JP2011042774A - Rubber composition and method for producing the same - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide a rubber composition having high elasticity, high tensile strength, excellent heat generation property and fatigue property, and excellent dispersibility of an inorganic filler by melting and kneading vulcanizable rubber, a polyamide elastomer having a melting point of 100-180°C, and a silane coupling agent together to activate the interface between different kinds of polymers for compatibilization. <P>SOLUTION: The rubber composition is produced by compounding 100 pts.wt. of vulcanizable rubber (A), 0.1-50 pts.wt. of a polyamide elastomer (B) having a melting point of 100-180°C, and 0.1-100 pts.wt. of a silane coupling agent (C) together. <P>COPYRIGHT: (C)2011,JPO&INPIT

Description

  The present invention relates to a rubber composition comprising a vulcanizable rubber, a polyamide elastomer having a melting point of 100 to 180 ° C., and a silane coupling agent.

  In general, when a resin or fiber is blended with rubber, there is a problem that although it becomes highly elastic, the tensile strength is lowered and the heat generation and fatigue are deteriorated. In particular, since polyamide and rubber are difficult to compatibilize, peeling at the interface is likely to occur, which causes the above-described problems.

  Methods for increasing the elasticity by blending a resin or fiber with rubber have been widely used, and various proposals have been made.

  For example, Patent Document 1 discloses a rubber composition in which a thermoplastic polyamide refined (or shortened fiber) and silica particles are blended with rubber to improve the wear resistance of a roll of OA equipment. Patent Document 2 discloses a rubber composition for a base-isolated laminate that absorbs vibration energy efficiently with a high elastic modulus by blending natural rubber or the like with a polyamide elastomer and fine carbon black.

However, although any desired effect can be obtained with any of the techniques, there is a problem that the tensile strength and the like are lowered, and when it is used for a tire member or the like, a more practical one has been demanded.

JP 7-224189 A Japanese Patent Laid-Open No. 10-237221

  The object of the present invention is to melt and knead a vulcanizable rubber, a polyamide elastomer having a melting point of 100 to 180 ° C., and a silane coupling agent, so as to be compatible by activating the interface between different polymers, The object is to provide a rubber composition having high elasticity, high tensile strength, exothermic property, fatigue property and excellent dispersibility of inorganic fillers.

  In the present invention, 0.1 to 50 parts by weight of a polyamide elastomer (B) having a melting point of 100 to 180 ° C. and 0.1 to 0.1 parts by weight of a silane coupling agent (C) are added to 100 parts by weight of vulcanizable rubber (A). The present invention relates to a rubber composition containing 100 parts by weight.

  The present invention relates to the rubber composition, wherein the polyamide elastomer (B) has a polyether soft segment and a Shore D hardness of 30 to 75.

  The present invention relates to the rubber composition, wherein the silane coupling agent (C) is an alkoxysilane.

  0.1 to 50 parts by weight of the polyamide elastomer (B) having a melting point of 100 to 180 ° C. and 0.1 to 100 parts of the silane coupling agent (C) with respect to 100 parts by weight of the vulcanizable rubber (A) The rubber composition is characterized by blending 1 part by weight and 1 part by weight of a rubber reinforcing agent (D).

(1) Melting and kneading the vulcanizable rubber (A), the polyamide elastomer (B) and the silane coupling agent (C) at a temperature equal to or higher than the melting point of the polyamide elastomer,
(2) 1 to 100 parts by weight of the melt-kneaded product of (1) and the rubber reinforcing agent (D) and the additive (E) other than (C) and (D) are melt-kneaded at a temperature equal to or higher than the melting point of the polyamide elastomer. The present invention relates to a method for producing the rubber composition characterized by a step.

(1) Melting and kneading the vulcanizable rubber (A), the polyamide elastomer (B) and the silane coupling agent (C) at a temperature equal to or higher than the melting point of the polyamide elastomer,
(2) 1 to 100 parts by weight of the melt-kneaded product of (1) and the rubber reinforcing agent (D) and the additive (E) other than (C) and (D) are melt-kneaded at a temperature equal to or higher than the melting point of the polyamide elastomer. The rubber composition is produced by a process.

  According to the present invention, a rubber composition that is compatible by activating an interface between different types of polymers, has high elasticity, high tensile strength, exothermic property, fatigue properties, and excellent dispersibility of inorganic fillers. Can be provided.

[Vulcanizable rubber]
The vulcanizable rubber used in the present invention is not particularly limited, and any known rubber can be used. For example, polymers of diene monomers such as natural rubber, butadiene rubber (BR), butadiene rubber (VCR) containing syndiotactic-1.2-polybutadiene, isoprene rubber, butyl rubber, chloroprene rubber; acrylonitrile butadiene rubber ( NBR), acrylonitrile-diene copolymer rubbers such as nitrile chloroprene rubber, nitrile isoprene rubber; styrene-diene copolymer rubbers such as styrene butadiene rubber (SBR), styrene chloroprene rubber, styrene isoprene rubber, ethylene propylene diene rubber (EPDM), etc. Is mentioned. Of these, butadiene rubber, syndiotactic-1.2-polybutadiene-containing butadiene rubber, acrylonitrile butadiene rubber, styrene butadiene rubber, natural rubber, and isoprene rubber are preferable. These can be used alone or in combination of two or more.

Moreover, a vulcanizing agent and a vulcanization accelerator can be added to the rubber composition of the present invention.
Examples of the vulcanizing agent include sulfur, a compound that generates sulfur by heating, a metal oxide such as an organic peroxide and magnesium oxide, a polyfunctional monomer, and a silanol compound. Examples of the compound that generates sulfur by heating include tetramethyl thiuram disulfide and tetraethyl thiuram disulfide.

  Examples of the vulcanization accelerator include aldehydes, ammonia, amines, guanidines, thioureas, thiazoles, thiurams, dithiocarbamates, xanthates, and more specifically, tetramethylthiuram disulfide. (TMTD) N-oxydiethylene-2-benzothiazolylsulfenamide (OBS), N-cyclohexyl-2-benzothiazylsulfenamide (CBS), dibenzothiazyl disulfide (MBTS), 2-mercaptobenzothiazole ( MBT), zinc di-n-butyldithiocarbite (ZnBDC), zinc dimethyldithiocarbide (ZnMDC) and the like.

In addition, if necessary, known additives usually used in rubber compositions such as anti-aging agent, filler, process oil, zinc white, stearic acid and the like can be blended.
Anti-aging agents include amine / ketone-based, imidazole-based, amine-based, phenol-based, sulfur-based and phosphorus-based anti-aging agents. More specifically, as an anti-aging agent, phenol-based 2,6-di-tert-butyl-p-cresol (BHT), phosphorus-based trinonylphenyl phosphite (TNP), sulfur-based 4.6-bis (Octylthiomethyl) -o-cresol, dilauryl-3,3′-thiodipropionate (TPL) and the like.
Examples of fillers include inorganic fillers such as calcium carbonate, basic magnesium carbonate, clay, Lissajous, diatomaceous earth, and other fillers such as recycled rubber and powder rubber. Process oils include aromatic and naphthenic fillers. And paraffinic process oil.

