RUBBER-LIKE POLYMERS FOR TIRE TREADS, A PROCESS FOR THEIR PREPARATION, AND COMPOSITIONS CONTAINING SAID POLYMERS

Abstract: A rubbery polybutadiene or butadiene/styrene copolymer is obtained by polymerisation in a hydrocarbon solvent in the presence of an organolithium compound as catalyst; and reacting the living site on the polymer with a carbodiimide and if required a tri- or higher functional coupling agent, to give a product having a weight average/number average mol. wt. ratio of 1.2 to 3, and Mooney viscosity 20-150. An amino compound may be added to minimise changes in viscosity.

Description: This invention relates to a rubber-like polybutadiene of styrene-butadiene copolymer produced in the presence of an organolithium catalyst which is suitable for treads of fuel-cost-saving tires and all-season tires, a process for their production and compositions containing them. In recent years, automobile tires have been desired which are reduced in rolling resistance from the viewpoint of saving fuel cost and improved in control stability and wet skid properties (breaking capabilities on wet roads) from the viewpoint of the safety of automobiles. On the other hand, in the production of tires for automobile the quality should become more uniform by improving the processability and the productivity should be improved by ameliorating the workability. As methods for reducing the rolling resistance while keeping the wet skid properties of tire, a weight reduction of tire, an optimization of the structure of tire, an improvement of the tread pattern of tire, or/and an improvement of the rubber composition used in tire-tread have been atempted. Among them, the methods for reducing the rolling resistance by improving the rubber composition used in tire tread include using as starting rubber a rubber having a small hysterisis loss, using a carbon black having a larger particle size in place of a carbon black having a smaller particle size, and reducing the amounts of carbon black and oil used in vulcanized rubber. As a method for improving the starting rubber, employment of a polymer having a higher molecular weight was proposed on the basis of conventional information concerning the physical properties of starting rubbers and vulcanized rubbers. However, according to this method, the impact resilience can be improved but the Mooney viscosities of a starting material and compounding ingredients are increased, resulting in a lowering of the processability, so that no great improvement can be made. On the other hand, by changing the formulation so as to reduce the mixing amounts of oil and carbon black, the Mooney viscosities of compounding ingredients are increased, resulting in a lowering of the processability also in this case. Thus, whichever method is employer, it is difficult to effect the improvement without sacrificing the processability. In recent years, it has been found that random styrene-butadiene copolymer rubber having many vinyl linkages and a branched structure are suitably used in tires, and rubbers various in structure are investigated and various proposals have been made. For example, there has been proposed a method in which a styrene-butadiene copolymer rubber having an increased vinyl content has been coupled by use of tin to form a branched styrene-butadiene copolymer rubber; the rolling resistance is improved by adding the butadienes immediately before the coupling reaction to carry out polymerization (JP-A-87407/82 and 162605/83). However, even this method can make no sufficient improvement in the rolling resistance and has been disadvantageous, for example, in that the production process becomes troublesome. There has also been proposed a completely random styrene-butadiene copolymer rubber produced by introducing monomers continuously into a polymerization region having a high stirring efficiency controlled so as to be at a temperature of 80°C or higher to allow polymerization to proceed by use of a catalyst composed of an organolithium compound and a Lewis base (UP 4547560). This polymer showed excellent performance characteristics with respect to tensile strength, impact resilience, low heat-generating properties, wear resistance, and wet skid properties. However, it required further improvements in impact resilience and low heat-generating properties. In addition thereto, as methods for improving the starting rubber, there have been proposed various methods which comprise introducing a functional group into the end of a living polymer. For example, there is a method which comprises producing a living polymer by use of a bifunctional anionic initiator, and then acting thereon an organosulfenyl chloride to introduce an active group to each end of the molecule (JP-B-855/69). However, this method is disadvantageous for industrial application, for example, because it is difficult to obtain a polymer with a high molecular weight both ends of which are living by this method and organosulfenyl chloride is difficult to handle; furthermore the polymer obtained by this method was insufficient in tensile strength or modulus. Further, there is a method which comprises introducing an amino group into the end (JP-A-5938209, DE-A-3309821 and EP-A-150479), but this method is disadvantageous in that the Mooney viscosities of compounding ingredients are greatly increased and impair the processability, and moreover the improvements of the impact resilience, low heat-generating properties, wear resistance and wet skid properties, are insufficient. As another method for introducing a functional group(s) at the terminal of the rubber of the starting material, there is disclosed a method in which a liquid rubber having a hydroxy group or carboxylic group at the terminal is reacted with various compounds so as to obtain a crosslinked product as a soft gel layer for a puncture-less tire (See JP-B-58-53035). This method however can not provide a solid rubber material having excellent performance characteristics with respect to tensile strength, impart resilience, low heat-generating properties and wear resistance without impairing the wet skid properties. Furthermore, with a recent increase of demand for all-season tires from the industrial world, rubber compositions for tire treads should have a higher performance characteristics balance than ever, for example, rubbers used in tire treads should have control capability on snowy or icy roads in cold districts in winter in addition to the conventional rolling resistance capability and wet skid properties, and should be improved in wear resistance. In order to improve the low-temperature performance, of all-season tires, it has been attempted to blend a rubber of natural rubber type, to use an oil or plasticizer having a more satisfactory low-temperature performance or a filler other than carbon black. However, when such various compounding ingredients are used, there is the problem of lowering the mechanical strength due to the compounding ingredients, and therefore the rubber used cannot but be limited in kind to those which are only slightly lowered in mechanical strength, so that the freedom of formulation is not always high. It is therefore the object of the present invention to provide a synthetic rubber and a composition thereof which have excellent performance characteristics with respect to tensile strength, impact resilience, low heat-generating properties and wear resistance without impairing the wet skid properties and the processability. An other object is to provide a process in which this rubber can be obtained. These objects are achieved as claimed in claims 1, 4 and 7. The dependent claims concerns preferred embodiments. One aspect of this invention relates to a polymer having a Mooney viscosity (ML₁+₄, 100°C) of 20 to 150 obtained by modification at the end of polymer by reacting a disubstituted carbodiimide compound having a linkage of the general formula ―N=C=N― or a disubstituted cyanamide compound having a linkage of the general formula =N-C≡N with a living polymer which is rubber-like polybutadiene or a rubber-like butadiene-styrene copolymer having an amount of bound styrene of 45% by weight or less obtained by polymerization in a hydrocarbon solvent using an organolithium catalyst, and which has a vinyl linkage content of the butadiene portion of 10 to 70%, and a molecular weight distribution ( M w/ M n), expressed in terms of the ratio of the weight average molecular weight ( M w) to the number average molecular weight ( M n) as measured by GPC, of 1.2 to 3. The above defined disubstituted carbodiimide compound and disubstituted cyanamide compound will also be shortly designated as "carbodiimide" and "cyanamide" in the following description. At the organolithium catalyst used in this invention, any one