Method of producing a molecular composite material

Abstract: A method of producing a molecular composite material comprising a rigid aromatic polythiazole and a matrix polymer, comprising the steps of: (a) preparing a homogeneous solution in an organic solvent of a said matrix polymer and an aromatic polythiazole prepolymer, in which hydrogen atoms of thiol groups are replaced by optionally substituted alkyl groups; and (b) removing said organic solvent and heating the mixture of aromatic polythiazole prepolymer and matrix polymer to cause a thiazole ring closure reaction. In this way a molecular composite material having excellent mechanical properties, heat resistance etc. can be produced.

Description: The present invention relates to a method of producing a molecular composite material comprising a rigid aromatic polythiazole and a matrix polymer. Such a molecular composite material is suitable as a structural material for aircraft, automobiles, spacecraft, etc. Recently, to achieve the reduction of weight of aircraft, automobiles, etc., plastic materials called "engineering plastics" having excellent mechanical properties, heat resistance, etc. have been increasingly used. In addition, development has been actively carried out to provide composite materials such as FRPs consisting of plastic materials and high-strength, high-modulus fibers such as carbon fibers. These composite materials are being used in many applications. It is known that the strength of these composite materials largely depends not only on the strength of the plastics and reinforcing fibers but also on the interfacial bonding strength of the fibers to the matrix resins. Also, the impregnating capability of matrix resins into the fiber-reinforced performs affects the ease of production of composite materials and the strength of the resulting products. Accordingly, even when high-strength, high-modulus fibers and resins are used as starting materials, composite materials having excellent strength are not necessarily obtained. In order to overcome the above problems, proposals have been made to develop high-strength polymer blend composites (molecular composite materials) by finely dispersing rigid polymers such as aromatic polyamides, in matrix resins to a molecular level. Aromatic polymers suitable for molecular composite materials include those containing heterocyclic repeating units such as thiazole rings, imidazole rings, oxazole rings, etc. Among them, aromatic polythiazoles having a thiazole ring are highly promising because of their excellent mechanical strength. However, the homogeneous dispersion of a reinforcing polymer in a matrix polymer cannot be achieved if the reinforcing polymer is simply blended with the matrix polymer. This means that simple blending fails to provide a molecular composite material having excellent mechanical properties. Various attempts have been made so far to overcome this problem. Japanese Patent Laid-Open No. 1-287167 discloses a method of producing a polymer composite comprising the steps of introducing a polymer solution mainly containing (A) a reinforcing polymer consisting of a polythiazole having a substantially rod-shaped skeleton and (B) a fusable matrix polymer into a solidification bath, and forming it into a film, the above polymer solution showing an optical anisotropy and being solidified via an apparent, optically isotropic phase after immersion in the solidification bath. Japanese Patent Publication No. 2-7976 discloses a polymer composition comprising a reinforcing polymer (A) consisting of a polythiazole having a substantially rod-shaped skeleton, and a matrix polymer (B) consisting of a less-crystallizable aromatic copolyamide having a glass transition temperature of 200°C or higher and a flow-initiation temperature of 500°C or lower, the weight ratio of A/(A + B) being 0.15 to 0.70. When the aromatic copolyamide is kept at a temperature between its glass transition temperature and its flow-initiation temperature for an arbitrary period of time within 5 hours, the resulting crystals have apparent sizes of 25Å or less. However, in the methods of producing polymer composites as disclosed in Japanese Patent Laid-Open No. 1-287167 and Japanese Patent Publication No. 2-7976, homogeneous dispersions of the reinforcing polymers in matrix polymers are not obtained. This means that the resulting molecular composite materials do not show largely improved mechanical strength, etc. This appears to be due to the fact that the rigid reinforcing polymers and the matrix polymers do not show good compatibility with each other. Thus, proposals have been made to provide a method of producing a molecular