[Polyamide elastomer having a melting point of 100 to 180 ° C.]
In the polyamide elastomer having a melting point of 100 to 180 ° C. used in the present invention, the hard segment is a polyamide, and the soft segment is a multi-block copolymer using polyether or polyester. The amide component is nylon 6,66,610,11,12, etc., representative examples of polyethers are diol poly (oxytetramethylene) glycol, poly (oxypropylene) glycol, etc., and typical examples of polyesters are poly (ethylene adipate). ) Glycol, poly (butylene-1,4 adipate) glycol, and the like.

  It is not preferable to use a polyamide elastomer having a melting point lower than 100 ° C. because it is inferior in heat resistance, and a melting point higher than 180 ° C. is not preferable because it does not melt and disperse when kneaded with rubber.

  The melting point of the polyamide elastomer used in the present invention is 100 ° C to 180 ° C, particularly preferably 120 ° C to 170 ° C.

  Further, in the present invention, the amount of the polyamide elastomer is preferably 0.1 to 50 parts by weight, more preferably 0.2 to 40 parts by weight, still more preferably 100 parts by weight of the vulcanizable rubber (A). 0.3 to 30 parts by weight, particularly preferably 0.5 to 20 parts by weight.

  If the amount of the polyamide elastomer is less than 0.1 parts by weight relative to 100 parts by weight of the vulcanizable rubber (A), the effect is not exhibited, and if it is more than 50 parts by weight, the workability deteriorates, which is not preferable.

  In particular, polyamide-forming monomers [ie, aminocarboxylic acid compound (D1) and / or lactam compound (D2)], XYX-type triblock polyetherdiamine compound (E) (Y is polyoxybutylene), and dicarboxylic acid A polyether polyamide elastomer obtained by polymerizing (F) is preferred.

  In the polyether polyamide elastomer, there is a ratio such that the terminal carboxylic acid or carboxy group contained in the polyamide-forming monomer, XYX type triblock polyether diamine, and dicarboxylic acid and the terminal amino group are approximately equimolar. preferable.

  In particular, when one end of the polyamide-forming monomer is an amino group and the other end is a carboxylic acid or a carboxy group, the XYX-type triblock polyether diamine and dicarboxylic acid are the amino group of the polyether diamine and the carboxy group of the dicarboxylic acid. The ratio is preferably such that the groups are approximately equimolar.

[Aminocarboxylic acid compound (D1) and lactam compound (D2)]
Next, the aminocarboxylic acid compound (D1) and the lactam compound (D2) will be described.
The aminocarboxylic acid compound (D1) used in the present invention is a compound represented by the following formula (1).
^{_{H 2 N-R 1 -COOH (}} 1)

Here, R ¹ represents a linking group containing a hydrocarbon chain, and is preferably an aliphatic, alicyclic or aromatic hydrocarbon group having 2 to 20 carbon atoms or an alkylene group having 2 to 20 carbon atoms, More preferably, the hydrocarbon group having 3 to 18 carbon atoms or the alkylene group having 3 to 18 carbon atoms, more preferably the hydrocarbon group having 4 to 15 carbon atoms or the alkylene group having 4 to 15 carbon atoms, Particularly preferably, it represents the hydrocarbon group having 10 to 15 carbon atoms or the alkylene group having 10 to 15 carbon atoms.

The lactam compound (D2) used in the present invention is a compound represented by the following formula (2). Here, R ² represents a linking group containing a hydrocarbon chain, and is preferably an aliphatic, alicyclic or aromatic hydrocarbon group having 3 to 20 carbon atoms or an alkylene group having 3 to 20 carbon atoms, More preferably, the hydrocarbon group having 3 to 18 carbon atoms or the alkylene group having 3 to 18 carbon atoms, more preferably the hydrocarbon group having 4 to 15 carbon atoms or the alkylene group having 4 to 15 carbon atoms, Particularly preferably, it represents the above hydrocarbon group having 10 to 15 carbon atoms or an alkylene group having 10 to 15 carbon atoms.

  As the aminocarboxylic acid compound (D1) and the lactam compound (D2), at least one aliphatic or alicyclic group selected from ω-aminocarboxylic acid, lactam, or a compound synthesized from diamine and dicarboxylic acid and salts thereof And / or polyamide-forming monomers containing aromatics are used.

  Examples of the diamine synthesized from diamine and dicarboxylic acid and salts thereof include at least one diamine compound selected from aliphatic diamine, alicyclic diamine and aromatic diamine, or derivatives thereof. . Examples of the dicarboxylic acid include at least one dicarboxylic acid compound selected from aliphatic dicarboxylic acid, alicyclic dicarboxylic acid and aromatic dicarboxylic acid, or derivatives thereof. In particular, by using a combination of an aliphatic diamine compound and an aliphatic dicarboxylic acid compound, a polyether polyamide elastomer having a low specific gravity, large tensile elongation, excellent impact resistance, and good melt moldability can be obtained. it can.

  The molar ratio of diamine to dicarboxylic acid (diamine / dicarboxylic acid) is preferably in the range of 0.9 to 1.1, more preferably in the range of 0.93 to 1.07, and in the range of 0.95 to 1.05. Is more preferable, and the range of 0.97 to 1.03 is particularly preferable. If this molar ratio is within the above range, high molecular weight can be easily achieved.

  Specific examples of the diamine include ethylene diamine, trimethylene diamine, tetramethylene diamine, hexamethylene diamine, heptamethylene diamine, octamethylene diamine, nonamethylene diamine, decamethylene diamine, undecamethylene diamine, dodecamethylene diamine, 2, Examples thereof include diamine compounds such as aliphatic diamines having 2 to 20 carbon atoms such as 2,4-trimethylhexamethylenediamine, 2,4,4-trimethylhexamethylenediamine, and 3-methylpentamethylenediamine.

  Specific examples of the dicarboxylic acid include oxalic acid, succinic acid, glutaric acid, adipic acid, pimelic acid, suberic acid, azelaic acid, sebacic acid, and aliphatic dicarboxylic acid having 2 to 20 carbon atoms such as dodecanedioic acid. A dicarboxylic acid compound can be mentioned.

  Specific examples of the lactam include aliphatic lactams having 5 to 20 carbon atoms such as ε-caprolactam, ω-enantolactam, ω-undecalactam, ω-dodecalactam, and 2-pyrrolidone.

  Specific examples of the ω-aminocarboxylic acid include 6-aminocaproic acid, 7-aminoheptanoic acid, 8-aminooctanoic acid, 10-aminocapric acid, 11-aminoundecanoic acid, 12-aminododecanoic acid, and the like. ˜20 aliphatic ω-aminocarboxylic acids and the like.

[XYX type triblock polyether diamine (E)]
The XYX-type triblock polyether diamine (E) used in the present invention is a compound represented by the following formula (3), and polypropylene is added by adding propylene oxide to both ends of poly (oxytetramethylene) glycol and the like. After making into glycol, polyether diamine etc. which are manufactured by making ammonia etc. react with the terminal of this polypropylene glycol can be used.

  Specific examples of the XYX type triblock polyether diamine (E) include XTJ-533 manufactured by HUNTSMAN (USA) (in the general formula (3), x is approximately 12, y is approximately 11, and z is approximately 11), XTJ-536 (In general formula (3), x is about 8.5, y is about 17, and z is about 7.5), and XTJ-542 (in general formula (3), x is about 3, y is about 9, For example, z is approximately 2).

  Further, as XYX type triblock polyether diamine (E), XYX-1 (general formula (3), x is about 3, y is about 14, z is about 2), XYX-2 (general formula (3) X is approximately 5, y is approximately 14, z is approximately 4), and XYX-3 (in general formula (3), x is approximately 3, y is approximately 19, z is approximately 2), etc. it can.