may be used so long as it is a hydrocarbon having at least one lithium atom bonded thereto, for example, ethyl lithium, propyl lithium, n-butyl lithium, sec-butyl lithium, tert-butyl lithium, phenyl lithium, propenyl lithium, hexyl lithium; n-butyl lithium and sec-butyl lithium are particularly preferred. These organolithium catalysts may be used either alone or as a mixture thereof. The amount of the organolithium catalyst is usually 0.3 to 3 mmoles, preferably 0.5 to 1.5 mmoles per 100 g of monomer, though depending on the Mooney viscosity of the polymer to be produced. The hydrocarbon solvent used in this invention includes n-butane, n-pentane, iso-pentane, n-hexane, n-heptane, iso-octane, cyclohexane, methylcyclopentane, benzene and toluene; particularly preferable solvents are n-hexane, n-heptane and cyclohexane. These hydrocarbon solvents may be used alone or as a mixture thereof and are used usually in a proportion of 1 to 20 parts by weight per one part of monomer. The bound styrene content of the styrene-butadiene copolymer rubber of this invention is preferably 45% by weight or less. When it exceeds 45% by weight, heat generation is increased and the impact resilience is lowered, resulting in deterioration of the performance characteristics. The bound styrene content is preferably 30% by weight or less. On the other hand, when the bound styrene content is too low, the tensile strength is lowered. Therefore, it is preferably 5% by weight or more. Further, its particularly preferable range is 10 to 30% by weight from the viewpoint of the balance among wet skid, tensile strength, impact resilience and heat generating properties. The vinyl linkage content of butadiene portion of the polybutadiene or styrene-butadiene copolymer rubber of this invention ranges from 10 to 70%, preferably from 15 to 50%. When the vinyl linkage content is too low, the wet skid resistance is low, while the vinyl linkage content is too high, the wear resistance is lowered. The vinyl linkage content is particularly preferably in the range of 20 to 45%. The molecular weight distribution of the styrene-butadiene copolymer rubber of this invention is 1.2 to 3, preferably 1.5 to 2.5. This molecular weight distribution refers to the ratio of the weight average molecular weight ( M w) to the number average molecular weight ( M n) as determined from a calibration curve of standard polystyrenes by using gel permeation chromatography (GPC). When the molecular weight distribution is small, the processability is insufficient, while when the molecular weight distribution is large, the impact resilience and the low heat-generating properties are insufficient. The molecular weight distribution measured by GPC may be either of one-peak type or two-peak type. There may be employed a method for enlarging the molecular weight distribution or increasing the branches by using coupling agents such as silicon tetrachloride, alkyl-silicon trichlorides, dialkylsilicon dichlorides, and tin tetrachloride, or branching agents such as divinyl-benzene, which are usually employed for improving the processability. The styrene-butadiene copolymer rubber of this invention is preferably a random copolymer. The styrene chain distribution of the styrene-butadiene copolymer rubber is analyzed by GPC of the low-temperature ozone degradation product of the copolymer rubber, according to the method of Tanaka. In this method, the styrene chain distribution is analyzed by GPC of a degradation product obtained by subjecting all the double bonds of butadiene to ozone cleavage (Macromolecules, 1983, 16, 1925). In the copolymer rubber of this invention, the amount of isolated styrene, i.e., styrene constituting chains of one styrene unit, is preferably 40% by weight or more, more preferably 50% by weight or more based on the total bound styrene, as analyzed by the above method, and the amount of long-chain block styrene, i.e., styrene constituting chains of 8 or more styrene units, is preferably 5% by weight or less, more preferably 2.5% by weight or less based on the total bound styrene. When the amount of isolated styrene is less than 40% by weight, or when the amount of long-chain block styrene exceeds 5% by weight; the balance between high wet skid resistance and the high impact resilience and low heat-generating properties, which is an excellent characteristic of this invention, is lowered. The disubstitued carbodiimide compound having a linkage of the general formula ―N=C=N― or disubstitued cyanamide compound having a linkage of the general formula > N-C≡N, used in the invention include for example, compounds belonging to dialkylcarbodiimides, alkylarylcarbodiimides, diarylcarbodiimides, dialkylcyanamides, alkylarylcyanamides and diarylcyanamides. These compounds are used alone or as a mixture thereof. Specifically, there are exemplified dimethylcarbodiimide, diethylcarbodiimide, dipropylcarbodiimide, dibutylcarbodiimide, dihexylcarbodiimide, dicyclohexylcarbodiimide, dibenzylcarbodiimide, diphenylcarbodiimide, methylpropylcarbodiimide, butylcyclohexylcarbodiimide, ethylnenzylcarbodiimide, propylphenylcarbodiimide, phenylbenzylcarbodiimide, dimethylcyanamide, diethylcyanamide, dipropylcyanamide, dibutylcyanamide, dihexylcyanamide, dicyclohexylcyanamide, dibenzylcyanamide, diphenylcyanamide, methylpropylcyanamide, butylcyclohexylcyanamide, ethylbenzylcyanamide, propylphenylcyanamide and phenylbenzylcyanamide. Among them, dicyclohexylcarbodiimide, diphenylcarbodiimide and diphenylcyanamide are particularly suitable. These compounds are fed in a proportion of 0.2 to 5 moles, more preferably 0.3 to 3 moles per mole of the living polymer. A still more preferable feeding amount is a proportion of 0.5 to 2 moles. When the feeding amount is too small, only a small improving effect on the physical properties can be obtained, while when the feeding amount is too large, unreacted substances exert influences such as a reduction of the vulcanization time and a lowering of the tensile strength. Therefore, neither of such feeding amounts are desirable. The reaction of the living polymer with the above compounds is very rapid, and the reaction temperature is generally from room temperature to 120°C and the reaction time is from several seconds to several hours. A more preferable polymer can be obtained when the living polymer molecules are combined to form a branched polymer by using a trifunctional or higher-order coupling agent in an amount of 0.1 to 0.7 equivalent, preferably 0.1 to 0.5 equivalent per mole of the living active site, and the said carbodiimide or cyanamide compound is introduced into all of the residual living active sites. In this case, cold flow of the rubber-like polymer is prevented and a rubber-like polymer is obtained which is excellent in processability, excellent in the performance characteristics of the vulcanized product, and well-balanced. When the amount of functional groups of trifunctional or higher-order coupling agent used is less than 0.1 equivalent per equivalent of the living active site, the preventing effect on cold flow is small, resulting in a lowering of the processability, while when it exceeds 0.7 equivalent, the amount of the carbodiimide introduced is dereased, so that the performance characteristics of the vulcanized product are deteriorated. Thus, a preferred embodiment of the polymer of this invention, a polybutadiene or a styrene-butadiene copolymer comprising a branched polymer molecule and a straight-chain polymer molecule wherein (1) 10 to 50% by weight of the molecules constituting the polymer is a branched polymer formed by binding by means of a trifunctional or higher-order coupling agent, and (2) at least 20% by weight, more preferably 30% by weight of the molecules constituting the polymer is a straight-chain polymer having a carbodiimide added thereto. From the viewpoint of the balance between the processability and the two properties, i.e., the impact resilience and low heat-generating properties, it is particularly preferable that the amount of the branched chain polymer molecule ranges from 10 to 40% by weight. When the amount of the straight-chain polymer having the carbodiimide bonded thereto is less than 20% by weight, the improving effects on the impact resilience and the low heat-generating properties are small. Furthermore, from the viewpoint of improving the impact resilience and the low heat-generating properties, it is particularly preferable that the total amount of the branched polymer molecule and the straight-chain polymer molecule having the carbodiimide bonded thereto is 50% by weight or more of the molecules constituting the polymer. Since the reaction of the living polymer with the coupling agent as a branching agent and the said carbodiimide or cyanamide compound is