composite material of a rigid aromatic polymer without resorting to mixing the rigid aromatic polymer and matrix polymer in an acidic solvent, comprising the steps of homogeneously mixing a prepolymer of the rigid aromatic polymer and a matrix polymer or its prepolymer in an organic solvent, removing the organic solvent and then heating it so that the rigid aromatic polymer is formed from its prepolymer (see Japanese Patent Laid-Open Nos. 64-1760 and 64-1761). By these methods, molecular composite materials having relatively good mechanical strength, etc. can be produced. However, since these molecular composite materials fail to show sufficiently high mechanical strength, further improvement is desired. The insufficient mechanical strength of the conventional molecular composite materials obtained by using aromatic polythiazole prepolymers is due to the fact that in the process of producing the aromatic polythiazole prepolymers, some thiol groups in the prepolymers are subjected to a thiazole ring-closure reaction or a cross-linking reaction, thereby forming insoluble components, and therefore good dispersion of the aromatic polythiazole cannot be achieved. Accordingly, an object of the present invention is to provide a method of producing a molecular composite material having improved mechanical strength, and other properties. We have now found that by reacting an aromatic diaminodithiol compound, in which hydrogen atoms of the thiol groups are replaced by optionally substituted alkyl groups, with a dicarboxylic acid derivative to form an aromatic polythiazole prepolymer, homogeneously dissolving this prepolymer and a matrix polymer in an organic solvent, and heating it after removing the organic solvent, a molecular composite material having the aromatic polythiazole homogeneously dispersed in the matrix polymer can be obtained. The present invention is based upon this finding. Thus viewed from one aspect the present invention provides a method of producing a molecular composite material comprising a rigid aromatic polythiazole and a matrix polymer, comprising the steps of: (a) preparing a homogeneous solution in an organic solvent of a said matrix polymer and an aromatic polythiazole prepolymer, wherein the hydrogen atoms of the thiol groups of the aromatic polythiazole prepolymer have been replaced by optionally substituted alkyl groups, the weight ratio of said aromatic polythiazole prepolymer to said matrix polymer being in the range of from 1:100 to 1:10; and (b) removing said organic solvent and heating the mixture of aromatic polythiazole prepolymer and matrix polymer at a temperature of from 250 to 400°C. Viewed from a further aspect the present invention also provides a method of preparing an aromatic polythiazole prepolymer comprising the steps of: (a) selectively reacting an aromatic diaminodithiol compound salt with an alkyl halide in an alkaline aqueous solvent, so that hydrogen atoms in the thiol groups of the aromatic diaminodithiol compound are replaced by the alkyl groups; and (b) polymerizing the monomer obtained in step (a) with a dicarboxylic acid derivative to form an aromatic polythiazole prepolymer. The alkyl group-substituted aromatic diaminodithiol compound may be synthesized from an aromatic diaminodithiol and an optionally substituted alkyl halide. The aromatic diaminodithiol compound, preferably used in the form of a salt, is a compound conveniently having amino groups and thiol groups on both sides of the residual aromatic group, and the residual aromatic group may be a benzene ring or for example any aromatic ring in which 2 or more benzene rings are condensed. Furthermore, the residual aromatic group may comprise 2 or more benzene rings bonded to each other, such as a biphenyl group. The amino groups and the thiol groups may be bonded to the aromatic residual group symmetrically either with respect to its axis or its central point. Typical examples of such aromatic diaminodithiol compounds are: These aromatic diaminodithiol compounds are prefrably used in the form of salts such as hydrochlorides to prevent their deterioration. The alkyl groups bonded to the thiol groups of the aromatic diaminodithiol compound are optionally substituted alkyl groups eg. C 1-6 or more preferably C 1-4 alkyl groups. Examples of unsubstituted alkyl groups include an isopropyl group, an ethyl group, an n-propyl group, an n-butyl group, a sec-butyl group, a tert-butyl group, etc. Among these, secondary or tertiary alkyl groups are particularly preferable. Examples of substituted alkyl groups include those substituted with a carboxyl group, an ester group, a cyano group, a benzyl group, a halogen