  In the XYX type triblock polyether diamine (E), x and z are 1 to 20, preferably 1 to 18, more preferably 1 to 16, more preferably 1 to 14, particularly preferably 1 to 12, y is 4 to 50, preferably 5 to 45, more preferably 6 to 40, more preferably 7 to 35, and particularly preferably 8 to 30. Further, as a combination of x, y and z, x is in the range of 2 to 6, y is in the range of 6 to 12, z is in the range of 1 to 5, or x is in the range of 2 to 10, and y is in the range of 13 to Preferred examples include a range of 28 and a combination of z in the range of 1-9.

  In the XYX type triblock polyether diamine (E), when x and z are each smaller than the above range, the resulting elastomer is inferior in transparency, which is not preferable. When y is smaller than the above range, rubber elasticity Is not preferable because of a low. Further, when x and z are larger than the above range, or when y is larger than the above range, the compatibility with the polyamide component becomes low and it is difficult to obtain a tough elastomer, which is not preferable.

[Dicarboxylic acid compound (F)]
The dicarboxylic acid compound (F) used in the present invention is a compound represented by the following formula (4).
_{^{HOOC- (R 3) m -COOH (}} 4)

Here, R ³ represents a linking group containing a hydrocarbon chain, and is preferably an aliphatic, alicyclic or aromatic hydrocarbon group having 1 to 20 carbon atoms or an alkylene group having 1 to 20 carbon atoms. And more preferably the hydrocarbon group having 1 to 15 carbon atoms or the alkylene group having 1 to 15 carbon atoms, more preferably the hydrocarbon group having 2 to 12 carbon atoms or the alkylene group having 2 to 12 carbon atoms. Particularly preferably, it represents the above hydrocarbon group having 4 to 10 carbon atoms or an alkylene group having 4 to 10 carbon atoms. M represents 0 or 1.

  As the dicarboxylic acid compound (F), at least one dicarboxylic acid selected from aliphatic, alicyclic and aromatic dicarboxylic acids or derivatives thereof can be used.

  Specific examples of the dicarboxylic acid include linear aliphatic dicarboxylic acids having 2 to 25 carbon atoms such as oxalic acid, succinic acid, glutaric acid, adipic acid, pimelic acid, suberic acid, azelaic acid, sebacic acid, dodecanedioic acid, Alternatively, aliphatic dicarboxylic acids such as dimerized aliphatic dicarboxylic acids having 14 to 48 carbon atoms (dimer acid) obtained by dimerizing unsaturated fatty acids obtained by fractional distillation of triglycerides and hydrogenated products thereof (hydrogenated dimer acid) And alicyclic dicarboxylic acids such as 1,4-cyclohexanedicarboxylic acid and aromatic dicarboxylic acids such as terephthalic acid and isophthalic acid. As the dimer acid and hydrogenated dimer acid, trade names “Pripol 1004”, “Plipol 1006”, “Plipol 1009”, “Plipol 1013” and the like manufactured by Unikema Corporation can be used.

  The ratio of the polyamide-forming monomer to the total components of the polyether polyamide elastomer is preferably 10 to 95% by mass, more preferably 15 to 90% by mass, more preferably 15 to 85% by mass, and particularly preferably 15 to 80% by mass. %, Most preferably 15 to 70 mass. If the ratio of the polyamide-forming monomer to all the components of the polyether polyamide elastomer is 10% by mass or more, the crystallinity of the polyamide component can be improved, and mechanical properties such as strength and elastic modulus can be improved. Can do. If it is 95 mass% or less, the function and performance as elastomers, such as rubber elasticity and a softness | flexibility, can be expressed.

  Moreover, the ratio of the total amount of the (E) compound and the (F) compound with respect to all the components of the polyether polyamide elastomer is preferably 5 to 90% by mass, more preferably 10 to 85% by mass, and more preferably 15 to 85%. % By mass, particularly preferably 20 to 85% by mass, most preferably 30 to 85% by mass.

  The Shore D hardness of the polyether polyamide elastomer is preferably in the range of 30 to 75, more preferably 33 to 72, and particularly preferably 35 to 70. In the present invention, the hardness (Shore D) can be measured according to ASTM D2240.

  The flexural modulus of the polyether polyamide elastomer is preferably 20 to 450 MPa, more preferably 20 to 400 MPa, more preferably 20 to 350 MPa, and particularly preferably 20 to 300 MPa. When the elastic modulus is within the above range, an elastomer having particularly excellent toughness and rubber elasticity can be obtained. In the present invention, the flexural modulus can be measured according to ASTM D790.

  The tensile yield strength of the polyether polyamide elastomer is preferably in the range of 3 to 25 MPa, more preferably in the range of 3 to 22 MPa, more preferably in the range of 3 to 20 MPa, and particularly preferably in the range of 3 to 18 MPa. When the tensile yield point strength is in the above range, an elastomer having particularly excellent toughness and rubber elasticity can be obtained. In the present invention, the tensile yield point strength can be measured according to ASTM D-638.

  The tensile elongation at break of the polyether polyamide elastomer is preferably 300% or more, particularly preferably 600% or more. If the amount is less than this range, performance as an elastomer such as toughness and rubber elasticity becomes difficult to be exhibited, which may not be preferable. In the present invention, the tensile elongation at break can be measured according to ASTM D-638.

  The flexural strength of the polyether polyamide elastomer is preferably 0.8 to 15 MPa, more preferably 1 to 13 MPa, more preferably 1.1 to 10 MPa, and particularly preferably 1.2 to 9 MPa. When the bending strength of the polyether polyamide elastomer is within the above range, an elastomer having an excellent balance between toughness such as bending strength and rubber elasticity can be obtained. In the present invention, the bending strength can be measured according to ASTM D-790.

  It is preferable that the polyether polyamide elastomer is not broken (abbreviated as NB) in the measurement of impact strength with an Izod notch at 23 ° C., because it is particularly excellent in impact resistance. In the present invention, the impact strength with Izod notch can be measured in accordance with ASTM D-256.

  The deflection temperature under load of the polyether polyamide elastomer is preferably 50 ° C. or higher. Within the above range, the material is less likely to be deformed during use, which is preferable. In the present invention, the deflection temperature under load can be measured according to ASTM D-648.

  The relative viscosity (ηr) of the polyether polyamide elastomer is preferably in the range of 1.2 to 3.5 (0.5 mass / volume% metacresol solution, 25 ° C.).

[Method for producing polyether polyamide elastomer]
As an example of a method for producing a polyether polyamide elastomer, three components of a polyamide-forming monomer, an XYX type triblock polyether diamine and a dicarboxylic acid are melt-polymerized under pressure and / or normal pressure, and further if necessary. A method comprising a step of melt polymerization under reduced pressure can be used, and further, three components of polyamide-forming monomer, XYX type triblock polyetherdiamine and dicarboxylic acid are simultaneously melt polymerized under pressure and / or normal pressure, If necessary, a method comprising a step of melt polymerization under reduced pressure can be used. It is also possible to use a method in which a polyamide-forming monomer and a dicarboxylic acid are first polymerized and then an XYX type triblock polyether diamine is polymerized.