substantially quantitative, the above-mentioned amounts of the branched polymer molecule and straight-chain polymer molecule can be attained by controlling the equivalent ratio between activated lithium and these reactive compounds. The amount of each component in the aforesaid polymer can be measured by separation of each component by GPC, determination of the amount of terminal group of the polymer by use of a reagent reactive to the active terminal group of the polymer, or comparison between the analysis results of GPC before and after the reaction with said carbodiimide or cyanamide compound. The trifunctional or higher-order coupling agent includes polyhalogenated compounds such as trichloromethylsilane, tetrachlorosilane, hexachlorodisilane, tin tetrachloride, butyltin trichloride, tin tetraiodide or carbon tetrachloride; diesters such as diethyl adipate or diphenyl carbonate; compounds having two or more diglycidylamino groups in the molecule such as tetraglycidyl-1,3-bisaminomethylcyclohexane; polyepoxy compounds such as epoxidized liquid polybutadiene; and the compounds described in JP-A-36957/74, such as polyisocyanates, polyimines, polyaldehydes, polyketones or polyanhydrides. Polyhalogenated tins such as tin tetrachloride are particularly preferred. The polymerization reaction, the addition reaction with the said carbodiimide or cyanamide compound and the coupling reaction may be carried out either in a batchwise manner or continuously and are not particularly limited in method to either of these manners. The polymer having an end-modifying group introduced thereinto by reacting the living polymer with these compounds contains usually an antioxidant and if necessary, is subjected to oil extension. Subsequently, the solvent is removed by a conventional method to obtain a polymer. The Mooney viscosity (ML₁+₄, 100°C) of the polybutadiene or styrene-butadiene copolymer of this invention is 20 to 150, preferably 25 to 130. When the Mooney viscosity is below that range, the tensile strength, wear resistance, impact resilience and low heat-generating properties of the vulcanized rubber are insufficient, and an excessive torque is placed on at the time of kneading by means of a roll or a Banbury mixer, or the dispersion of carbon becomes insufficient, resulting in a deterioration of the performance characteristics of the vulcanized rubber. When the rubber-like polybutadiene or styrene-butadiene copolymer modified with the said carbodiimide or cyanamide compound is allowed to stand for a long period of time, its Mooney viscosity is markedly increased, and moreover the Mooney viscosity of a compound obtained by adding compounding ingredients to the above polymer is markedly increased, resulting in difficult processing, and moreover, the important performance characteristics such as impact resilience at high temperatures of the vulcanized rubber are deteriorated. In an other preferred embodiment of this invention the increase of the Mooney viscosity of the rubber-like polymer is prevented by adding an amino compound in a definite proportion is indicated Claim 6 to the inventive polybutadiene or styrene-butadiene copolymer; the obtained polymer is then free from the increase of Mooney viscosity. This rubber-like polymer composition is advantageous, since the performance characteristics of the vulcanized product are also excellent, which makes the composition useful for applications, such as tire treads. For keeping a good processability and maintaining various performance characteristics, it is preferable to add to the rubber-like polybutadiene or styrene-butadiene copolymer of this invention an amino compound in an amount of 0.1 to 40 moles in terms of amino group per mole of the terminal functional group of the polymer. It has been proved that this addition not only prevents the above-mentioned problems but also improves the wear resistance. The amino compound used in this invention includes organic amino compounds of the general formula R n -NH m (wherein R is an alkyl, cycloalkyl, alkylcycloalkyl, aryl, alkylaryl or arylalkyl group having 1 to 20 carbon atoms; n is an integer of 1 to 3; and m is 0, 1 or 2 and satisfies n + m = 3); polyvalent amine or polyamine compounds of the general formula ―NH q -R′-(NH-R′) u -NH r -R s (wherein R is an alkyl, cycloalkyl, alkylcycloalkyl, aryl, alkylaryl or arylalky group having 1 to 20 carbon atoms; R′ is an alkylene, cycloalkylene, alkylcycloalkylene, cycloalkylalkylene, arylene, alkylarylene, arylalkylene or arylcycloalkylene group having 2 to 20 carbon atoms; p is 0, 1 or 2; q is 0, 1 or 2 and satisfies p + q = 2; r is 0, 1 or 2; s is 0, 1 or 2 and satisfies r + s = 2; and u is zero or an integer of 1 to 9); imine compounds, for example, of the general formulas: (wherein R is an alkyl, cycloalkyl, alkylcycloalkyl, aryl, alkylaryl or arylalkyl group having 1 to 20 carbon atoms; R′ is an alkylene, cycloalkylene, alkylcycloalkylene, cycloalkylalkylene, arylalkylene or arylcycloalkylene group having 2 to 20 carbon atoms; and M is an 0 atom or an S atom); nitrogen-containing heterocyclic compounds, etc. Specific examples of the amino compound include ethylamine, propylamine, butylamine, hexylamine, decylamine, octadecylamine, cyclohexylamine, aniline, naphthylamine, toluidine, benzylamine, diethylamine, dibutylamine, dihexylamine, didecylamine, ethylhexylamine, methylpentylamine, dicyclohexylamine, ethylcyclohexylamine, diphenylamine, methylaniline, phenylnaphthylamine, butylbenzylamine, N-methyltoluidine, triethylamine, tributylamine, trihexylamine, tridecylamine, methylethylbutylamine, dimethyloctadecylamine, dimethylcyclohexylamine, N,N-dimethylaniline, methylethylbenzylamine, N,N-dimethyltoluidine, ethylenediamine, propylenediamine, tetramethylenediamine, hexamethylenediamine, 1,12-diaminododecane, 1,4-diaminocyclohexane, m-phenylenediamine, p-phenylenediamine, 3,6-dimethyl-1,4-diaminobenzene, p-aminomethylbenzylamine, N-butylethylenediamine, N-methylpropylenediamine, N-methyl-p-phenylenediamine, N,N′-diethylethylenediamine, N-methyl-N′-butylethylenediamine, N,N′-dimethylhexamethylenediamine, N,N′-dimethyl-p-phenylenediamine, N,N′-dioctyl-p-phenylenediamine, N-ethyl-N′-cyclohexyl-p-phenylenediamine, N-propyl-N′-phenyl-p-phenylenediamine, N,N-diethylethylenediamine, N,N-dibutylethylenediamine, N,N-dimethylhexamethylenediamine, N,N-dimethyl-p-phenylenediamine, 4-N,N-dimethylaminomethylbenzylamine, ethylenediamine, N,N,N′-tributylhexamethylenediamine, N,N,N′,N′-tetrabutylethylenediamine, N,N,N′,N′-tetramethylhexamethylenediamine, diethylenetriamine, triethylenetetramine, tetraethylenepentamine, pentaethylenehexamine, bis(3-aminoethyl)amine, 1,3-bis(3′-aminopropylamino)propane, ethyleneimine, trimethyleneimine, 2-ethylethyleneimine, cyclohexeneimine, pyrrolidine, piperidine, nonamethyleneimine, piperazine, cyclodi(trimethylene)-diimine, N-methylethyleneimine, morpholine, thiomorpholine, pyridine, pyrrole, pyrimidine, triazine, indole, quinoline, purine, etc. Among them, compounds having a primary or secondary amino group are preferred. Further, among these compounds, there are particularly suitably used, for example, polyvalent amine or polyamine compounds such as tetraethylenepentamine, diethylenetriamine, N,N′-dibutylethylenediamine, N,N′-dioctyl-p-phenylenediamine, etc.; imine compounds such as morpholine, thiomorpholine, etc.; and aromatic amine compounds such as toluidine, N-methylaniline, etc. In this invention, as a method for adding the amino compound, there can be employed any of a method comprising batchwise or continuous addition to a solution of a functional group-containing rubber-like polymer obtained by reacting a living polymer with the said carbodiimide or cyanamide compound, a method comprising addition by mechanical kneading after removing the solvent from a solution of said functional group-containing rubber-like polymer by a conventional finishing method, etc. In particular, a method comprising reacting a living rubber-like polymer with the said carbodiimide or cyanamide compound in a solution, successively adding the amino compound to the reaction solution, further adding thereto an antioxidant such as BHT, and then removing the solvent, is preferred. In this case, the preventing effect on the increase of Mooney viscosity of the resulting rubber-like polymer composition is particularly remarkable as compared with other methods. In the case of other methods comprising addition after the reaction, an increase of the Mooney viscosity is observed during the removal of solvent in some cases. In this invention, the adding amount of the organic amino compound is 0.1 to 40 moles, preferably 0.5 to 20 moles, more preferably 1.0 to 15 moles in terms of amino group per mole of the functional group added to the rubber-like