group, a nitro group, etc. In the case of such substituent groups, the alkyl groups need not be secondary ones. Examples of such substituted alkyl groups include: -CH 2 CH 2 CN, -CH(CH 3 )CN, In the first two alkyl groups above the alkyl groups bonded to the oxygen atom in the ester bond need not be methyl groups, and may be longer linear alkyl groups. Particularly when the hydrogen atoms in the thiol groups of the aromatic diaminodithiol compound are substituted with an alkyl group having a cyano group, an ester group or a carboxyl group, the resulting prepolymer can undergo a ring closure reaction at a relatively low temperature in the range of 250-350°C. In addition, the resulting prepolymer can easily be dissolved in an organic solvent such as N-methyl-2-pyrrolidone. By selecting an alkyl group having an appropriate length carbon chain (eg. carbon number: about 2 to 5), molecular composite materials having excellent physical and chemical properties can be produced. The above alkyl group may also be used in the form of a halide, namely an alkyl halide. Particularly preferred halides which may be used in the present invention are bromides, chlorides and iodides. The dicarboxylic acid derivatives used in the present invention include acid halides, cyanides, amides and esters, eg. those having carboxylic groups substituted by the following: The residual groups of the dicarboxylic acid derivatives are preferably aromatic groups, eg. halogenated aryl groups, including aryl groups linked by alkyl, haloalkyl, cycloalkyl, SO 2 or oxa groups, specific examples including the following: Particularly preferred as the dicarboxylic acid derivative is terephthalic acid. The dicarboxylic acid derivative may be used either alone or in combination. Matrix polymers suitable for use in the present invention include aramide resins, polyether sulfones, polyetherimides, thermoplastic polyimides, thermosetting polyimides, polyamideimides, etc. Since these resins have excellent compatibility with the aromatic polythiazole prepolymer, they can provide molecular composite materials with excellent mechanical strength. In the production of the composite materials, an aromatic polythiazole prepolymer is preferably first produced. The aromatic polythiazole prepolymer may be produced, for instance, by the following steps: (a) selectively reacting an aromatic diaminodithiol compound salt with an alkyl halide in an alkaline aqueous solvent, so that hydrogen atoms in the thiol groups of the aromatic diaminodithiol compound are replaced by the alkyl groups; and (b) polymerizing the monomer obtained in step (a) with a dicarboxylic acid derivative to form an aromatic polythiazole prepolymer. In step (a), the aromatic diaminodithiol compound salt is reacted with an alkyl halide in an alkaline aqueous solvent. The alkaline aqueous solvent used may be water or a mixture of water and alcohol (ethanol and/or methanol) in which an alkaline salt such as sodium hydroxide is dissolved. By using an alkaline aqueous solvent, the aromatic diaminodithiol compound salt can be easily dissolved, whilst increasing the nucleophilic nature of the thiol groups. This accelerates the substitution reaction of hydrogen atoms in the thiol groups with the optionally substituted alkyl groups. The alkali concentration in the solvent is preferably 30 weight % or less. The substitution reaction may conveniently be conducted at a temperature of 0 to 100°C. When the temperature is less than 0°C, the substitution reaction rate is too small. On the other hand, when it exceeds 100°C, a secondary reaction is likely to take place. The preferred reaction temperature is 0 to 95°C. The reaction time is not specifically restricted, but it is generally about 2 to 24 hours. In order to accelerate the substitution reaction, the solution is preferably stirred. Also, by using an excess of the alkyl halide, the reaction rate can be increased. Furthermore, by adding a phase transfer catalyst such as cetyl trimethyl ammonium chloride, cetyl trimethyl ammonium bromide, n-butyl triphenyl phosphonium bromide, tetraphenyl phosphonium bromide or 18-crown-6, the reaction between the aromatic diaminodithiol compound salt and the alkyl halide can be accelerated. In the reaction of step (a), the reaction of the aromatic diaminodithiol compound salt and the alkyl halide proceeds as follows. Here, the aromatic diaminodithiol compound salt is exemplified by 2,5-diamino-1,4-benzenethiol dihydrochloride: wherein X-R represents an alkyl halide. In step (b), the monomer obtained in step (a) is polymerized with the dicarboxylic acid derivative to synthesize an aromatic polythiazole prepolymer. In this case, the