  In the production of the polyether polyamide elastomer, there is no particular limitation on the raw material charging method, but the polyamide forming monomer, the XYX type triblock polyether diamine and the dicarboxylic acid are preferably charged with respect to all components. Is in the range of 10 to 95% by mass, particularly preferably in the range of 15 to 90% by mass, and the XYX type triblock polyether diamine is preferably in the range of 3 to 88% by mass, particularly preferably in the range of 8 to 79% by mass. Among the raw materials, the XYX type triblock polyether diamine and the dicarboxylic acid are preferably charged so that the amino group of the XYX type triblock polyether diamine and the carboxy group of the dicarboxylic acid are approximately equimolar.

  The polymerization temperature is preferably 150 to 300 ° C, more preferably 160 to 280 ° C, and particularly preferably 180 to 250 ° C. When the polymerization temperature is 150 ° C. or higher, the polymerization reaction proceeds favorably, and when it is 300 ° C. or lower, thermal decomposition is suppressed and a polymer having good physical properties can be obtained.

  The polyether polyamide elastomer can be produced by a method comprising a step of normal pressure melt polymerization or normal pressure melt polymerization followed by reduced pressure melt polymerization when ω-aminocarboxylic acid is used as the polyamide-forming monomer.

  On the other hand, when using a lactam or a diamine synthesized from a dicarboxylic acid and / or a salt thereof as a polyamide-forming monomer, an appropriate amount of water is allowed to coexist and melt polymerization under a pressure of 0.1 to 5 MPa is performed. And a subsequent method comprising normal pressure melt polymerization and / or reduced pressure melt polymerization.

  The polymerization time is usually 0.5 to 30 hours. If the polymerization time is 0.5 hours or more, the molecular weight can be increased, and if it is 30 hours or less, coloring due to thermal decomposition and the like can be suppressed, and a polyether polyamide elastomer having desired physical properties can be obtained. .

  The production of the polyether polyamide elastomer can be carried out batchwise or continuously, and a batch reactor, a single- or multi-tank continuous reactor, a tubular continuous reactor, etc. can be used alone or in combination. Can be used.

When producing a polyether polyamide elastomer, monoamines and diamines such as laurylamine, stearylamine, hexamethylenediamine, and metaxylylenediamine, acetic acid, Monocarboxylic acids such as benzoic acid, stearic acid, adipic acid, sebacic acid and dodecanedioic acid, or dicarboxylic acids can be added.
These amounts are preferably added as appropriate so that the relative viscosity of the finally obtained elastomer is in the range of 1.2 to 3.5 (0.5 mass / volume% metacresol solution, 25 ° C.). .

  The addition amount of the above-mentioned monoamine and diamine, monocarboxylic acid and dicarboxylic acid is preferably set within a range that does not hinder the properties of the obtained polyether polyamide elastomer.

  In the production of the polyether polyamide elastomer, phosphoric acid, pyrophosphoric acid, polyphosphoric acid, etc. are used as a catalyst as necessary, and phosphorous acid, hypophosphorous acid, and Inorganic phosphorus compounds such as these alkali metal salts and alkaline earth metal salts can be added. The addition amount is usually 50 to 3000 ppm with respect to the charged raw materials.

  Polyether polyamide elastomer is heat resistant agent, ultraviolet absorber, light stabilizer, antioxidant, antistatic agent, lubricant, slip agent, crystal nucleating agent, tackifier, and sealability improvement as long as its properties are not hindered. An agent, an antifogging agent, a release agent, a plasticizer, a pigment, a dye, a fragrance, a flame retardant, a reinforcing material, and the like can be added.

  Polyether polyamide elastomer has low water absorption, excellent melt moldability, excellent moldability, excellent toughness, excellent bending fatigue resistance, excellent rebound resilience, low specific gravity, and low temperature flexibility. Excellent low-temperature impact resistance, excellent stretch recovery, excellent sound deadening properties, excellent rubber properties and transparency.

  The polyether polyamide elastomer has good compatibility with thermoplastic resins such as polyamide, polyvinyl chloride, thermoplastic polyurethane and ABS resin excluding the polyether polyamide elastomer used in the present invention, and should be blended with these thermoplastic resins. Thus, the moldability, impact resistance, elasticity and flexibility of these resins can be improved. The polyether polyamide elastomer has gas barrier properties, but the gas barrier properties can be further improved by mixing with other resins.

The polyether polyamide elastomer in the present invention is commercially available as “UBESTA XPA 9040X1, 9040F1, 9048X1, 9048F1, 9055X1, 9055F1, 9063X1, 9063F1, 9040X2, 9048X2, 9040F2, and 9048F2.” (Ube Industries, Ltd.) etc. can be used.
A sheet-like molded product can be obtained by a known molding method such as injection molding, extrusion molding, blow molding, or vacuum molding.
Further, the polyether polyamide elastomer has an effect of accelerating vulcanization when added to rubber and vulcanized, and can contribute to improvement of productivity of rubber products.

〔Silane coupling agent〕
Examples of the silane coupling agent (C) blended in the rubber composition according to the present invention include alkoxysilanes such as methyltrimethoxysilane, methyltriethoxysilane, diethoxydiethylsilane, dimethoxydiphenylsilane, dimethoxydimethylsilane, Dimethoxymethylphenylsilane, triethoxyethylsilane, trimethoxyphenylsilane, trimethoxypropylsilane, phenyltriethoxysilane, hexyltrimethoxysilane, octadecyltriethoxysilane, octadecyltrimethoxysilane, and N-dodecyltriethoxysilane.

Including the above alkoxysilanes, alkoxysilanes containing vinyl groups, alkoxysilanes having ester bonds, alkoxysilanes having epoxy groups, alkoxysilanes having epoxy groups, alkoxysilanes having mercapto groups, sulfide groups Examples include alkoxysilanes having chloro groups, alkoxysilanes having chloro groups, alkoxysilanes having styryl groups, alkoxysilanes having ureido groups, and alkoxysilanes having isocyanate groups.

Examples of alkoxysilanes having a vinyl group include vinyltrimethoxysilane, vinyltriethoxysilane, diethoxymethylvinylsilane, vinylmethyldimethoxysilane, trichlorovinylsilane, allyltriethoxysilane, allyltrimethoxysilane, allyltrichlorosilane, and vinyltris. Alkoxysilanes having (2-methoxyethoxy) silane acryloxy group or methacryloxy group, such as 3-acryloxypropyltrimethoxysilane, 3-methacryloxypropyltriethoxysilane, 3-methacryloxypropyltrimethoxysilane, 3- Methacryloxypropylmethyldiethoxysilane and 3-methacryloxypropylmethyldimethoxysilane.

Examples of alkoxysilanes having an ester bond include triacetoxymethylsilane and diacetoxydimethylsilane.

Examples of alkoxysilanes having an epoxy group include 2- (3,4-epoxycyclohexyl) ethyltrimethoxysilane, 3-glycidoxypropyldimethoxymethylsilane, 3-glycidoxypropyltriethoxysilane, and 3-glycol. Examples include cidoxypropyltrimethoxysilane and 3-glycidoxypropylmethyldiethoxysilane.

Examples of alkoxysilanes having an amino group include 3- (N-phenyl) aminopropyltrimethoxysilane, 3-aminopropyldiethoxymethylsilane, 3-aminopropyltriethoxysilane, 3-aminopropyltrimethoxysilane, 3-triethoxysilyl-N- (1,3-dimethyl-butylidene) propylamine, N- (2-aminoethyl) -3-aminopropyltrimethoxysilane, N- (2-aminoethyl) -3-aminopropyl Examples include methyldimethoxysilane, N- (2-aminoethyl) -3-aminopropyltriethoxysilane, and N- (vinylbenzyl) -2-aminoethyl-3-aminopropyl.