polymer. When it is less than 0.1 mole, no preventing effect on the increase of Mooney viscosity of the rubber-like polymer composition is obtained, while when it excess 40 moles, influences, for example, bleeding of the amino compound, and an increase of the vulcanization rate during vulcanization after addition of compounding ingredients are produced, so that troubles are caused. The polybutadiene or styrene-polybutadiene rubber modified with the said carbodiimide or cyanamide compound or the rubber-like polymer formed by adding thereto an amino compound of this invention thus obtained is used as starting rubber, alone or in the form of a blend with other synthetic rubbers and/or natural rubber. In this case, for the exhibition of the excellent characteristics attained by this invention, it is necessary that at least 10% by weight of the starting rubber should be the polybutadiene or styrene-polybutadiene copolymer rubber modified with the said carbodiimide or cyanamide compound of this invention, and this proportion is suitably 30% by weight or more. Particularly when the polymer having an amino compound added thereto is used, it is preferably used in a proportion of 30% by weight or more. The synthetic rubbers or natural rubber other than the polymers of this invention which are used in the form of a blend include styrene-butadiene copolymer rubbers obtained by emulsion polymerization, styrene-butadiene copolymer rubbers obtained by solution polymerization having a 1,2-vinyl content of less than 35%, 1,4-cis-polybutadiene rubbers, 1,2,-syndiopolybutadiene rubbers, polybutadiene rubbers having a 1,2-vinyl content of 10% to 90%, synthetic polyisoprene rubbers, or natural rubber. One or more of them may be used. The synthetic polyisoprene rubbers have a cis-1,4-linkage content of 90% or more. The natural rubber component is necessary not only for improving the processability of the rubber composition of this invention but also for imparting sufficient mechanical strength and low heat-generating properties and good low-temperature performance to the rubber composition in combination with the above-mentioned specific polybutadiene or styrene-butadiene copolymer. The processability, impact resilience, low heat-generating properties, mechanical strength, wear resistance, and low-temperature performance can be highly balanced with one another by using the polybutadiene and/or the styrene-butadiene copolymer of this invention as 30 to 90 parts by weight, preferably 40 to 80 parts by weight of the starting rubber component, and natural rubber or the synthetic polyisoprene rubber as 10 to 70 parts by weight, preferably 20 to 60 parts by weight of the starting rubber component. Furthermore, conjugated-diene-type rubber-like polymers other than the polymers according to this invention can be used as the starting rubber component in such a range that they do not deteriorate the performance characteristics of the above-mentioned rubber composition. Their amount is 0 to 30 parts by weight of the starting rubber component. In addition, as a more preferable rubber-like polymer composition, there is exemplified a composition using, as the above-mentioned polybutadiene or styrenebutadiene copolymer, a polymer comprising a branched polymer molecule and a straight-chain polymer molecule in which (1) said branched polymer molecule is obtained by reacting a trifunctional or higher-order coupling agent with a living polymer and accounts for at least 10 to 50% by weight of said polybutadiene or styrene-butadiene polymer, (2) said straight-chain polymer molecule is obtained by adding the said carbodiimide or cyanamide compound to all the residual living active sites simultaneously with or after the reaction with the coupling agent and accounts for at least 20% by weight of said polybutadiene or styrene-butadiene copolymer, and (3) the styrene content of said polybutadiene or styrene-butadiene copolymer is 0 to 30% by weight. As a particularly preferable rubber-like polymer composition, there is exemplified one which is obtained by further mixing 0 to 30 parts by weight of a conjugated-diene-type rubber polymer other than the polymers of this invention with the above-mentioned rubber-like polymer composition. The rubber-like polymers of this invention can be made into oil-extended rubber, depending on the Mooney viscosity of the rubber component. In this case, as a processing oil, aromatic oil, naphthene oil, and paraffin oil can be used depending on purposes and are usually used in an amount of 5 to 50 parts by weight per 100 parts of the rubber component, and the Mooney viscosity (ML₁+₄, 100°C) of the resulting rubber-like polymer composition is preferably in the range of 20 to 80. When the Mooney viscosity is less than 20, cold flow tends to occur, while when it exceeds 80, torque is placed on at the time of compounding, resulting in difficult processing. The rubber-like polymer composition incorporated with an amino compound of this invention also can be made into oil-extended rubber, depending on the Mooney viscosity of the rubber component. A processing oil used in this case is one which has a total acid value [mg KOH/g] of preferably 0.4 or less, particularly preferably 0.1 or less. When a processing oil having a high total acid value is used, the Mooney viscosity of the rubber-like polymer composition of this invention cannot be sufficient prevented from increasing. A rubber-like composition which is further another aspect of this invention is obtained usually by adding reinforcing carbon black, extender oil for rubber, aliphatic carboxylic acids, sulfur, and vulcanization accelerators to a starting rubber comprising the rubber-like polybutadiene (including those treated with coupling agents) or styrene-butadiene copolymer (including those treated with coupling agents) of this invention, modified at the respective terminals. In addition, if necessary, this composition may contain compounding ingredients for rubber such as vulcanization acceleration assistants, aging resistors, antiozonants, or processing aids. The amount of carbon black in this composition is 10 to 100 parts by weight preferably 20 to 80 parts by weight per 100 parts of the starting rubber. When it is less than 10 parts by weight, the tensile strength and the wear resistance are not sufficient, while when it exceeds 100 parts by weight, the rubber elasticity is greatly lowered. As the carbon black used in the rubber composition of this invention, there are preferably exemplified those having an iodine adsorption amount (IA) of 40 mg/g or more and a dibutyl phthalate oil absorption (DBP) of 70 ml/100 g or more. Such carbon blacks have a uniform and small particle size and are highly structured, and when a carbon black other than them is used, there cannot, in some cases, be obtained a high balance among high tensile strength, high impact resilience and wear resistance which is required of the rubber composition of this invention. Suitable carbon blacks are those having IA of 60 mg/g to 160 mg/g and DBP of 80 ml/100 g to 150 ml/100 g. These carbon blacks include, for example, those called HAF, ISAF and SAF. In the rubber composition of this invention, sulfur is used as a vulcanizing agent in an amount of 0.1 to 5 parts by weight per 100 parts by weight of the starting rubber. When the amount of sulfur is too small, the tensile strength, impact resilience and wear resistance are insufficient, while it is too large, the rubber elasticity is lowered. It is preferably 0.5 to 2.5 parts by weight. In the rubber composition of this invention, conventional various vulcanization accelerators may be used, namely, those of sulfenamide series, guanidine series or thiuram series, in an amount of preferably 0.2 to 3 parts by weight per 100 parts by weight of the starting rubber. Particularly preferably, vulcanization accelerators of thiazole series are used. The vulcanization accelerators of thiazole series are vulcanization accelerators having, as its basic structure, a (wherein R is alkylene or arylene) group. When these vulcanization accelerators are used, a composition having excellent tensile strength, impact resilience and wear resistance can be obtained according to the present invention. These accelerators include suitably vulcanization accelerator M (2-mercaptobenzothiazole), vulcanization accelerator DM (dibenzothiazyl disulfide) and vulcanization accelerator CZ (N-cyclohexyl-2-benzothiazylsulfenamide). As the extender oil for rubber used in the rubber composition of this invention, any one is selected from those used as processing oil usually for formulating rubber, depending on purposes and uses. These extender oils for rubber are classified as paraffin series, naphthene series and aromatic series according to their structures, and