monomer obtained in step (a) and the dicarboxylic acid derivative are mixed in an equimolar ratio, and subjected to polymerization under the conditions as described below. Examples of solvents which may be used in the reaction include N-methyl-2-pyrrolidone, hexamethyl phosphoric triamide, N,N-dimethylacetamide, etc., which may be used either alone or in combination. To increase solubility, chlorides such as LiCl, CaCl 2 , etc. may be added in an amount of up to 10%. The monomer obtained in step (a) and the dicarboxylic acid derivative are dissolved in the above solvent in an equimolar ratio, and subjected to a polymerization reaction at a temperature between -20°C and +100°C. When the polymerization temperature is lower than -20°C, a sufficient polymerization reaction does not take place. On the other hand, when it exceeds +100°C, a side reaction is likely to take place. Incidentally, when it exceeds +50°C, the resulting prepolymer tends to have a low degree of polymerization. Accordingly, the preferred polymerization temperature range is -20°C to +50°C, more preferably -20°C to +30°C. The monomer concentration is preferably about 0.1 to 2 mol/l since when the monomer concentration exceeds 2 mol/l, it cannot generally dissolve completely. In the polymerization reaction of step (b), the solution is preferably stirred to increase the polymerization reaction rate. The polymerization reaction time is not particularly restricted, but it is generally about 1 to 24 hours. Under the above conditions, an aromatic polythiazole prepolymer having a large degree of polymerization can be obtained without causing a ring closure reaction. The resulting aromatic polythiazole prepolymer has an intrinsic viscosity η inh of about 1.0 to 2.0 (measured at a concentration of 0.5 g/dl in N-methyl-2-pyrrolidone, 30°C). In the polymerization reaction of step (b), the reaction between the monomer obtained in step (a) and the dicarboxylic acid derivative proceeds as follows. Here, the monomer obtained in step (a) is exemplified by 2,5-diamino-1,4-benzenedithiol dihydrochloride substituted with alkyl groups, and the dicarboxylic acid derivative is exemplified by terephthalic acid dichloride. wherein n represents the degree of polymerization. When the polymerization reaction is conducted by using two dicarboxylic acid derivatives, a prepolymer in the form of a copolymer as exemplified below can be obtained. wherein Ar and Ar′ respectively represent aromatic groups of the dicarboxylic acids, and m and n represent the numbers of repeating units (polymerization degree). Depending upon the types of dicarboxylic acid derivatives, various copolymers may be obtained. The resulting aromatic polythiazole prepolymer is washed and dried by a known method. The aromatic polythiazole prepolymer obtained by the method as described above and the matrix polymer are then dissolved in an organic solvent which is compatible with both components. Suitable organic solvents for this purpose include N-methyl-2-pyrrolidone, dimethylsulfoxide and N,N-dimethylacetamide. With respect to the proportion of the aromatic polythiazole prepolymer to the matrix polymer, the aromatic polythiazole component may be included in an extremely small amount to achieve reinforcement, but the weight ratio of the aromatic polythiazole to the matrix polymer in the final product is preferably in the range of 1:1000 to 2:1. When the amount of the aromatic polythiazole serving as a reinforcing polymer is too large, it is so dense in the resulting molecular composite material that the aromatic polythiazole molecules undesirably tend to gather together to form clusters, making the dispersion of the aromatic polythiazole poor at a molecular level. Accordingly, the resulting molecular composite material has a poor mechanical strength. The preferred proportion of the aromatic polythiazole prepolymer to the matrix polymer is 1:100 to 1:10. The aromatic polythiazole prepolymer and the matrix polymer may be dissolved in an organic solvent by any method provided that a homogeneous solution is produced. For instance, the aromatic polythiazole prepolymer solution and the matrix polymer solution may be prepared separately, and then mixed to provide a homogeneous solution, or the matrix polymer may be added to a solution in which the prepolymer is dissolved. Also, both components may be added at once to the same organic solvent. The concentration of the final solution is determined such that the total amount of the aromatic polythiazole prepolymer and the matrix polymer is 1 to 20 weight %. The mixing time may depend upon the types of the matrix polymers and the solvents used, but it is preferably 6 