Examples of alkoxysilanes having a mercapto group include 3-mercaptopropyltriethoxysilane, 3-mercaptopropyltrimethoxysilane, and 3-mercaptopropylmethyldimethoxysilane.

  Examples of alkoxysilanes having a sulfide group include 3-octanoylthio-1-propyltriethoxysilane and bis (triethoxysilylpropyl) tetrasulfide.

Examples of alkoxysilanes having a chloro group include chloromethyltriethoxysilane, 3-chloropropyldimethoxymethylsilane, 3-chloropropyltrichlorosilane, 3-chloropropyltriethoxysilane, 3-chloropropyltrimethoxysilane, 3 -Chloropropyldimethoxymethylsilane, butyltrichlorosilane, chlorohexyltrichlorosilane, dodecaciltrichlorosilane, ethyltrichlorosilane, n-decyltrichlorosilane, n-octyltrichlorosilane, n-tetradecyltrichlorosilane, phenyltrichlorosilane, etc. .

  Examples of alkoxysilanes having a styryl group include p-styryltrimethoxysilane.

  Examples of alkoxysilanes having a ureido group include 3-ureidopropyltriethoxysilane.

Examples of the alkoxysilane having an isocyanate group include 3-isocyanatopropyltriethoxysilane, 3-isocyanatopropyltrimethoxysilane, and tris- (3-trimethoxysilylpropyl) isocyanurate.

  A silane coupling agent may be used in combination of a plurality of the above compounds.

  The amount of the silane coupling agent used is preferably 0.1 to 100 parts by weight, more preferably 0.2 to 50 parts by weight, and particularly preferably 0 to 100 parts by weight of the vulcanizable rubber (A). .5 to 10 parts by weight.

In particular, an alkoxysilane having an amino group or an epoxy group is desirable.

In addition, when a silane coupling agent having an amino group is used, it is effective for both a vulcanizable rubber such as SBR and a polyamide-based resin, and as a result, the compatibility between the two is activated. Since it increases, it is more preferable.
Similarly, the same effect can be obtained with a silane coupling agent having an epoxy group.

[Rubber reinforcement]
A rubber reinforcing agent may be blended in the rubber composition according to the present invention.

Examples of the rubber reinforcing agent include various carbon blacks, white carbon, silica, activated calcium carbonate, and ultrafine magnesium silicate. Among these, at least one of carbon black and silica is preferable. Particularly preferred is carbon black having a particle size of 90 nm or less and a dibutyl phthalate (DBP) oil absorption of 70 ml / 100 g or more. For example, FEF, FF, GPF, SAF, ISAF, SRF, HAF and the like are used.

The silica particles must have a silica purity of 97% or higher. Silica having a purity of less than 97% does not have a sufficient rubber reinforcing effect, so that a rubber composition blended with such silica does not have sufficient wear resistance. The average particle diameter of the silica particles is 0.1 to 50 μ, preferably 1 to 50 μ, particularly preferably 5 to 50 μ. Such silica particles can be obtained, for example, by a method of pulverizing completely melted quartz glass so as to have an appropriate particle size. Further, pulverized natural quartz having a silica purity of 97% or more is also preferably used. Furthermore, particles obtained by hydrolyzing an organosilicon compound such as silane are also preferably used.

  The amount of the rubber reinforcing agent used is preferably 1 to 100 parts by weight, more preferably 10 to 80 parts by weight, and particularly preferably 20 to 70 parts by weight with respect to 100 parts by weight of the vulcanizable rubber (A). is there.

When carbon black and silica used for the rubber reinforcing agent are mixed, it becomes possible to achieve both workability, low energy loss and wear. In particular, the weight ratio of carbon black / silica is preferably 90/10 to 10/90, more preferably 80/20 to 20/80, and particularly preferably 70/30 to 30/70.
If the amount of silica is less than 10%, energy loss increases, and if it is more than 90%, there is a drawback that workability and wear resistance are deteriorated.

  A rubber composition using a silane coupling agent functions to improve the dispersibility of the rubber reinforcing agent in the rubber matrix by mixing with a rubber reinforcing agent such as silica. As a result, it also leads to effects such as low fuel consumption.

The rubber composition according to the present invention is a mixture of the above components under the condition that the maximum temperature during kneading is equal to or higher than the melting point of the polyamide elastomer using an ordinary banbury, open roll, kneader, biaxial kneader or the like. Obtained by kneading.
The maximum temperature during kneading is preferably in the range of the same temperature as the melting point of the polyamide elastomer to 50 ° C. higher than the melting point, more preferably 5 ° C. higher than the melting point to 40 ° C. higher than the melting point.
If the maximum temperature during kneading is lower than the melting point of the polyamide elastomer, the polyamide elastomer does not melt and disperse, and if it is 50 ° C. higher than the melting point, the vulcanizable rubber may deteriorate.

[Other additives]
If necessary, the rubber composition according to the present invention includes a vulcanizing agent, a vulcanizing auxiliary agent / activator, a scorch inhibitor, an anti-aging agent, a filler, a process oil, zinc white, stearic acid, etc. You may knead | mix the compounding agent used in an industry.

  As the vulcanizing agent, known vulcanizing agents such as sulfur, organic peroxides, resin vulcanizing agents, and metal oxides such as magnesium oxide are used.

  As the vulcanization aid, known vulcanization aids such as aldehydes, ammonia, amines, guanidines, thioureas, thiazoles, thiurams, dithiocarbamates, xanthates and the like are used.

  As the scorch inhibitor (retarder), organic acids, nitroso compounds, N-cyclohexylthiophthalimide, sulfonamide derivatives and the like are used.

  Examples of the anti-aging agent include amine / ketone series, imidazole series, amine series, phenol series, sulfur series and phosphorus series.

  Examples of the filler include inorganic fillers such as calcium carbonate, basic magnesium carbonate, clay, Lissajous and diatomaceous earth, and organic fillers such as recycled rubber and powder rubber.

  The process oil may be any of aromatic, naphthenic, and paraffinic. Also, soybean oil can be used.

As the additive (E) other than (C) and (D), process oil, zinc oxide, stearic acid, an anti-aging agent and the like are preferable.

The amount of process oil is preferably 1 to 50 parts by weight with respect to 100 parts by weight of vulcanizable rubber (A),
The amount of zinc oxide is preferably 0.5 to 10 parts by weight with respect to 100 parts by weight of vulcanizable rubber (A),
The amount of stearic acid is preferably 0.1 to 5 parts by weight with respect to 100 parts by weight of the vulcanizable rubber (A), and the amount of the antioxidant is 100 parts by weight of the vulcanizable rubber (A). The amount is preferably 0.1 to 5 parts by weight.

  If the amount is less than the above amount, the effect is not manifested. Conversely, if the amount is too large, problems such as blooming on the rubber surface occur, which is not preferable.

〔Manufacturing process〕
The rubber composition obtained by the present invention can be obtained by a production method according to the following two-stage process.
(1) A step of melt-kneading the vulcanizable rubber (A), the polyamide elastomer (B) and the silane coupling agent (C) at a temperature equal to or higher than the melting point of the polyamide elastomer, and then (2) the above-mentioned ( 1 to 100 parts by weight of the melt-kneaded product obtained in the step 1) and the rubber reinforcing agent (D) and the additive (E) other than (C) and (D) are melt-kneaded at a temperature equal to or higher than the melting point of the polyamide elastomer. It is desirable to produce a rubber composition based on the process of performing.