the aromatic series ones are suitably used in applications in which the tensile strength and the wear resistance are regarded as important, while not only the naphthene series ones but also the paraffin series ones are suitably used in applications in which the impact resilience and the low-temperature characteristics are regarded as important. The amount of said extender oil for rubber is suitably 5 to 100 parts by weight, preferably 5 to 80 parts by weight, per 100 parts by weight of the starting rubber. When it is less than 5 parts by weight, the processability is low and the dispersion of carbon black becomes insufficient, so that performance characteristics such as tensile strength and elongation are not exhibited, while when it exceeds 100 parts by weight, the tensile strength, impact resilience and the hardness are greatly lowered. Further, in the vulcanized rubber composition, aliphatic carboxylic acids represented by stearic acid are used as vulcanization assistants or processing aids preferably in an amount of 0.5 to 5 parts by weight per 100 parts by weight of the starting rubber component. The rubber compositions of this invention can, if necessary, contain fillers other than carbon black, zinc oxide, antioxidants or wax, at the time of use. The fillers other than carbon black include silicic acid, silicates, calcium carbonate, titanium oxide and various clays. The compositions of this invention are obtained by kneading the above-mentioned ingredients by means of a mixer well known in the rubber industry, for example, an open roll mill, an internal mixer or by various well-known methods. Rubber articles obtained by subjecting these compositions to a vulcanization step have excellent performance characteristics as compared with rubber articles obtained from conventional rubber compositions, are suitable for treads of tire as described above, and are used particularly in cap treads, or under treads of low-fuel-cost tires, all-season tires and high-performance tires. Needless to say, they can be used for purposes other than these purposes, for example, parts of tire such as sidewall, carcass and cushion rubber of tire, rubber vibration insulator, industrial articles by making the most of their excellent performance characteristics. This invention is concretely explained below with reference to several examples but is not limited thereto. In the following examples and comparative examples, all parts are by weight unless otherwise specified. "phm" denotes parts by weight per 100 parts of monomer. Example 1 Two stainless-steel reactors with a capacity of 10 liters equipped with a jacket and a stirrer were connected in series, and continuous copolymerization was carried out using 1,3-butadiene and styrene (75/25 by weight) as monomers, n-hexane as solvent, n-butyl lithium as catalyst in a proportion (phm) of 0.06 g per 100 g of the monomers, 0.60 phm of ethylene glycol dibutyl ether as vinylating agent, and 1,2-butadiene as allene compound in an amount of 0.03 mole per mole of the catalyst. In the first reactor, the internal temperature was controlled so as to be 100°C, and the above-mentioned monomers were fed by means of metering pumps so as to adjust the average residence time to 45 minutes. The polymerization conversions at the outlet of the first reactor were measured by gas chromatography to find that the butadiene polymerization conversion was 97% and the styrene polymerization conversion 95%. The Mooney viscosity (ML₁+₄, 100°C) was measured by means of a Mooney viscometer to be 42. Further, the polymer solution was continuously introduced into the second reactor, and 0.19 phm (1 mole relative to Li) was continously added in the second reactor, and the internal temperature was controlled so as to be 100°C. At the outled of the second reactor, 2,6-di-tert-butyl-p-cresol was added as antioxidant, after which desolvation was carried out by steam stripping and drying was conducted by means of a heated roll at 110°C, whereby there was obtained a styrene-butadiene copolymer rubber having a functional group introduced into the end of polymer. This rubber is defined as evaluation sample A. The Mooney viscosity (ML₁+₄, 100°C) of the rubber obtained was measured by means of a Mooney viscometer to be 43. The amount of bound styrene and the 1,2-vinyl content of butadiene portion were measured by means of an infrared spectrophotometer by the method of Hampton. The amount of the found styrene was 25% by weight, and the 1,2-vinyl content of butadiene portion was 29%. The molecular weight distribution ( M w/ M n) was measured to be 2.2 from results obtained by GPC, by using a calibration curve for polymer of standard polystyrenes. A curve of GPC showed that the molecular weight distribution was of one-peak type. The amount of isolated styrene was 64 wt.% based on the total styrene, as determined from GPC of the ozone degradation product and that of long-chain block styrene was 0.6 wt.%. Next, by use of evaluation sample A as starting rubber, compounds were obtained using N 339 carbon black having (IA) of 90 mg/g and (DBP) of 119 ml/100 g, according to the formulation shown in Table 1 by means of a test Banbury mixer having a capacity of 1.7 liters by method B of the standard compounding and mixing procedure of ASTM-D-3403-75. These compounds were vulcanized and physical properties of each vulcanized compound were measured. The measurements were carried out by the following methods. (1) Hardness and tensile strength; Measured according to JIS-K-6301. (2) Impact resilience: Measured by according to the method of Luepke described as JIS-K-6301, except that the impact resilience at 70°C was measured by heating of a sample in an oven at 70°C for about 1 hour, taking out the sample quickly, and measuring its impact resilience. (3) Goodrich heat generation: A test was carried out by means of a Goodrich flexometer under the conditions of a load of 21,74 kg (48 pounds), a displacement of 0.57 cm (0.225 inch), a starting temperature of 50°C, and a rotation rate of 1800 rpm, and the difference between the raised temperature after 20 minutes and the starting temperature is shown. (4) Wet skid resistance: Measured according to the method of ASTM-E-808-74 by means of a portable skid tester of Stanley-London by using Safety Walk (mfd. by 3 M) as road surface. The results are shown in terms of index, taking the measured value for SBR 1502 as 100. The individual physical properties are tabulated in Table 3. Examples 2 to 4 and 7 to 9, and Comparative Examples 1 to 4. Production of rubbers for evaluation was conducted in the same manner as in Example 1, except that the formulations shown in Table 2 were employed. The rubbers obtained are defined as evaluation samples B to D and G to I, respectively. By use of evaluation samples B to D and G to I, compounds were obtained in the same manner as in Example 1, except that the formulations shown in Table 3 were employed. These compounds were vulcanized and physical properties of each vulcanized compound were measured. The physical properties measured are tabulated in Table 3. Example 5 Two reactors with a capacity of 10 liters equipped with a stirrer and a jacket were connected in series, and 17.9 g/min. of purified 1,3 butadiene and 7.5 g/min. of purified styrene as monomers, 109.3 g/min. of n-hexane as solvent, n-butyl lithium as catalyst in an amount of 0.065 phm relative to the total monomers, and tetramethylethylenediamine in an amount of 0.030 phm relative to the total monomers, were individualy fed from the bottom of the first reactor by means of metering pumps. Further, 4.6 g/min. of purified 1,3 butadiene and 10.7 g/min. of n-hexane were fed from the position of 2/3 of the height of the first reactor, and polymerization was carried out while adjusting the stirring rotation rate to 250 rpm, the internal temperature to 105°C and the average residence time to 45 minutes. The polymer was sampled at the outlet of the first reactor and its Mooney viscosity was measured to be ML 100°C / 1 + 440. Further, the polymer solution was continuously introduced into the bottom of the second reactor, and 0.0065 phm (0.15 equivalent relative to Li) of silicon tetrachloride was continuously added from the bottom. In addition, a n-hexane solution of 0.16 phm (0.75 mole relative to Li) dicyclohexylcarbodiimide was added at the position of 2/3 of the height of the second reactor, and the resulting mixture was subjected to reaction. The temperature of the second reactor was controlled so as to be 100°C. To the polymer solution which had left the second reactor was continuously added 0.75 phm of BHT, and the solvent was removed by heating to recover a polymer. The polymer obtained had a Mooney viscosity of ML 100°C / 1 + 4 60 and a styrene content of 25% by