hours to 30 days. The mixing temperature is preferably between -15°C and 150°C. The aromatic polythiazole prepolymer solution and the matrix polymer solution may be prepared and mixed with each other preferably in an atmosphere of an inert gas such as a nitrogen gas, an argon gas, etc. or in a vacuum. After the preparation of a homogeneous solution, the organic solvent is evaporated off. This evaporation step is preferably carried out after a film or a yarn is formed by a casting method. Since a solution of the prepolymer substituted with alkyl groups shows a large liquid crystal property, it is easy to form yarns from a solution of the prepolymer and the matrix polymer in an organic solvent. To increase the liquid crystal property of the prepolymer, it is preferable that the alkyl groups bonded to the thiol groups are long. Actually, by taking into consideration the weight loss, etc. of the prepolymer by heating, alkyl groups having a proper length are preferably used. The composite of the aromatic polythiazole prepolymer and the matrix polymer may be dried by a known method. Next, the above composite of the aromatic polythiazole prepolymer and the matrix polymer is heated, so that a thiazole ring closure reaction takes place in the prepolymer thereby producing a molecular composite material. By this heat treatment, the alkyl group (R) is removed from the prepolymer, thereby forming a thiazole ring at that site. As a result, an aromatic polythiazole can be produced. When the aromatic polythiazole prepolymer obtained by the reaction (2) is used as a prepolymer, the poly-p-phenylenebenzobisthiazole having the following structure can be obtained. The ring closure reaction of the prepolymer is conducted by heating at 250-450°C, within which range an actual heating temperature may vary depending on the types of the matrix polymer used. When the heating temperature is less than 250°C, the thiazole ring cannot be formed. On the other hand, when heated at a temperature exceeding 450°C, the polythiazole is likely to thermally decompose. In view of this fact, the upper limit of the heating temperature is preferably 400°C. The heating of the mixture of the prepolymer and the matrix polymer may be conducted at a constant temperature, or according to a heating program in which the heating temperature is changed stepwise. One example of such a heating program comprises maintaining the mixture at 120°C for 30 minutes, heating from 120°C to 350°C over 30 minutes, and then maintaining at 350°C for 30 minutes. By the above method, the aromatic polythiazole prepolymer homogeneously dispersed in the matrix polymer at a molecular level is converted to an aromatic polythiazole. Accordingly, excellent dispersion of the aromatic polythiazole in the matrix polymer to a molecular level can be achieved. This eliminates the problem of poor mechanical strength due to insufficient bonding strength in the interfaces between the aromatic polythiazole molecules and the matrix polymer molecules. Thus, a molecular composite material having excellent mechanical properties can be obtained. According to the present invention, by using an aromatic diaminodithiol compound salt having thiol groups whose hydrogen atoms are replaced by alkyl groups in advance and by polymerizing it with a dicarboxylic acid derivative, the aromatic polythiazole prepolymer can be obtained. The prepolymer can be readily dissolved in various organic solvents, and homogeneous dispersion of the prepolymer in the matrix polymer can be achieved. Since the thiol groups are protected by the alkyl groups, they do not constitute polymerization sites at which a thiazole ring closure reaction may occur, making it unlikely to cause the formation of insoluble components. Also, since the aromatic diaminodithiol compound used has thiol groups whose hydrogen atoms are replaced by alkyl groups, its polymerization reaction with the dicarboxylic acid derivative can be conducted at lower temperatures than in the conventional methods. In addition, by using alkyl groups having substituent groups such as a carboxyl group, an ester group, a cyano group and a benzyl group, etc., the ring closure reaction of the prepolymer can be achieved at an extremely low temperature. Since the prepolymer having alkyl groups substituted with these groups are extremely soluble in organic solvents such as N-methyl-2-pyrrolidone, etc., the polythiazole can be produced without using strong acids. Preferred embodiments of the invention will now be described by way of example and with reference to the accompanying drawings in which: Fig. 1 is a graph showing a heating pattern of a film of Example 1; Fig. 2 is a graph