  In particular, the process of melt-kneading at a temperature equal to or higher than the melting point of the polyamide elastomer with respect to the production process disperses the polyamide elastomer in the vulcanizable rubber and promotes compatibilization with the silane coupling agent, thereby obtaining a rubber reinforcing effect. It is done.

  In the rubber composition obtained in the above two-stage process, the dispersion of the polyamide elastomer further proceeds, and the rubber reinforcing agent and other additives are also dispersed, so that a higher rubber reinforcing effect can be obtained.

  The rubber composition of the present invention relates to a rubber composition having high elasticity, high tensile strength, exothermic property, and excellent fatigue properties, such as a tire external member such as a tread, a sidewall, and a chafer in a tire, a carcass belt, Tire internal parts such as beads and inner liners, industrial articles such as anti-vibration rubber, rubber belts, hoses, seismic isolation rubber, fenders, footwear such as men's shoes, women's shoes, sports shoes, industrial, printing and office equipment Rubber rolls for golf, sports equipment such as golf balls, tennis balls, sports floors, solid tires for agriculture and forklifts, rubber crawlers, casters, sealing materials, adhesives, rubber sheets, waterproofing materials, packings, sponge products It can also be used.

  Furthermore, when applied to an inner liner of a tire, a mixture of a polyamide elastomer and a rubber or resin having a high gas barrier property can be used. Examples of rubbers and resins with high gas barrier properties include known materials such as halogenated butyl rubber, EVOH, low density polyethylene, polystyrene, polypropylene, polycarbonate, polyvinyl acetate, amorphous polyethylene terephthalate, polyvinyl chloride, nylon 6, and polyfluoride. A mixture of vinyl, polyvinylidene chloride, polyacrylonitrile, ethylene vinyl alcohol copolymer, polyvinyl alcohol, or the like can also be used. In this case, the carcass and the inner liner may be directly laminated.

  Hereinafter, the present invention will be specifically described with reference to Examples and Comparative Examples. In Examples and Comparative Examples, the physical properties of vulcanizable rubber and the properties of the resulting rubber composition and the vulcanized product were measured as follows.

[Rubber properties that can be vulcanized]
(1) Mooney viscosity (ML)
The Mooney viscosity (ML) was measured by a Mooney viscometer (SMV-202, manufactured by Shimadzu Corp.) in accordance with JIS-K6300 and preheated for 1 minute at 100 ° C. for 4 minutes.

(2) Intrinsic viscosity [η]
Intrinsic viscosity [η] is obtained by placing 0.1 g of sample rubber and 100 ml of toluene in an Erlenmeyer flask and completely dissolving them at 30 ° C., and then adding the above solution to the Canon Fenceke kinematic viscometer in a constant temperature bath maintained at 30 ° C. 10 ml was added, the falling time (T) of the solution was measured, and the value obtained by the following formula was used.
ηsp = T / T0-1 (T0: falling time of toluene only)
ηsp / c = [η] + k ′ [η] ² c
(Ηsp: specific viscosity, k ′: Huggins constant (0.37), c: sample concentration (g / ml))

(3) Toluene solution viscosity (Tcp)
Toluene solution viscosity (Tcp) was obtained by dissolving 2.28 g of polymer in 50 ml of toluene, and using viscometer calibration standard solution (JIS-Z8809) as a standard solution. 400 was used and measured at 25 ° C.

(4) Microstructure The microstructure was analyzed by infrared absorption spectrum analysis. The microstructure was calculated from the absorption intensity ratio of cis 740 cm ⁻¹ , trans 967 cm ⁻¹ and vinyl 910 cm ⁻¹ .

(5) ηsp / c
ηsp / c was a reduced viscosity measured at 135 ° C. from a 0.20 g / dl o-dichlorobenzene solution as a measure of the molecular weight of 1.2 polybutadiene crystal fiber.

[Rubber properties after compounding]
The Mooney viscosity (ML1 + 4, 100 ° C.) was measured by a Mooney viscometer (SMV-202, manufactured by Shimadzu Corporation) in accordance with JIS-K6300, with a preheat 1 minute measurement at 100 ° C. for 4 minutes. The smaller the value, the lower the viscosity and the better the fluidity.

Die swell is a measure of the dimensional stability of the compound, using a processability measuring device (manufactured by Monsanto, MPT) at a shear rate of 100 ° C. and 100 sec ⁻¹ and the cross-sectional area of the compound during extrusion. The ratio of the die orifice cross-sectional area (where L / D = 1.5 mm / 1.5 mm) was measured. It shows that extrusion property is so favorable that a numerical value is small.

  Vulcanization characteristics (t90) were measured using a JSR Curast Meter II F type at 150 ° C until the vulcanization torque reached 90%. The smaller the value, the shorter the vulcanization time. Show.

[Physical properties of vulcanizate]
The JIS-A hardness indicates that the hardness is higher as the numerical value is larger, measured with a type A according to the measurement method defined in JIS-K6253.

  Tensile stress measured 100% tensile stress according to JIS-K6251. The larger the value, the higher the tensile stress.

  The tensile strength and elongation at break were determined by measuring the tensile strength and elongation at break according to JIS-K62511. Larger values indicate higher tensile strength and elongation at break.

  The tear strength was measured according to JIS-K6252. The larger the value, the higher the tear stress.

  Tensile fatigue is measured using a tensile fatigue tester (manufactured by Ueshima Seisakusho Co., Ltd.) with a scratch of 0.5 mm in the center of a dumbbell-shaped No. 3 (JIS-K6251) test piece, initial strain of 50%, 300 times / min. The number of times that the test piece broke under the conditions was measured. The larger the value, the better the stretch fatigue property.

  The exothermic property was measured according to the measurement method defined in JIS-K6265. The smaller the numerical value, the smaller the calorific value and the better.

  The loss factor (tan δ) was measured using RPA2000 (manufactured by Alpha Technologies) under the conditions of 60 ° C., 10 Hz, and 2% strain. The smaller the value, the smaller the energy loss and the better.

  The bending crack growth property was measured in accordance with JIS-K6260, and the crack length was measured when the movement distance of the specimen gripper was bent 10,000 times at 30 mm using a dimer bending tester (manufactured by Ueshima Seisakusho). It shows that bending crack growth resistance is so favorable that a numerical value is small.

  Abrasion was measured under the condition of a slip rate of 20% using a Lambourn abrasion tester specified in JIS-K6265. The larger the value, the less the amount of wear and the better.

    The oxygen permeability was measured under the conditions of 23 ° C. and 50% relative humidity using an oxygen gas permeation measuring device (MOCON-OX-TRAN 2/20 manufactured by Modern Control) according to ASTM-D3985. The smaller the value, the less oxygen permeation and the better the gas barrier property.

Hereinafter, the characteristic value of the polyether polyamide elastomer was measured as follows.
(1) Relative viscosity (ηr) (0.5 mass / volume% metacresol solution, 25 ° C.)
Using reagent-grade m-cresol as a solvent, it was measured at 25 ° C. using an Ostwald viscometer at a concentration of 5 g / dm ³ .