weight, and the microstructure of its butadiene portion was as follows: 1,4-trans-linkage 46%, 1,4 cis linkage 32%, and 1,2-vinyl linkage 22%. Its M w/ M n was 2.2, and a curve of GPC indicated one-peak type.. The amount of isolated styrene determined from GPC of ozone degradation product was 65% by weight based on the total styrene, and that of long-chain block styrene was 0.2% by weight. This polymer is defined as evaluation sample E. This evaluation sample was made into a compound in the same manner as in Example 1, after which the compound was vulcanized and physical properties of the vulcanized compound were measured. The evaluation physical properties of evaluation sample E are tabulated in Table 3. Example 6 An experiment was carried out in the same manner as in Example 5, except that 0.15 phm of diphenylcyanamide (0.75 mole relative to Li) was used in place of dicyclohexycarbodiimide. The polymer thus obtained is defined as sample F. Its evaluated physical properties are similarly tabulated in Table 3. Comparative Examples 5 and 6 An experiment was carried out in the same manner as in Example 1, except that production of rubbers for evaluation was conducted according to the formulations shown in Table 4. Further, compounds were obtained in the same manner as in Example 1 and vulcanized, and physical properties of each vulcanized compound were measured. The physical properties are tabulated in Table 4 together with those of the sample obtained by Example 1. From the results shown in Table 3, the following characteristics of the rubber compositions of this invention are apparent. All of Examples 1 to 6 are compositions of this invention using as rubber component a polymer modified with a disubstituted carbodiimide or a disubstituted cyanamide. Comparison between Examples 1 and 2 and Comparative Example 1 and comparison between Example 4 and Comparative Example 2 show that the compositions of this invention are greatly improved in all of tensile strength, impact resilience, and heat-generating properties as compared with the compositions using a polymer unmodified with the said carbodiimide or cyanamide compound. Example 7 is a composition of this invention using as rubber component a polymer modified at the end so as to have an amount of isolated styrene of as low as 31% as measured by ozone degradation-GPC, and is somewhat inferior to Example 1 but incomparably superior to Comparative Example 1 in performance characteristics. Examples 8 and 9 are rubber compositions using a blend of the polymer of this invention and another rubber, are superior in tensile strength and impact resilience to Comparative Example 3, i.e., a rubber composition using as rubber component a polymer unmodified with a carbodiimide, and have low heat-generating properties. Excellent effects of this invention are exhibited also in the other Examples. From the results shown in Table 4, it can be seen that the polymer modified with the said carbodiimide or cyanamide compound has lower compound Mooney viscosity, better processability, higher tensile strength and impact resilience at high temperatures which is related to fuel cost saving, and lower heat-generating properties, as compared with Comparative Examples 5 and 6 using other modifiers. Examples 10 and 11, and Comparative Example 7 Into a reactor with a capacity of 10 liters equipped with a stirrer were charged 4598 g of cyclohexane, 780 g of purified 1,3-butadiene, 162 g of purified styrene and 38 g of tetrahydrofuran, and the temperature was maintained at 40°C, after which 0.52 g of n-butyl lithium was introduced thereinto to initiate polymerization, and thereafter the polymerization temperature was adiabatically raised. From the time when the internal temperature became 75°C, a mixture of 138 g of butadiene and 322 g of cyclohexane was added by means of a metering pump over a period of 15 minutes. The highest temperature in the reaction was 100°C. One minute after the completion of the addition, 0.132 g of tin tetrachloride (0.25 equivalent relative to Li) was added, and after another 1 minute, 1.26 g of dicyclohexylcarbodiimide (0.75 mole relative to Li) was added and the resulting mixture was subjected to reaction for 20 minutes. Then, 8 g of BHT was added as antioxidant to the polymer solution, after which the solvent was removed by heating to recover a polymer. The polymer obtained (sample J) had a Mooney viscosity (ML 100°C / 1 + 4) of 50, and a styrene content of 15% by weight, and the microstructure of its butadiene portion was as follows: 1,4 trans linkage 34%, 1,4-cis-linkage 23%, and 1,2-vinyl likage 43%. Its M w/ M n was 1.60 and a curve of GPC indicated two-peak type. The styrene content and the microstructure of the butadiene portion were determined by measurement of IR spectrum, followed by calculation by the method of Hampton. The M w/ M n was determined employing GPC (LC-5A mfd. by Shimazu Seisakusho, Ltd., columns: 10⁴, 10⁵ and 10⁶ one each, solvent: tetrahydrofuran, detector: differential refractometer), followed by calculation by a method using a calibration curve prepared using standard polystyrenes. The amount of isolated styrene was 67% by weight based on the total styrene, as determined from GPC of ozone degradation product, and that of long-chain block styrene was 0.8% by weight. The Mooney viscosity of the polymer immediatly before the addition of the tin tetrachloride was 30 and its M w/ M n was 1.10. Further, sample K (Comparative Example 7) was obtained in the same manner as in the case of preparing sample J, except that no reaction with dicyclohexylcarbodiimide was carried out. The polymer obtained had a Mooney viscosity (ML 100°C / 1 + 4) of 53 and a styrene content of 15% by weight, and the microstructure of its butadiene portion was as follows: 1,4-trans linkage 34%, 1,4-cis-linkage 23%, and 1,2-vinyl linkage 43%. Its M w/ M n was 1.65, and the amount of isolated styrene was 65%, while that of long-chain block styrene was 0.8% by weight. The Mooney viscosity of polymer immediately before adding tin tetrachloride was 30, and its M w/ M n was 1.10. The same compounds as in Example 1 were obtained for samples I and J under the compounding conditions shown in Table 1, and then vulcanized, the physical properties of each vulcanized compound were measured. In Example 11, a compound was obtained by use of sample J in the same manner as in Example 1, except for using N-550 carbon black having (IA) of 44 mg/g and (DBP) of 114 ml/100 g, and then vulcanized, and physical properties of the vulcanized compound were measured. The evaluation results are shown in Table 5. Example 12 Into a reactor with a capacity of 10 liters equipped with a stirrer were charged 4920 g of cyclohexane, 918 g of purified 1,3-butadiene, 162 g of purified styrene and 38 g of tetrahydrofuran, and the temperature was maintained at 40°C, after which 0.52 g of n-butyl lithium was introduced thereinto to initiate polymerization, and thereafter the polymerization temperature was adiabatically raised. The highest temperature in the reaction reached 110°C, and 10 minutes after the highest temperature had been reached, 0.132 g of tin tetrachloride (0.25 equivalent relative to Li) was added and after another 1 minute, 1.26 g of dicyclohexylcarbodiimide (0.75 mole relative to Li) was added, after which the resulting mixture was subjected to reaction for 20 minutes. Then, a polymer was recovered in the same manner as in Example 9. The polymer obtained (sample L) had a Mooney viscosity (ML₁+₄, 100°C) of 48 and a styrene content of 15% by weight, and the microstructure of its butadiene portion was as follows: 1,4-trans-linkage 35%, 1,4-cis-linkage 23%, and 1,2-vinyl linkage 42%. Its M w/ M n was 1.60 and a curve of GPC was of two-peak type. The amount of isolated styrene was 46% by weight based on the total styrene, as determined from GPC of ozone degradation product, and that of long-chain block styrene was 7.3% by weight. The Mooney viscosity of the polymer immediately before the addition of the tin tetrachloride was 33 and its M w/ M n was 1.10. Further, a compound was obtained in the same manner as in Example 1 and then vulcanized, and physical properties of the vulcanized compound were measured. The evaluation results are shown in Table 5. Example 10 was incomparably superior to Comparative Example 7 in all of tensile strength, impact resilience and heat-generating properties. Example 11 was a composition of this invention using N-550 carbon black, and though inferior in tensile strength to Example 10, it is excellent in both impact resilience and heat generating properties. Example 12 was a composition of this invention using as rubber component a polymer obtained by modifying at the end a polymer having an amount of long-chain block styrene of 7.3% as