JP2010095604A - Rubber composition - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide a rubber composition having excellent wear resistance, high elasticity, high tensile strength, low heat generation and fatigue by blending a polyamide elastomer having a melting point of 100-180°C with a vulcanizable rubber modified with a silane compound. <P>SOLUTION: The rubber composition is obtained by blending 0.1-50 pts.wt. of the polyamide elastomer (B) having a melting point of 100-180°C with 100 pts.wt. of the vulcanizable rubber (A) modified with a silane compound including an amino group, an epoxy group, or an isocyanate group. <P>COPYRIGHT: (C)2010,JPO&INPIT

Description

  The present invention relates to a rubber composition comprising a vulcanizable rubber modified with a silane compound and a polyamide elastomer having a melting point of 100 to 180 ° C.

Conventionally, as an automobile tire rubber, a rubber composition containing polybutadiene rubber (BR) or styrene-butadiene rubber (SBR) as a main component, and other natural rubber is used.

In recent years, demands for lower fuel consumption of automobiles and driving safety requirements on snow and ice have increased, and automobile tire tread rubber has low rolling resistance (ie, high rebound resilience) and road surface grip on snow and ice (ie, Development of a rubber material having a large wet skid resistance) is desired. However, a rubber having high impact resilience such as polybutadiene rubber (BR) tends to have low wet skid resistance, whereas styrene-butadiene rubber (SBR) has high wet skid resistance but also high rolling resistance. was there.

Conventionally, many methods for chemically modifying a low cisdiene rubber with a modifier in the presence of a lithium catalyst have been proposed as a method for solving the above problems. For example, a method of modifying low cis BR with a benzophenone compound has been proposed in Patent Document 1 and Patent Document 2, and it has been reported that rolling resistance of automobile tires is small, wet skid resistance is large, and impact resilience is also improved. Has been.

In Patent Document 3, Patent Document 4, and Patent Document 5, by reacting a diene rubber having an active alkali metal terminal with a nitroamino compound, a nitro compound, a nitroalkyl compound, etc., it has excellent rebound resilience, low temperature It is stated that a rubber with low hardness can be obtained.

However, low cis BR has insufficient wear resistance, and this problem cannot be solved even by modification. In addition, even the SBR has a low impact resilience, and even after modification, this defect cannot be sufficiently solved.
Thus, methods for improving wear resistance and increasing elasticity by blending resin and fiber with rubber have been widely used, and various proposals have been made.

  For example, Patent Document 6 discloses a rubber composition in which a refined (or shortened fiber) thermoplastic polyamide 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 effect can be obtained with any technique, there is a problem that the tensile strength and the like are lowered, and when used for a tire member or the like, it is further practically excellent in further fuel efficiency. Things were sought.

JP 58-162604 A JP 59-117514 A Japanese Examined Patent Publication No. 6-53766 Japanese Patent Publication No. 6-57769 Japanese Patent Publication No. 6-78450 JP 7-224189 A Japanese Patent Laid-Open No. 10-237221

  It is an object of the present invention to blend a vulcanizable rubber modified with a silane compound with a polyamide elastomer having a melting point of 100 to 180 ° C. so that it has wear resistance, high elasticity, high tensile strength, low heat build-up, and fatigue. The present invention relates to a rubber composition having excellent properties.

  The present invention is characterized in that 0.1 to 50 parts by weight of a polyamide elastomer (B) having a melting point of 100 to 180 ° C. is blended with 100 parts by weight of a vulcanizable rubber (A) modified with a silane compound. The present invention relates to a rubber composition.

  The present invention relates to the rubber composition described above, wherein the silane compound (A) is modified with a silane compound containing an amino group, an epoxy group or an isocyanate group.

The present invention relates to the rubber composition described above, wherein the polyamide elastomer (B) has a hardness (Shore D) of 30 to 65.
About.

  According to the present invention, it is possible to provide a rubber composition excellent in wear resistance, high elasticity, high tensile strength, low heat build-up, and fatigue properties.

[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 vulcanizable rubber monomers such as natural rubber, butadiene rubber (BR), butadiene rubber (VCR) containing syndiotactic-1.2-polybutadiene, isoprene rubber, butyl rubber, chloroprene rubber; acrylonitrile Acrylonitrile-diene copolymer rubbers such as butadiene rubber (NBR), 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). 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.

[Silane compound modifier]
The vulcanizable rubber modifier used in the present invention is preferably a silane compound containing an amino group, an epoxy group or an isocyanate group.