(2) Terminal carboxy group concentration ([COOH])
40 ml of benzyl alcohol was added to about 1 g of the polymer, heated and dissolved in a nitrogen gas atmosphere, phenolphthalein was added as an indicator to the obtained sample solution, and titrated with an N / 20 potassium hydroxide-ethanol solution.
(3) Terminal amino group concentration ([NH ₂ ])
About 1 g of the polymer was dissolved in 40 ml of a phenol / methanol mixed solvent (volume ratio: 9/1), thymol blue was added as an indicator to the obtained sample solution, and titrated with N / 20 hydrochloric acid.

(4) Melting point (Tm) and crystallization temperature (Tc)
Tm and Tc were measured under a nitrogen atmosphere using a differential scanning calorimeter DSC-50 manufactured by Shimadzu Corporation. The temperature was raised from room temperature to 230 ° C. at a rate of 10 ° C./min (referred to as a temperature rise first run), held at 230 ° C. for 10 minutes, and then lowered to −100 ° C. at a rate of 10 ° C./min (temperature fall first run). Then, the temperature was raised to 230 ° C. at a rate of 10 ° C./min (referred to as a temperature raised second run). From the obtained DSC chart, the exothermic peak temperature of the temperature decrease first run was Tc, and the endothermic peak temperature of the temperature increase second run was Tm.
(5) Composition The composition of the polyether polyamide elastomer was determined from a proton NMR spectrum measured at room temperature using JNM-EX400WB type FT-NMR manufactured by JEOL Ltd. at a concentration of 4% by mass using heavy trifluoroacetic acid as a solvent. The composition of each component was determined.

(6) Shore D hardness Shore D was measured according to ASTM D2240. It measured using the sheet | seat of thickness 6mm shape | molded by injection molding. The measurement was performed at a temperature of 23 ° C.
(7) Mechanical properties: Measurements (i) to (iv) shown below were performed by molding the following test pieces by injection molding.
(I) Tensile test (tensile yield point strength and tensile elongation at break): A Type I test piece described in ASTM D638 was measured according to ASTM D638.
(Ii) Bending test (flexural modulus and bending strength): Measured according to ASTM D790 using a test piece having a test piece size of 6.35 mm × 12.7 mm × 127 mm.
(Iii) Impact strength (with Izod notch): Measured at 23 ° C. in accordance with ASTM D256 using a test piece with dimensions of 12.7 mm × 12.7 mm × 63.5 mm.
(Iv) Deflection temperature under load: It was measured at a load of 0.45 MPa in accordance with ASTM D648 using a test piece having a test piece size of 6.35 mm × 12.7 mm × 127 mm.

Production Example 1 (Production of PAE1)
In a 70 liter pressure vessel equipped with a stirrer, thermometer, torque meter, pressure gauge, nitrogen gas inlet, pressure regulator and polymer outlet, Ube Industries' 12-aminododecanoic acid 8.000 kg, ABA type Of triblock polyether diamine (manufactured by HUNTSMAN, trade name: XTJ-542) 10.471 kg and adipic acid 1.529 kg were charged. After sufficiently replacing the inside of the container with nitrogen, heating was gradually performed while supplying nitrogen gas at a flow rate of 300 liters / minute. The temperature was raised from room temperature to 230 ° C. over 3 hours, and polymerization was carried out at 230 ° C. for 8 hours. The pressure in the container was adjusted to 0.05 MPa after heating was started. Next, stirring was stopped, and the colorless and transparent polymer in a molten state was drawn out from the polymer takeout port into a string shape, cooled with water, and pelletized to obtain about 12 kg of pellets. The obtained pellets are white tough and flexible polymers rich in rubber elasticity, ηr = 2.16, [COOH] = 1.28 × 10 ⁻⁵ eq / g, [NH ₂ ] = 1.86 × 10 ^{−. It was 5} eq / g, Mn = 63700, Tm = 135 ° C., Tc = 59 ° C. The polymer composition is PA12 / XTJ-542 / AA = 40.7 / 52.9 / 6.4 (% by weight) (where PA12, XTJ-542 and AA represent each component in the polymer, PA12 is nylon 12 units XTJ-542 represents an ABA type triblock polyether diamine unit, and AA represents an adipic acid unit. The obtained pellets were injection molded to obtain samples for measuring various physical properties. The Shore D hardness and mechanical properties of the obtained sample are as follows.
Shore D hardness: 40, flexural modulus: 76 MPa, flexural strength: 4.3 MPa, tensile yield strength: 6.3 MPa, tensile elongation at break: 300% or more, impact strength: NB, deflection temperature under load: 48 ° C.

Production Example 2 (Production of PAE2)
Ube Industries Co., Ltd. 12-aminododecanoic acid 11.200kg, ABA type in a 70 liter pressure vessel equipped with stirrer, thermometer, torque meter, pressure gauge, nitrogen gas inlet, pressure regulator and polymer outlet Of triblock polyetherdiamine (trade name: XTJ-542, manufactured by HUNTSMAN) and 7.121 kg of adipic acid were charged. After sufficiently replacing the inside of the container with nitrogen, heating was gradually performed while supplying nitrogen gas at a flow rate of 300 liters / minute. The temperature was raised from room temperature to 230 ° C. over 3 hours, and polymerization was carried out at 230 ° C. for 6 hours. The pressure in the container was adjusted to 0.05 MPa after heating was started. Next, stirring was stopped, and the colorless and transparent polymer in a molten state was drawn out from the polymer takeout port into a string shape, cooled with water, and pelletized to obtain about 12 kg of pellets. The obtained pellet is a white tough and flexible polymer rich in rubber elasticity, ηr = 2.22, [COOH] = 1.61 × 10 ⁻⁵ eq / g, [NH ₂ ] = 2.17 × 10 ^{−. It was 5} eq / g, Mn = 52900, Tm = 154 ° C., Tc = 109 ° C. Polymer composition is PA12 / XTJ-542 / AA = 56.5 / 38.9 / 4.6 (% by weight) (where PA12, XTJ-542 and AA represent each component in the polymer, PA12 is nylon 12 unit XTJ-542 represents an ABA type triblock polyether diamine unit, and AA represents an adipic acid unit. The obtained pellets were injection molded to obtain samples for measuring various physical properties. The Shore D hardness and mechanical properties of the obtained sample are as follows.
Shore D hardness: 48, bending elastic modulus: 132 MPa, bending strength: 7.2 MPa, tensile yield strength: 9.2 MPa, tensile breaking elongation: 300% or more, impact strength: NB, deflection temperature under load: 73 ° C.