determined from GPC of ozone degradation product, and was somewhat inferior to Example 10 but incomparably superior to Comparative Example 7 in impact resilience and heat-generating properties. As described above, effects of this invention are apparent. Example 13 and Comparative Example 8 Preparation of polymers Into a reactor with a capacity of 10 liters equipped with a stirrer and a jacket were charged 4200 g of cyclohexane, 640 g of purified butadiene, 160 g of purified styrene and 60 g of tetrahydrofuran as polar compound, and the temperature was maintained at 50°C, after which 0.34 g of n-butyl lithium was added as catalyst to initiate polymerization. Thereafter, the polymerization reaction was carried out for 60 minutes while maintaining the polymerization temperature at 40 to 85°C, and 0.104 g of tin tetrachloride (equivalent ratio to n-butyl lithium: 0.3) was first added to the resulting living polymer, followed by adding thereto 0.62 g of dicyclohexylcarbodiimide (equivalent ratio to n-bytyl lithium: 0.6), and branching reaction and addition reaction were carried out. Further, 8 g of di-tert-butylhydroxytoluene was added as antioxidant to this polymerization solution, after which the solvent was evaporated to recover a polymer. The polymer obtained (sample M) had a Mooney viscosity (ML₁+₄, 100°C) of 68 and a styrene content of 20% by weight, and the microstructure of its butadiene portion was as follows: 1,4 trans linkage 26%, 1,4-cis linkage 19%, and 1,2-vinyl linkage 55%. According to analysis by GPC of this polymer, the amount of branched polymer molecule was 30%, the M w/ M n was 1.7, the amount of isolated styrene was 62% based on the total styrene, as determined from GPC of ozone degradation product, and the amount of long-chain block styrene was 0%. From analysis of the tin content of the polymer obtained and analysis of the reacting amount of dicyclohexylcarbodiimide, it was confirmed that a substantially objective reaction had been carried out. The Mooney viscosity of the above-mentioned polymer before the branching reaction was 32 and its M w/ M n was 1.15 as measured by GPC. Further, various polymers different in styrene content, microstructure of butadiene portion, branching agent, ratio of branched polymer molecule, etc. were prepared in the same manner as in the preparation of sample M. They were used as polymers within the scope of this invention and for comparison. Their polymer structures were shown in Table 6. The styrene content and microstructure of butadiene portion were determined by measurement of spectra by means of an infrared spectrophotometer, followed by calculation by the method of Hampton. The M w/ M n was measured by a method using GPC (LC-3A mfd. by Shimazu Seisakusho, Ltd., columns: 10⁴, 10⁵ and 10⁶ one each, solvent: tetrahydrofuran, detector: a differential refractometer) and a calibration curve prepared using polystyrenes as standard substances. Among the polymers listed in Table 6, samples M to S and sample W are polymers within the scope of this invention and samples T to V are polymers for comparison. The rubbers listed in Table 7 were prepared as natural rubber and other rubber-like polymers and used for preparing rubber compounds. Example 13 and Comparative Example 8 By use of the polymer listed in Table 6 and the other starting rubbers listed in Table 7, rubber compounds were obtained using the formulation for evaluation No. 1 shown in Table 8 and each starting rubber component having the composition shown in Table 9, by means of a test Banbury mixer having a capacity of 1.7 liters by method B of the standard compounding and mixing procedure of ASTM-D-3403-75. These rubber compounds were vulcanized at 160°C for 20 minutes, and physical properties of the vulcanized compounds and the processability were evaluated according to the following methods. (1) Tensile strength: The same as in Example 1. (2) Impact resilience: The same as in Example 1. (3) Goodrich heat generation: The same as in Example 1. (4) Wet skid resistance: The same as in Example 1. The results are shown in terms of indexes, taking the measured value for Comparative Example 8-5 as 100. (5) Ice skid resistance: The same measuring apparatus as for wet skid resistance was used. Ice having surface temperature of -8°C was used as road surface in a room adjusted to -8°C. The results are shown in terms of index, taking the measured value for Comparative Example 8-5 as 100. (6) Roll processability: A 15,24 cm (6-inch) test roll was used and the handling properties and the wrap of each rubber compound on the roll were observed. A good result was expressed by 4 and bagging without any wrap on the roll by 1. (7) Extrusion processability: A Garvey's die was attached to a Brabender Plastograph and the extrusion rate, the surface texture and the state of edge were observed. The best result was expressed by 4 and the worst result by 1. As is evident from the results on the processability and the physical properties of vulcanized product, the rubber compositions comprising a polybutadiene or a styrene-butadiene copolymer (samples M to R) having a specific structure defined in this invention and natural rubber are excellent not only in processability but also in tensile strength, impact resilience, low heat-generating properties, wet skid characteristics and ice skid characteristics. The rubber composition comprising a styrene-butadiene copolymer (sample W) of this invention and natural rubber is insufficient in ice skid characteristics but excellent in processability, tensile strength, impact resilience, low heat-generating properties and wet skid characteritics. Among the rubber compositions comprising each of samples T to V outside the scope of this invention and natural rubber, the compounds having good processability are insufficient in impact resilience and heat-generating properties, while the compound having good impact resilience and low heat-generating properties is insufficient in processability. Example 14 and Comparative Example 9 The specific polymers according to this invention listed in Table 10 were made into rubber compositions according to the formulation shown in Table 8 as in Example 13, and their processability and physical properties of their vulcanized products were measured. As is evident from the results shown in Table 10, the rubber compositions of Examples 14-1 to 14-13 using as starting rubber component a blend of the specific polymer of this invention and a natural rubber component and/or a synthetic rubber component in the ratio according to this invention, in particular, Examples 14-2 to 14-4 and Examples 14-7 to 14-12 are good in processability and in physical properties of vulcanized product. On the other hand, the rubber composition of Comparative Example 9 is insufficient in the balance between processability and physical properties of vulcanized product. Example 15 and Comparative Example 10 An experiment was carried out in the same manner as in Example 10, and after dicyclohexylcarbodiimide was reacted, each of the amino compounds shown in Table 11 was added and the resulting mixture was stirred continuously for 10 minutes. Subsequently, 8 g of BHT was added as antioxidant to each polymer solution, after which the solvent was removed by heating to obtain a polymer composition. The polymer obtained had a Mooney viscosity [ML₁+₄, 100°C] of 50 and a styrene content of 15% by weight, and the microstructure of its butadiene portion was as follows: 1,4 trans linkage 34%, 1,4 cis linkage 23%, and 1,2 vinyl likage 43%. The Mooney viscosity [ML₁+₄, 100°C] of polymer immediately before adding tin tetrachloride was 30 (Examples 15-1 and 15-2). A polymer composition obtained by the same treatment as described above, except for adding no amino compound, is defined as Example 15-3. Polymer compositions obtained by adding 1.19 g (0.75 mole relative to Li) of diphenylcarbodiimide in place of dicyclohexylcarbodiimide, subjecting the resulting mixture to reaction for 20 minutes, adding the amino compound shown in Table 11, and stirring the resulting mixture continuously for 10 minutes, are defined as Examples 15-4 and 15-5, respectively. A polymer composition obtained by the same treatment as described above, except for adding no amino compound, is defined as Example 15-6. A polymer composition obtained by conducting polymerization, addition of tin tetrachloride, and modification at the end with diphenylcarbodiimide in the same manner as described above, adding 8 g of BHT as antioxidant, thereafter removing the solvent by heating, and mixing the thus obtained polymer with the amino compound shown in Table 11 by means of rolls, was defined as Example 15-7. Comparative Example 10 is a polymer obtained without modification at the end and addition of an