showing the relation between tensile modulus and the amount of polybenzothiazole with respect to a molecular composite material sample of Example 1 and a sample of Comparative Example 1; Fig. 3 is a graph showing the relation between tensile modulus and the amount of polybenzothiazole with respect to a molecular composite material sample of Example 2 and a sample of Comparative Example 2; Fig. 4 is a graph showing the relation between tensile strength and the amount of polybenzothiazole with respect to a molecular composite material sample of Example 2 and a sample of Comparative Example 2; Fig. 5 is a graph showing the relation between tensile modulus and the amount of polybenzothiazole with respect to a molecular composite material sample of Example 3; Fig. 6 is a graph showing the relation between tensile modulus and the amount of polybenzothiazole with respect to a molecular composite material sample of Example 4; Fig. 7 is a graph showing the relation between tensile strength and the amount of polybenzothiazole with respect to a molecular composite material sample of Example 4; and Fig. 8 is a graph showing the relation between tensile modulus and the amount of polybenzothiazole with respect to a molecular composite material sample of Example 5 and a sample of Comparative Example 3. Example 1 (1) Synthesis of Monomer for Prepolymer 21.6 g of sodium hydroxide were dissolved in 300 ml of distilled water, and 30.0 g of 2,5-diamino-1,4-benzenethiol dihydrochloride were added and dissolved in the resulting sodium hydroxide solution whilst stirring and cooling it to 5°C by ice water. 22.4 ml of 3-bromopropiononitrile were dropped into the resulting solution under stirring. In the course of dropping this 3-bromopropiononitrile, 3.0 g of cetyl trimethyl ammonium bromide were added, precipitation took place immediately. Whilst continuing the stirring of the solution, the solution was gradually heated to ambient temperature. 4 hours after keeping the solution at ambient temperature, the resulting reaction product was subjected to suction filtration by a glass filter, and the precipitate was sufficiently washed with distilled water. After washing, it was dried at 60°C in vacuum. A yellowish solid material was obtained in a yield of 38.3 g. The resulting solid was subjected to a recrystallization treatment using methylene chloride to obtain a greenish crystal which was dried in vacuum. The resulting crystal material had a melting point of 130°C. Also, as a result of elemental analysis, the following data were obtained. Elemental Analysis: C 12 H 14 N 4 S 2 Element C H N S Calculation 51.77 5.07 20.12 23.04 Measurement 51.70 5.01 20.02 23.14 Further, as a result of 1 H-NMR measurement, triplet peaks were observed at 2.97 ppm and 2.67 ppm, respectively, and singlet peaks were observed at 4.63 ppm and 6.79 ppm, respectively. - It was confirmed by the above analyses that the resulting crystal material had the following structure: (2) Synthesis of Poly-p-Phenylenebenzobisthiazole Prepolymer Partially Substituted with Chloride 2.784 g of the compound (monomer) obtained in step (1) were dissolved in 20 ml of N-methyl-2-pyrrolidone (NMP). The resulting solution was cooled in a salt ice water bath, and 2.375 g of 2-chloroterephthalic acid chloride were added. The solution was gradually heated to 0°C while stirring and then kept at 0°C. When the solution became viscous, clear, homogeneous and lime-green, the solution was gradually heated to ambient temperature. 3 hours after introducing 2-chloroterephthalic acid chloride, the solution was slowly poured into methanol while stirring. After stirring for 30 minutes, filtration was conducted, and the solvent was removed. The resulting polymer was dried at 60°C for 24 hours in vacuum. The yield was 4.43 g, amounting to 99.5% by weight. This polymer had an intrinsic viscosity η inh of 2.10 (measured at a concentration of 0.5 g/dl in NMP at 30°C by an Ubbelode's viscometer). Elemental analysis of this polymer gave the following results: Elemental Analysis: C 20 H 16 N 4 S 2 Element C H N S Calculated 58.80 3.95 13.72 15.70 Measured 58.63 3.87 13.51 15.55 From the above results, this polymer was identified as a prepolymer of poly-p-phenylenebenzobisthiazole, hydrogen atoms of whose thiol groups were substituted by 3-bromo-propinonitryl groups. (3) Synthesis of Thermosetting Polyimide (Matrix Polymer) 4.3256 g (40 mmol) of p-phenylene diamine were dissolved in 80 ml of NMP at ambient temperature. Next, 11.7689 g of 3,3′-4,4′-biphenyl tetracarboxylic diacid anhydride were added to the above solution, so that a polymerization reaction at 25°C for 3 hours occurred to produce a polyamic