Ltd.) was melted by heating at 170° C. and then the temperature was raised to 240° C. while m-xylylenediamine (MXDA from Mitsubishi Gas Chemical Company, Inc.) was gradually added dropwise in a molar ratio of 1:1 to sebacic acid while stirring the contents. After completion of the dropwise addition, the temperature was raised to 260° C. After completion of the reaction, the contents were collected in the form of strands and pelletized in a pelletizer. The resulting pellets were placed in a tumbler and solid-phase polymerized under reduced pressure to give a polyamide resin having a controlled molecular weight.
The polyamide resin (MXD10) had a melting point of 191° C., a glass transition point of 60° C., a number average molecular weight of 30,000, and an oxygen transmission rate of 0.8 cc·mm/m2·day·atm as determined by the methods described below.
This polyamide resin is hereinafter abbreviated as “MXD10”.
A reaction vessel equipped with a stirrer, a partial condenser, a total condenser, a thermometer, a dropping device and a nitrogen inlet as well as a strand die was charged with precisely weighed 8950 g (44 mol) of sebacic acid (TA grade available from Itoh Oil Chemicals Co., Ltd.), 13.7401 g of calcium hypo (150 ppm expressed as the phosphorus atom concentration in the polyamide resin), and 10.6340 g of sodium acetate. The molar ratio between calcium hypophosphite and sodium acetate is 1.0. The reaction vessel was thoroughly purged with nitrogen and then pressurized with nitrogen to 0.3 MPa and heated to 160° C. with stirring to homogeneously melt sebacic acid.
Then, 6026 g (44 mol) of p-xylylenediamine (PXDA) was added dropwise with stirring over 170 min. During then, the internal temperature was continuously raised to 281° C. During the dropwise addition step, the pressure was controlled at 0.5 MPa and the water generated was removed outside the system through the partial condenser and the total condenser. The temperature in the partial condenser was controlled in the range of 145 to 147° C. After completion of the dropwise addition of p-xylylenediamine, the pressure was lowered at a rate of 0.4 MPa/hr to atmospheric pressure over 60 min. During then, the internal temperature rose to 299° C. Then, the pressure was lowered at a rate of 0.002 MPa/min to 0.08 MPa over 20 min. Then, the reaction was continued at 0.08 MPa until the torque of the stirrer reached a predetermined value. The reaction period at 0.08 MPa was 10 min. Then, the inside of the system was pressurized with nitrogen, and the polymer was collected from the strand die and pelletized to give a polyamide resin. The resulting polyamide resin PXD10 had a melting point of 290° C. and a glass transition point of 75° C. It had a number average molecular weight of 25000, and an oxygen transmission rate of 2.5 cc·mm/m2·day·atm.
This polyamide resin is hereinafter abbreviated as “PXD10”.
A polyamide resin was obtained in the same manner as in Preparation example 1 except that m-xylylenediamine was replaced by a 3:7 mixture (molar ratio) of m-xylylenediamine and p-xylylenediamine and the temperature was raised to 260° C. while the xylylenediamine mixture was gradually added dropwise in a molar ratio of 1:1 to sebacic acid, and after completion of the dropwise addition, the temperature was raised to 280° C.
The polyamide resin (MPXD10-1) had a melting point of 258° C., a glass transition point of 70° C., a number average molecular weight of 20,000, and an oxygen transmission rate of 2 cc·mm/m2·day·atm as determined by the methods described below.
This polyamide resin is hereinafter abbreviated as “MPXD10-1”.
A polyamide resin was obtained in the same manner as in Preparation example 1 except that m-xylylenediamine was replaced by a 7:3 mixture (molar ratio) of m-xylylenediamine and p-xylylenediamine. The polyamide resin (MPXD10-2) had a melting point of 215° C., a glass transition point of 63° C., a number average molecular weight of 28,000, and an oxygen transmission rate of 1.4 cc·mm/m2·day·atm as determined by the methods described below.
This polyamide resin is hereinafter abbreviated as “MPXD10-2”.
The melting point and glass transition point (expressed in ° C.) of the polyamide resins described above were determined by the following method.
The melting point and glass transition point were determined by differential scanning calorimetry (DSC) using DSC-60 available from SHIMADZU CORPORATION under analytical conditions as follows: a sample of about 5 mg was heated from 30 to 300° C. at a rate of 10° C./min, held at 300° C. for 2 min, then cooled to 30° C. at a rate of 20° C./min, and then heated at a rate of 10° C./min, whereby the melting point and glass transition point were determined.
The number average molecular weight of each of the XD10 resins described above was determined as follows.
The number average molecular weight was determined by GPC analysis and expressed as an PMMA equivalent using HLC-8320GPC available from Tosoh Corporation on TSKgel SuperHM-H columns eluting with hexafluoroisopropanol (HFIP) containing 10 mmol/l sodium trifluoroacetate at a temperature of 40° C. A calibration curve was prepared for six PMMA standards dissolved in HFIP.
<Other Additives>
Chopped strands available from Nippon Electric Glass Co., Ltd. under the brand name “T-275H”.
N,N′-di-2-naphthyl-p-phenylenediamine available from Ouchi Shinko Chemical Industrial Co., Ltd. under the brand name “NOCRAC White”.