amino compound. Example 16 and Comparative Example 11 Two stainless-steel reactors with a capacity of 10 liters equipped with a stirrer and a jacket were connected in series, and continuous polymerization was carried out by using 1,3-butadiene as monomer, n-hexane as solvent, n-butyl lithium as catalyst in a proportion (phm) of 0.050 g per 100 g of the monomer, 0.25 phm of tetramethylethylenediamine as vinylating agent, and 1,2-butadiene as allene compound in an amount of 0.03 mole per mole of the catalyst. In the first reactor, the internal temperature was controlled so as to be 100°C, and the above-mentioned monomer and the like were fed by means of metering pumps so as to adjust the average residence time to 45 minutes. Further, the polymerization solution was continuously introduced into the second reactor, after which each of the carbodiimides or cyanamides shown in Table 11 (1 equivalent relative to Li) was continuously added to the living polymer in the second reactor, and the internal temperature was controlled so as to be 100°C. The amino compound shown in Table 11 was continuously added at the outlet of the second reactor, after which the resulting mixture was introduced into an in-line mixer, and BHT was added as antioxidant. Then, the solvent was removed by means of a drum dryer at 130°C to obtain a polymer composition. The microstructure of the polybutadiene was as follows: 1,4-trans linkage 33%, 1,4-cis linkage 12%, and 1,2-vinyl linkage 65%. The Mooney viscosity [ML₁+₄, 100°C] of the polymer composition immediately after preparation was 54 (Examples 16-1, 16-2 and 16-3). A polymer obtained in the same manner as described above, except for adding no amino compound, was defined as Example 16-4, and a polymer obtained without modification at the end and addition of an amino compound was Comparative Example 11. The Mooney viscosity [ML₁+₄, 100°C] immediately after preparation of Examples 15 and 16 and Comparative Examples 10 and 11 and their Mooney viscosities [ML₁+₄, 100°C] after 1 week, 3 weeks and 6 weeks were measured. The results obtained are shown in Table 11. Further, compounds were obtained by use of each polymer composition after the lapse of 3 months according to the formulation shown in Table 1 in the same manner as in Example 1, and then vulcanized, and physical properties of each vulcanized compound were measured. The wear resistance was measured by means of a pico abrasion tester and expressed in terms of index, taking the measured value for Comparative Example 10 or 11 as 100. Carbon gel in compound polymers of Examples 15-1 and 15-3 and Comparative Example 10 after mixing sulfur were determined to be 35%, 25% and 20%, respectively. The determination of carbon gel was carried out according to the following method: Carbon gel = W G - W O · Ft W O · Fr × 100 wherein Ft: the weight ratio of benzene-insoluble compounding ingredients, Fr: the weight ratio of rubber component, W O : the weight of compound polymer before test (about 0.1 g, divided in 10), W G : the weight after immersion in benzene for 24 hours, followed by taking out, and drying by means of a vacuum dryer at 70°C for 24 hours. Harris'basket used: made of 0,149 mm (10-mesh) brass. Volume of benzene used: 100 cm³ The measurement results of physical properties of the compounds of Example 15 and Comparative Example 10 are shown in Table 12. Similarly, results for Example 16 and Comparative Example 11 are shown in Table 13. The results shown in Tables 11, 12 and 13 show that the addition of an amino compound in this invention, as compared with the case of no addition thereof, leads to effective prevention of the increase of Mooney viscosity after storage for a long period of time, depression of the increase of compound Mooney viscosity after compounding, and excellent performance characteristics of physical properties of vulcanized product. As compared with rubber articles obtained from conventional rubber compositions, the rubber compositions of this invention exhibit excellent performance characteristics, the increase in the Mooney viscosity of their compounds are only slight, and they are excellent in processability, exhibit especially good impact resilience, tensile strength and wet skid properties, and have low heat-generating properties.

Claims: 1. A polymer having a Mooney viscisity (ML₁+₄, 100°C) of 20 to 150 obtained by modification at the end of polymer by reacting a disubstituted carbodiimide compound having a linkage of the general formula ―N=C=N― or a disubstituted cyanamide compound having a linkage of the general formula =N-C≡N with a living polymer which is a rubber-like polybutadiene or a rubber-like butadiene-styrene copolymer having an amount of bound styrene of 45% by weight or less obtained by polymerization in a hydrocarbon solvent using an organolithium catalyst, and which has a vinyl linkage content of the butadiene portion of 10 to 70%, and a molecular weight distribution ( M w/ M n), expressed in terms of the ratio of the weight average molecular weight ( M w) to the number average molecular weight ( M n) as measured by GPC, of 1.2 to 3. 2. A polymer according to Claim 1, comprising a branched polymer molecule and a straight-chain polymer molecule wherein (1) 10 to 50% by weight of the molecules constituting the polymer are a branched polymer formed by binding a trifunctional or higher-order coupling agent to the living sites of the living polymer, (2) at least 20% by weight of the molecules constituting the polymer are a straight-chain polymer having the said carbodiimide or cyanamide compound added thereto, and (3) the styrene content of the polymer is 0 to 30% by weight, the polymer being obtained by bonding a trifunctional or higher-order coupling agent to the living active sites of the living polymer in an amount of 0.1 to 0.7 equivalents per mole of the living active sites, and introducing the said carbodiimide or cyanamide compound into all the other living active sites. 3. A polymer according to claim 1 or 2 further comprising 0.1 to 40 moles, in terms of amino groups of an amino compound, per mole of terminal functional groups of the polymer. 4. A process for producing a rubber-like polybutadiene or a rubber-like butadiene-styrene copolymer according to claim 1 having a Mooney viscosity (ML₁+₄, 100°C) of 20 to 150, characterized by reacting a butadiene monomer or styrene and butadiene monomers in a hydrocarbon solvent in the presence of an organolithium catalyst to obtain a living polymer having a vinyl linkage content of the butadiene portion of 10 to 70%, a molecular weight distribution ( M w/ M n), expressed in terms of the ratio of the weight average molecular weight ( M w) to the number average molecular weight ( M n) as measured by GPC, of 1.2 to 3, and an amount of bound styrene of 45% by weight or less in the case of a copolymer of styrene and butadiene, and reacting the said carbodiimide or cyanamide compound with the living polymer to carry out modification at the end of the polymer. 5. A process for producing a rubber-like polybutadiene or a rubber-like butadiene-styrene copolymer according to claim 4, which comprises reacting a trifunctional or higher-order coupling agent with living active sites of the living polymer in an amount of 0.1 to 0.7 equivalents per equivalent of the living active sites before or simultaneously with the reacting of the said carbodiimide or cyanamide compound, and thereby forming a branched polymer molecule in a portion in the molecule. 6. A process according to claim 1 or 5, wherein 0.1-40 moles, in terms of amino groups, of an amino compound per mole terminal functional groups of the polymer are added to the polymer. 7. A rubber composition for tire treads comprising a blend of 100 parts by weight of a starting rubber containing at least 10% by weight of a polymer according to claim 1, 10 to 100 parts by weight of carbon black, 0.1 to 5 parts by weight of sulfur, and a vulcanization accelerator. 8. A composition according to claim 7, characterized in that the starting rubber contains at least 30% by weight of a rubber-like polymer according to claim 3. 9. A rubber composition for tires according to claim 7, comprising a starting rubber, reinforcing carbon black, an extender oil for rubber, sulfur and a vulcanization accelerator, said starting rubber comprising, in 100 parts by weight of the total of this component, (A) 30 to 90 parts by weight of the polymer according to claim 2, (B) 10 to 70 parts by weight of natural rubber or a synthetic polyisoprene rubber, and (C) 0 to 30 parts by weight of conjugated diene type rubber-like polymers.

Inventors: KITAGAWA, YUICHI, SAITO, AKIRA, YAMADA, HARUO
Applicants: ASAHI KASEI KOGYO KABUSHIKI KAISHA
Application year: 1987
Main classification: C08C19
IPC codes: C08C19, B60C1