acid. (4) Production of Molecular Composite Material The polyamic acid solution obtained in step (3) was further diluted with NMP to prepare a solution of the polyamic acid at a concentration of 10 weight %. Next, the polybenzothiazole prepolymer obtained in step (2) was dissolved in NMP to prepare a prepolymer solution in NMP at 10 weight %. The above two solutions were then mixed to produce two kinds of solutions having polybenzothiazole concentrations of 9 weight % and 17 weight %, respectively, based on the weight of total polymer (polybenzothiazole + matrix polymer). These solutions were occasionally stirred at -15°C and in an argon gas atmosphere for one week, so as not to cause hydrolysis of the polyamic acid. As a result, a homogeneous solution was obtained. Each of the two kinds of solutions were subjected to slip casting on a glass plate using a doctor blade having a thickness of 0.5 mm to produce a film. Each of the films was subjected to a heat treatment in vacuum under the heat treatment program shown in Fig. 1 to produce a film-like molecular composite material. (5) Property Test With respect to the two types of films obtained as described above, a tensile modulus was measured. This measurement was conducted according to JIS K7127. The results are shown in Fig. 2. Comparative Example 1 The matrix polymer (consisting of thermosetting polyimide) of Example 1 was produced into a film in the same manner as in Example 1. The tensile modulus was measured in the same manner as in Example 1, and the results are shown in Fig. 2. Example 2 The polybenzothiazole prepolymer obtained in step (2) of Example 1 and a polyamide-imide powder (AI-10, manufactured by Amoco) as the matrix polymer were used to produce a molecular composite material. In this case, five types of molecular composite materials having polybenzothiazole contents of 7-40 weight % based on the total polymer were produced as follows: First, in the preparation of the homogeneous solution of the prepolymer and the polyamide-imide, NMP was used as an organic solvent, and the components were mixed in an argon atmosphere at ambient temperature. The mixing was carried out for one week while occasionally stirring. Next, the resulting solution was formed into a film by the same slip casting method as in Example 1. After drying the film, it was heated at 350°C for 30 minutes in vacuum. With respect to each of the films thus obtained, the tensile modulus was measured in the same manner as in Example 1. The results are shown in Fig. 3. Further, in each of these films, the tensile strength was measured. This measurement was conducted according to JIS K7127. The results are shown in Fig. 4. Comparative Example 2 The matrix polymer (consisting of polyamide-imide) of Example 2 was formed into a film in the same manner as in Example 2. The tensile modulus was measured in the same manner as in Example 2 and the results are also shown in Fig. 3. Further, as in Example 2, the tensile strength was measured. The results also are shown in Fig. 4. Example 3 The polybenzothiazole prepolymer obtained in step (2) of Example 1 and a thermoplastic polyimide (XU-218, manufactured by Ciba Geigy) as the matrix polymer were used to produce a molecular composite material. In this case, two types of molecular composite materials having polybenzothiazole contents of 5-30 weight % based on the total polymer were produced as follows: First, the homogeneous solution of the prepolymer and the thermoplastic polyimide was obtained by preparing a 10-weight %-polybenzothiazole prepolymer solution in NMP and a 10-weight %-thermoplastic polyimide solution in NMP, and then mixing proper amounts of the two solutions at ambient temperature in an inert gas atmosphere. The mixing was carried out for one week while occasionally stirring. Next, the resulting solution was formed into a film by the same slip casting method as in Example 1. After drying the film, it was heated at 350°C for 30 minutes in vacuum. With respect to each of the films thus obtained, the tensile modulus was measured in the same manner as in Example 1. The results are shown in Fig. 5. Example 4 The polybenzothiazole prepolymer obtained in step (2) of Example 1 and polyether sulfone (VICTREX PES4100G, manufactured by ICI) as the matrix polymer were used to produce a molecular composite material. In this case, two types of molecular composite materials having polybenzothiazole contents of 6 weight % and 12 weight %, respectively, based on the total polymers were produced as follows: First, the homogeneous solution of the prepolymer and the polyether sulfone was obtained by preparing a 10-weight %-polybenzothiazole prepolymer solution