The silane compound having an amino group (preferably an aminoalkyl group bonded to an alkyl group having 1 to 6 carbon atoms) is preferably an aminoalkylalkoxysilane compound. Examples of specific compounds include 3-aminopropyldimethylmethoxysilane, 3-aminopropylmethyldimethoxysilane, 3-aminopropylethyldimethoxysilane, 3-aminopropyltrimethoxysilane, 3-aminopropyldimethylethoxysilane, 3 -Aminopropylmethyldiethoxysilane, 3-aminopropyltriethoxysilane, 3-aminopropyldimethylbutoxysilane, 3-aminopropylmethyldibutoxysilane, 3- (2-aminoethylaminopropyl) dimethoxymethylsilane, N- ( 2-aminoethyl) -3-aminopropyl, 3- (2-aminoethylaminopropyl) dimethoxyethylsilane, 3- (2-aminoethylaminopropyl) dimethoxypropylsilane, 3- (2-aminoethylaminopropylene) 3) Dimethoxybutylsilane, 3- (2-aminoethylaminopropyl) diethoxymethylsilane, 3- (2-aminoethylaminopropyl) trimethoxysilane, 3- (2-aminoethylaminopropyl) triethoxysilane, 3 -(2-aminoethylaminopropyl) tributoxysilane and the like. Among these compounds, 3-aminopropyltrimethoxysilane, 3- (2-aminoethylaminopropyl) dimethoxymethylsilane, and 3- (2-aminoethylaminopropyl) trimethoxysilane are particularly preferable.

Examples of the silane compound having an epoxy group include 2- (3,4-epoxycyclohexyl) ethyltrimethoxysilane, 3-glycidoxypropyldimethoxymethylsilane, 3-glycidoxypropyltriethoxysilane, and 3-glycidide. Examples include xylpropyltrimethoxysilane and 3-glycidoxypropylmethyldiethoxysilane.

Examples of the silane compound containing an isocyanate group include 3-isocyanatopropyltriethoxysilane, 3-isocyanatopropyltrimethoxysilane, and tris- (3-trimethoxysilylpropyl) isocyanurate.

Further, it may be modified with a specific imino group or amino group-containing hydrocarbyloxysilane compound. An aminohydrocarbyloxysilane compound is particularly preferable. As the modification method, the method described in JP-A No. 2003-155381 can be used. When a vulcanizable rubber modified with an aminohydrocarbyloxysilane compound is used, an increase in the Mooney viscosity of the rubber composition with time is suppressed, and fuel economy, fracture characteristics, and abrasion resistance are also achieved.

These modifiers may be used alone or in combination of two or more.

Further, the molecular structure of the silane compound has two or more functional groups, for example, two or more amino groups, two or more imino groups, two or more epoxy groups, two or more isocyanate groups, or a different functional group. It may be a polyfunctional silane compound in which two or more exist.

As a general method for modifying a vulcanizable rubber with a modifier in the present invention, a silane modifier and a vulcanizable rubber may be contacted in an organic solvent to cause a modification reaction, or It can be carried out by directly adding a modifier to the vulcanizable rubber polymerization solution. As other methods, direct kneading modification using an extrusion kneader or the like is also possible.

When the modification reaction rate is slow, aluminum halide or alkyl halide can be used as a catalyst in order to increase the reaction rate. Examples of the aluminum halide include aluminum chloride, aluminum bromide, and aluminum iodide. Examples of alkyl halides include alkyl halides having 1 to 6 carbon atoms, such as ethyl bromide, ethyl iodide, butyl chloride, butyl bromide, and butyl iodide.

The organic solvent used for the modification reaction can be freely used as long as it does not react with vulcanizable rubber. Usually, the same solvent as used for the production of the diene rubber is used. Specific examples thereof include aromatic hydrocarbon solvents such as benzene, chlorobenzene, toluene and xylene, and aliphatic carbonization of 5 to 10 carbon atoms such as n-heptane, n-hexane, n-pentane and n-octane. Examples thereof include hydrogen solvents, cycloaliphatic hydrocarbon solvents such as cyclohexane, methylcyclohexane, tetralin, and decalin. Further, methylene chloride, tetrahydrofuran and the like can also be used.

The temperature of the reaction solution for the modification reaction is preferably in the range of 0 to 100 ° C, and particularly preferably in the range of room temperature to 70 ° C. If the temperature is too low, the modification reaction proceeds slowly, and if the temperature is too high, the polymer is easily gelled. There is no particular limitation on the time for the modification reaction, but it is usually preferably in the range of 0.5 to 6 hours. If the modification reaction time is too short, the reaction does not proceed sufficiently, and if the time is too long, the polymer tends to gel.

The amount of vulcanizable rubber in the modification reaction solution is usually in the range of 5 to 500 g, preferably 20 to 200 g, more preferably 30 to 100 g per liter of solvent.