The components described above were weighed in the amounts shown in Table 1 below (all expressed in parts by mass), blended in a tumbler and fed into a twin-screw extruder (“TEM26SS” available from Toshiba Machine Co., Ltd.). The components were melt-kneaded under conditions of a cylinder temperature of 300° C., and a screw speed of 100 rpm and the melt was extruded and pelletized and then dried under vacuum at 150° C. for 5 hours to prepare pellets of polyamide resin compositions.
The resulting pellets were used to perform various evaluations by the evaluation methods described below.
The evaluation results are shown in Table 1.
[Evaluation Methods]
In the Examples and Comparative examples, the analysis/evaluation methods are as follows.
The pellets described above were injection-molded into test specimens of 60 mm×60 mm×2 mm using the injection molding machine “SE130DU-HP model” available from Sumitomo Heavy Industries, Ltd. under conditions of a cylinder temperature of 250° C. to 300° C., a mold temperature of 30° C., and a molding cycle time of 40 seconds. The lengths of the test specimens in MD and TD directions were measured and compared with the dimensions of the cavity of the mold to determine molding shrinkages (expressed in %).
The average of the molding shrinkages in machine direction (MD) and transverse direction (TD) was calculated and evaluated as follows.
A: Less than 1
B: 1 or more and less than 1.5
C: 1.5 or more and less than 2
D: 2 or more.
The pellets described above were injection-molded into ISO test specimens (having a thickness of 4.0 mm) using the injection molding machine “SE130DU-HP model” available from Sumitomo Heavy Industries, Ltd. under conditions of a cylinder temperature of 250° C. to 300° C., a mold temperature of 30° C., and a molding cycle time of 40 seconds. The resulting ISO test specimens were annealed at 150° C. for 1 hour. Their flexural strength (expressed in MPa) and modulus of flexural elasticity (expressed in GPa) were measured according to ISO178 standard at a temperature of 23° C.
Then, the ISO test specimens were immersed in aqueous solutions each containing 10% by mass of hydrochloric acid, NaOH or CaCl2 (at a temperature of 23° C.), and after 7 days, the flexural strength (expressed in MPa) and the modulus of flexural elasticity (expressed in GPa) of the test specimens were measured and compared with the values measured before immersion to determine the retention rates (expressed in %)
Further, the average of the retention rates of elastic modulus and strength after immersion in the aqueous solutions each containing 10% by mass of hydrochloric acid, NaOH or CaCl2 (at a temperature of 23° C.) was evaluated as follows.
A: Average of 90% or more
B: Average of less than 90% and 60% or more
C: Average of less than 60% and 40% or more
D: Average of less than 40%.
The ISO test specimens described above were immersed in distilled water at 23° C., and after 110 days, water on the surface was wiped off and then the weight was measured and the water absorption rate (the rate of weight change expressed in %) was calculated from the difference between the weights before and after immersion to observe changes in water absorption rate over time.
Further, the water absorption rate was evaluated according to the following criteria:
A: less than 5%
B: 5% or more and less than 7%
C: 7% or more and less than 10%
D: 10% or more.
The pellets described above were injection-molded into test specimens having a thickness of 4.0 mm using the injection molding machine “SE130DU-HP model” available from Sumitomo Heavy Industries, Ltd. under conditions of a cylinder temperature of 250° C. to 300° C., a mold temperature of 30° C., and a molding cycle time of 40 seconds. The resulting molded products were analyzed by differential scanning calorimetry (DSC)- using “DSC-60” available from SHIMADZU CORPORATION. Evaluation was made according to crystallization peaks during heating as follows:
A: Crystallization peaks during heating with 0 J/g or more and less than 3 J/g
B: Crystallization peaks during heating with 3 J/g or more and less than 5 J/g
C: Crystallization peaks during heating with 5 J/g or more and less than 7 J/g
D: Crystallization peaks during heating with 7 J/g or more.
Based on the results of (1) to (4) above, the total numbers of ratings A to D were counted.
%
indicates data missing or illegible when filed
The results above show that the Comparative examples either had a low overall evaluation (high number of rating C) as in the case of Comparative example 1 or included rating D leading to a critical defect as in the case of Comparative examples 2 to 4. By contrast, the Examples included high numbers of rating A and rating B and none of them included rating D, showing that they are excellent materials with balanced properties.
Specifically, the systems of Comparative examples 1 and 2 solely composed of an aliphatic polyamide have high crystallinity, but low chemical resistance and high water absorption rate. On the other hand, the systems of Comparative examples 3 and 4 containing high levels of a polyamide resin (B) were found to be defective for use as molded products because they had low crystallinity index though they had high chemical resistance.
Further, pellets were prepared in the same manner as in Example 1 except that 100 parts by mass of the glass fiber, 0.2 parts by mass of the fine-grained talc, 0.1 part by mass of the secondary aromatic amine stabilizer, and 0.2 parts by mass of the inorganic stabilizer were added per 100 parts by mass of the resin composition, and subjected to various evaluations. The properties of the resulting molded product were as excellent as those of Example 1.
The molded products of the present invention show high chemical resistance, low water absorption rate and high crystallinity index so that they can be conveniently used as various parts and the like, and therefore, they will find very wide industrial applicability. Further, the processes for preparing molded products according to the present invention allow molded products having high dimensional stability to be prepared.
| Number | Date | Country | Kind |
|---|---|---|---|
| 2011-275249 | Dec 2011 | JP | national |
| Filing Document | Filing Date | Country | Kind | 371c Date |
|---|---|---|---|---|
| PCT/JP2012/080262 | 11/22/2012 | WO | 00 | 6/16/2014 |