Production Example 3 (Production of PAE3)
A 70-liter pressure vessel equipped with a stirrer, thermometer, torque meter, pressure gauge, nitrogen gas inlet, pressure regulator, and polymer outlet, Ube Industries, Ltd. 12-aminododecanoic acid 14.000 kg, ABA type 53.6 kg of triblock polyetherdiamine (trade name: XTJ-542, manufactured by HUNTSMAN) and 0.764 kg of adipic acid were charged. After sufficiently replacing the inside of the container with nitrogen, heating was gradually performed while supplying nitrogen gas at a flow rate of 300 liters / minute. The temperature was raised from room temperature to 230 ° C. over 3 hours, and polymerization was carried out at 230 ° C. for 6.5 hours. The pressure in the container was adjusted to 0.05 MPa after heating was started. Next, stirring was stopped, and the colorless and transparent polymer in a molten state was drawn out from the polymer takeout port into a string shape, cooled with water, and pelletized to obtain about 13 kg of pellets. The obtained pellet is a soft polymer with white toughness and rich rubber elasticity, ηr = 2.05, [COOH] = 2.48 × 10 ⁻⁵ eq / g, [NH ₂ ] = 2.82 × 10 ^{− It was 5} eq / g, Mn = 37700, Tm = 163 ° C., Tc = 123 ° C. The polymer composition is PA12 / XTJ-542 / AA = 70.1 / 26.6 / 3.3 (% by weight) (where PA12, XTJ-542 and AA represent each component in the polymer, PA12 is nylon 12 units XTJ-542 represents an ABA type triblock polyether diamine unit, and AA represents an adipic acid unit. The obtained pellets were injection molded to obtain samples for measuring various physical properties. The Shore D hardness and mechanical properties of the obtained sample are as follows.
Shore D hardness: 55, flexural modulus: 232 MPa, flexural strength: 11.9 MPa, tensile yield strength: 14.8 MPa, tensile break elongation: 300% or more, impact strength: NB, deflection temperature under load: 78 ° C.

Reference Examples 1-5
Using a Laboplast mill (manufactured by Toyo Seiki Seisakusho), BR150L, PEA2 and a silane coupling agent (indicated by SC in the table) were charged according to the composition shown in Table 1, and kneaded for 3 minutes at a start temperature of 120 ° C. The temperature at the time of discharging the kneaded product was 160 ° C.

Examples 1-4 and Comparative Examples 1-2
Among the compounding recipes shown in Table 2, the vulcanization accelerator, the kneaded material of the reference example excluding sulfur, NR and the compounding agent are kneaded for 5 minutes at a start temperature of 90 ° C. using a lab plast mill (Toyo Seiki Seisakusho) A primary kneaded product was obtained. At this time, the maximum kneading temperature was 1600C to 1700C.
Next, the primary kneaded product was kneaded with a vulcanization accelerator and sulfur on a 6-inch roll at 60 ° C. to obtain a secondary kneaded product.
Next, the secondary kneaded product was placed in a mold and press vulcanized at 150 ° C. for 15 minutes to obtain a vulcanized product. The physical properties of the resulting vulcanizate were measured, and the results are summarized in Table 2.

From Table 2, it can be seen that the rubber compositions of Examples 1 to 4 have higher hardness and tensile properties than those of Comparative Example 1, and are excellent in wearability, heat generation properties, and fatigue properties.
Moreover, since the comparative example 2 did not mix | blend PAE, hardness and tensile stress were low and heat_generation | fever reduced.

Examples 5-6 and Comparative Examples 3-4
Among the compounding formulations shown in Table 3, vulcanization accelerator, kneaded material of reference examples excluding sulfur, rubber / PAE, and compounding agent are used at Labo Plast Mill (Toyo Seiki Seisakusho) at a start temperature of 90 ° C. for 5 minutes. It knead | mixed and the primary kneaded material was obtained. At this time, the maximum kneading temperature was 1600C to 1700C.
Next, the primary kneaded product was kneaded with a vulcanization accelerator and sulfur on a 6-inch roll at 60 ° C. to obtain a secondary kneaded product.
Next, the secondary kneaded product was placed in a mold and press vulcanized at 150 ° C. for 15 minutes to obtain a vulcanized product. The physical properties of the obtained vulcanizate were measured, and the results are summarized in Table 3.

From Table 3, it can be seen that the rubber compositions of Examples 5 to 6 have higher hardness and tensile properties than those of Comparative Example 3, and are excellent in wearability, heat generation properties, and fatigue properties.
Moreover, since the comparative example 4 did not mix | blend PAE, hardness and tensile stress were low, and abrasion property and exothermic property fell.

Reference Examples 6 and 7
Using a lab plast mill (manufactured by Toyo Seiki Seisakusho), BR14H, PEA and a silane coupling agent (indicated by SC in the table) were charged according to the composition shown in Table 4, and kneaded at a start temperature of 120 ° C. for 4 minutes. The temperature at the time of discharging the kneaded product was 160 ° C.

Examples 7-9 and Comparative Examples 5-6
Among the compounding formulations shown in Table 5, the vulcanization accelerator, the kneaded material of the reference example excluding sulfur, rubber / PAE, and the compounding agent were used at a start temperature of 90 ° C. for 5 minutes using a lab plast mill (manufactured by Toyo Seiki Seisakusho). It knead | mixed and the primary kneaded material was obtained. At this time, the maximum kneading temperature was 1600C to 1700C.
Next, the primary kneaded product was kneaded with a vulcanization accelerator and sulfur on a 6-inch roll at 60 ° C. to obtain a secondary kneaded product. The resulting secondary kneaded product was measured for filler dispersibility (FDI) using RPA2000.
Next, the secondary kneaded product was placed in a mold and press vulcanized at 150 ° C. for 15 minutes to obtain a vulcanized product. The physical properties of the obtained vulcanizate were measured, and the results are summarized in Table 3.

For filler dispersibility (FDI), strain dispersion of storage elastic modulus (G ′) was measured at 120 ° C. and 1 Hz using RPA2000 manufactured by Rheometrics.
Next, FDI = G ′ (42%) / G ′ (1.4%) was calculated, and the comparative example 5 was set as 100 and displayed as an index. The larger the value, the better the dispersibility of the filler.

From Table 5, it can be seen that the rubber compositions of Examples 7 to 9 have better filler dispersibility, higher tensile strength, and better wearability, heat generation and fatigue properties than Comparative Examples 5 and 6. .

Claims (6)

  0.1 to 50 parts by weight of a polyamide elastomer (B) having a melting point of 100 to 180 ° C. and 0.1 to 100 parts by weight of a silane coupling agent (C) with respect to 100 parts by weight of vulcanizable rubber (A). A rubber composition characterized by being blended.   The rubber composition according to claim 1, wherein the soft segment of the polyamide elastomer (B) is a polyether, and the Shore D hardness is 30 to 75.   The rubber composition according to any one of claims 1 to 2, wherein the silane coupling agent (C) is an alkoxysilane.   0.1 to 50 parts by weight of the polyamide elastomer (B) having a melting point of 100 to 180 ° C. and 0.1 to 100 parts of the silane coupling agent (C) with respect to 100 parts by weight of the vulcanizable rubber (A) The rubber composition according to any one of claims 1 to 3, wherein 1 part by weight and 1 to 100 parts by weight of a rubber reinforcing agent (D) are blended. (1) Melting and kneading the vulcanizable rubber (A), the polyamide elastomer (B) and the silane coupling agent (C) at a temperature equal to or higher than the melting point of the polyamide elastomer,
(2) 1 to 100 parts by weight of the melt-kneaded product of (1) and the rubber reinforcing agent (D) and the additive (E) other than (C) and (D) are melt-kneaded at a temperature equal to or higher than the melting point of the polyamide elastomer. The manufacturing method of the rubber composition of Claim 4 characterized by the process. (1) Melting and kneading the vulcanizable rubber (A), the polyamide elastomer (B) and the silane coupling agent (C) at a temperature equal to or higher than the melting point of the polyamide elastomer,
(2) 1 to 100 parts by weight of the melt-kneaded product of (1) and the rubber reinforcing agent (D) and the additive (E) other than (C) and (D) are melt-kneaded at a temperature equal to or higher than the melting point of the polyamide elastomer. The rubber composition according to claim 4, which is produced by a process.