in NMP and a 10-weight %-polyether sulfone solution in NMP, and then mixing proper amounts of the two solutions at ambient temperature in an inert gas atmosphere. The mixing was carried out for one week while occasionally stirring. Next, the resulting solution was formed into a film by the same slip casting method as in Example 1. After drying the film, it was heated at 350°C for 30 minutes in vacuum. With respect to each of the films thus obtained, the tensile modulus was measured in the same manner as in Example 1. The results are shown in Fig. 6. Further, the tensile strength was measured in the same manner as in Example 2. The results are shown in Fig. 7. Example 5 In the same manner as in step (2) of Example 1, two types of polybenzothiazole prepolymers having intrinsic viscosities η inh (measured at a polymer concentration of 0.5 g/dl in NMP using an Ubbedobe's viscometer at 30°C) of 1.0 and 2.1, respectively, were produced. Each of the above polybenzothiazole prepolymers was mixed with an aramide resin (TX-1, manufactured by Toray Industries, Inc.) as a matrix polymer to produce a plurality of molecular composite materials each having a polybenzothiazole content of 50 weight % or less based on the weight of total polymer. The homogeneous solution of the prepolymer and the aramide resin was obtained by preparing a 5-weight %-polybenzothiazole prepolymer solution in NMP and a 5-weight %-aramide resin solution in NMP, and then mixing proper amounts of the two solutions at 40°C in an inert gas atmosphere. This mixing was carried out for one week while occasionally stirring. Next, the resulting solution was formed into a film by the same slip casting method as in Example 1. After drying the film, it was heated at 350°C for 30 minutes in vacuum. With respect to each of the films thus obtained, the tensile modulus was measured in the same manner as in Example 1. The results are shown in Fig. 8. Comparative Example 3 The matrix polymer (aramide resin) of Example 5 was formed into a film in the same manner as in Example 5, and its tensile modulus was measured in the same manner as in Example 5. The results are shown in Fig. 8. The molecular composite materials obtained by the method of the present invention have excellent properties such as mechanical strength, heat resistance, solvent resistance, etc., so that they can be used widely for automobile parts, aircraft parts, space equipment, etc.

Claims: A method of producing a molecular composite material comprising a rigid aromatic polythiazole and a matrix polymer, comprising the steps of: (a) preparing a homogeneous solution in an organic solvent of a said matrix polymer and an aromatic polythiazole prepolymer, wherein the hydrogen atoms of the thiol groups of the aromatic polythiazole prepolymer have been replaced by optionally substituted alkyl groups, the weight ratio of said aromatic polythiazole prepolymer to said matrix polymer being in the range of from 1:100 to 1:10; and (b) removing said organic solvent and heating the mixture of aromatic polythiazole prepolymer and matrix polymer at a temperature of from 250 to 400°C. A method as claimed in claim 1 wherein said aromatic polythiazole prepolymer is obtainable by a method comprising the steps of: (a) selectively reacting an aromatic diaminodithiol compound salt with an alkyl halide in an alkaline aqueous solvent, so that hydrogen atoms in the thiol groups of the aromatic diaminodithiol compound are replaced by the alkyl groups; and (b) polymerizing the monomer obtained in step (a) with a dicarboxylic acid derivative to form an aromatic polythiazole prepolymer. A method as claimed in claim 1 or claim 2, wherein said alkyl group is substituted by a carboxyl group, an ester group, a cyano group, a benzyl group, a halogen atom or a nitro group. A method as claimed in claim 2 or claim 3, wherein said dicarboxylic acid derivative is terephthalic acid dichloride. A method as claimed in any one of claims 1 to 4, wherein said matrix polymer is an aramide resin, a polyether sulfone, a polyether imide, a polyimide or a polyamideimide. A method as claimed in any preceding claim, wherein the aromatic polythiazole prepolymer and the matrix polymer are mixed with each other in an inert gas atmosphere or in a vacuum. A method as claimed in any preceding claim, wherein during step (b), the reaction temperature is elevated stepwise within the range of from 250 to 400°C.

Inventors: AKITA HIROSHI, HATTORI TATSUYA, AKITA, HIROSHI, HATTORI, TATSUYA
Applicants: HONDA MOTOR CO LTD, HONDA GIKEN KOGYO KABUSHIKI KAISHA
Application year: 1991
Main classification: C08G75
IPC codes: C08L81, C08L79, C08G73, C08G75, C08L77, C08L101