The amount of the modifier used in the modification reaction is usually in the range of 0.01 to 150 mmol, preferably 1 to 100 mmol, and more preferably 3 to 50 mmol with respect to 100 g of vulcanizable rubber. If the amount used is too small, the amount of elemental nitrogen introduced into the modified vulcanizable rubber will be small and the modification effect will be small. If the amount used is too large, unreacted modifier remains in the modified vulcanizable rubber, which is not preferable because it takes time to remove it.

In carrying out the modification reaction, it is preferable to use a catalyst depending on the type of the modifying agent. The amount of catalyst used in this reaction is usually 0.01 to 100 mmol, preferably 0.05 to 50 mmol, more preferably 0.08 to 20 mmol, relative to 100 g of vulcanizable rubber.

The modified vulcanizable rubber used in the present invention is blended alone or blended with other synthetic rubber or natural rubber, and if necessary, is extended with a process oil, and then a filler such as carbon black, a vulcanizing agent. , Vulcanization accelerators and other ordinary compounding agents are added and vulcanized, and used as rubber compositions that require mechanical properties and wear resistance of various industrial products such as tires, hoses, belts, etc. . The modified vulcanizable rubber can also be used as a plastic material modifier.

[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, and still more preferably 0.3 to 100 parts by weight with respect to 100 parts by weight of the vulcanizable rubber (A). 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 processability 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 the total 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 hardness (Shore D) of the polyether polyamide elastomer is preferably in the range of 30 to 65, more preferably in the range of 35 to 60. 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.

  A rubber reinforcing agent may be blended in the rubber composition according to the present invention, and various carbon blacks, white carbons, silicas, activated calcium carbonates, ultrafine magnesium silicates and the like are particularly mentioned. 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.

A silane coupling agent may be used to mix rubber and silica well.
As the coupling agent, alkylphenol formaldehyde resin initial condensate, acid anhydride, silane coupling agent, titanate coupling agent and the like are preferable.

  The amount of the rubber reinforcing agent used is preferably 1 to 100 parts by weight, more preferably 10 to 80 parts by weight, particularly preferably 20 to 70 parts by weight based on 100 parts by weight of the silane-modified vulcanizable rubber (A). Parts by weight.

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.

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.

  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. In addition, soybean oil may be used.

  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.

  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 adding 0.1 g of sample rubber and 100 ml of toluene into an Erlenmeyer flask and completely dissolving them at 30 ° C., and then in a constant temperature water 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] 2c
(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 used as 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.

[Vulcanized physical properties]
The hardness is measured according to a measurement method defined in JIS-K6253, and the larger the numerical value, the higher the hardness.

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

  For the tensile strength, the tensile strength at break was measured according to JIS-K62511. It shows that tensile strength is so high that a numerical value is large.

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

  Tensile fatigue resistance is measured by using a tensile fatigue tester (manufactured by Yasuda Seiki Seisakusho) to make a 0.5 mmφ scratch in the center of a dumbbell-shaped No. 3 (JIS-K6251) test piece, with an initial strain of 100%, 300 times / The number of times the test piece broke was measured under the condition of minutes. 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 smaller 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) 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 −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 hardness and mechanical properties of the obtained sample are as follows.
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 pellets are white tough and flexible polymers rich in rubber elasticity, ηr = 2.22, [COOH] = 1.61 × 10 −5 eq / g, [NH 2] = 2.17 × 10 −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 hardness and mechanical properties of the obtained sample are as follows.
Hardness: 48, flexural 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 pellets are white tough and flexible polymer rich in rubber elasticity, ηr = 2.05, [COOH] = 2.48 × 10 −5 eq / g, [NH 2] = 2.82 × 10 −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 hardness and mechanical properties of the obtained sample are as follows.
Hardness: 55, flexural modulus: 232 MPa, bending strength: 11.9 MPa, tensile yield strength: 14.8 MPa, tensile breaking elongation: 300% or more, impact strength: NB, deflection temperature under load: 78 ° C.

Claims (4)

  A rubber composition comprising 0.1 to 50 parts by weight of a polyamide elastomer (B) having a melting point of 100 to 180 ° C. per 100 parts by weight of a vulcanizable rubber (A) modified with a silane compound .   The rubber composition according to claim 1, wherein the silane compound (A) is modified with a silane compound containing an amino group, an epoxy group, or an isocyanate group.   3. The rubber composition according to claim 1, wherein the soft segment of the polyamide elastomer (B) is a polyether.   The rubber composition according to any one of claims 1 to 3, wherein the polyamide elastomer (B) has a hardness (Shore D) of 30 to 65.