POLY(ARYLENE ETHER KETONE), METHOD OF ITS PRODUCTION, AND ITS USE

Abstract: A poly(arylene ether ketone) mainly comprising repeating units represented by general formula (I), wherein Ar¹ represents a 1,5-, 2,6- or 2,7-naphthalene ring or a combination thereof, and Ar² represents a p-phenylene, p,p'-biphenylene, or 1,5-, 2,6- or 2,7-naphthalene ring or a combination thereof. This polymer has a high secondary transition point and excellent solvent resistance and moldability, and can be molded into, for example, heat-resistant fiber and electrical insulation film.

Description: This invention relates to the use of a specific crystalline poly(arylene ether ketone) for producing films or fibers. The invention also relates to a biaxially oriented film of a crystalline poly(arylene ether ketone) and a stretched fiber of a crystalline poly(arylene ether ketone). Polyaryl ether ketones are excellent in chemical resistance, acid resistance, alkali resistance, dimensional stability and mechanical characteristics, and have been studied as engineering plastics, fibers, films, matrices for composite materials, etc. As a polyaryl ether ketone, a polymer wherein an aryl group is a phenylene group has been so far well known. Namely, there have been known a process in which a polyaryl ether ketone comprising recurring units represented by formula (a) is produced by reacting 4,4'-dihalobenzophenone with hydroquinone (JP-A-90296/1979), a process in which a polyaryl ether ketone comprising recurring units represented by formula (b) is produced by reacting 4,4'-dihalobenzophenone with 4,4'-dihydroxybenzophenone (JP-A-22939/ 1982), and a process in which a polyaryl ether ketone comprising recurring units represented by formula (c) is produced by reacting bis(p-halobenzoyl)benzene with hydroquinone (JP-A-34900/1978 and 97094/1978). Heat resistance of these polyaryl ether ketones are not altogether enough, and development of polyaryl ether ketones having excellent heat resistance has been demanded. JP-A-29427/1989 discloses an aromatic polyketone copolymer comprising 15 to 90 mol% of structural units represented by formula (d) and 10 to 85 mol% of structural units presented by formula (e) JP-A-31828/ 1989 discloses an aromatic polyketone copolymer comprising 50 to 85 mol% of structural units represented by formula (e) and 15 to 50 mol% of structural units represented by formula (f) JP-A-33132/1989 involves an aromatic polyketone copolymer comprising 15 to 40 mol% of structural units represented by formula (g) and 60 to 85 mol% of structural units represented by formula (h) W089/04848 includes an arylene ether ketone copolymer comprising (a) 99 to 10 mol% of recurring units represented by formula (I) and (b) 1 to 90 mol% of recurring units represented by formula (II) -Ar-O-Ar-CO- wherein each Ar denotes a m-phenylene group, a p-phenylene group, or a di-m-phenylene group, a di-p-phenylene group, a poly-m-phenylene group or a poly-p-phenylene group in which plural phenylene rings are bound together by a direct bond, -O- or -CO-, and a homopolymer comprising only the recurring units of formula (I). However, W089/04848 does not describe at all a homopolymer wherein the recurring units of formula (I) are those represented by the following formula: EP-A-0 327 984, which is a prior art in all designated Contracting States within the meaning of Article 54(3) and (4) EPC, discloses a poly(arylene ether ketone) consisting of (a) 55-95 mol% of units: (-O-ph-(-Q-ph-) s -O-ph-CO-(-ph-T-) t -ph-) and (b) 5-45 mol% of units: -(-O-Ar 1 -(-Q'-Ar 2 -) s -O-Ar 3 -CO-(-Ar 4 -T'-) t -Ar 5 -)- wherein Ar 1 = phenyl, biphenyl or 1,5-, 2,6-, 2,7-naphthyl, s = 0, t = 1, Ar 3 = phenyl, Ar 4 = 2,6-, 2,7-naphthyl and T' = CO. EP-A-0 315 441 refers to a polymer produced from a monomer compound of the following formula: -ph-O-ph-CO-naphth. -CO-ph-O-ph-, preferably the 2,6-naphthyl form thereof. It is the object of the present invention to provide a new use for a specific crystalline poly(arylene ether ketone) having fiber forming ability and film forming ability. Moreover, it is an object of this invention to provide a biaxially oriented film of a crystalline poly(arylene ether ketone) as well as a stretched fiber of a crystalline poly(arylene ether ketone). The invention is directed to the use of a crystalline poly(arylene ether ketone) having fiber forming ability and film forming ability, and comprising at least 70 mol% of recurring units represented by formula (1) wherein Ar 1 denotes a 2,6-naphthalene ring, and Ar 2 denotes p-phenylene, p,p'-biphenylene, a 2,6-naphthalene ring, or a combination of them, and having inherent viscosity of 0.3 to 2.0 measured at 30°C in conc. sulfuric acid for producing a film or a fiber, wherein said film is a biaxially oriented film having Young's modulus of at least 400 kg/mm 2 and said fiber is a stretched fiber having Young's modulus of at least 1000 kg/mm 2 . Moreover, the invention is directed to a biaxially oriented film of a crystalline poly(arylene ether ketone) comprising at least 70 mol% of recurring units represented by formula (1) wherein Ar 1 denotes a 2,6-naphthalene ring, and Ar 2 denotes p-phenylene, p,p '-biphenylene, a 2,6-naphthalene ring, or a combination of them, and having inherent viscosity of 0.3 to 2.0 measured at 30°C in conc. sulfuric acid produced by heat-polycondensing a starting material composed principally of bis(p-fluorobenzoyl)naphthalene represented by formula (2) wherein Ar 1 is as defined in formula (1) , and an aromatic dihydroxy compound represented by formula (3) HO-Ar 2 -OH wherein Ar 2 is as defined in formula (1), in an inert medium in the presence of at least one alkali compound selected from hydroxides, carbonates and bicarbonates of alkali metals at a temperature of 300 to 360°C, said film having Young's modulus of at least 400 kg/mm 2 . Finally the invention is directed to a stretched fiber of a crystalline poly(arylene ether ketone) comprising at least 70 mol% of recurring units represented by formula (1) wherein Ar 1 denotes a 2,6-naphthalene ring, and Ar 2 denotes p-phenylene, p,p' -biphenylene, a 2,6-naphthalene ring, or a combination of them, and having inherent viscosity of 0.3 to 2.0 measured at 30°C in conc. sulfuric acid produced by heat-polycondensing a starting material composed principally of bis(p-fluorobenzoyl)naphthalene represented by formula (2) wherein Ar 1 is as defined in formula (1) , and an aromatic dihydroxy compound represented by formula (3) HO-Ar 2 -OH wherein Ar 2 is as defined in formula (1), in an inert medium in the presence of at least one alkali compound selected from hydroxides, carbonates and bicarbonates of alkali metals at a temperature of 300 to 360°C, said fiber having Young's modulus of at least 1000 kg/mm 2 . In formula (1), Ar 1 denotes a 2,6-naphthalene ring, represented by formula: In formula (1), Ar 2 denotes p-phenylene, p,p'-biphenylene, a 2,6-naphthalene ring, or a combination of them. Most preferable of these is p-phenylene represented by formula: Thus, as the recurring units of formula (1), recurring units represented by formula wherein Ar 1 is a 2,6-naphthalene ring and Ar 2 is p-phenylene, are especially preferable. The crystalline poly(arylene ether ketone) principally comprises the recurring units of formula (1). As the other recurring units than those of formula (1), for example, the above known recurring units (a)-(h) and those of the following formula are available. The crystalline poly(arylene ether ketone) contains at least 70 mol%, preferably at least 80 mol% of all the recurring units. Above all, the crystalline poly(arylene ether ketone) substantially comprising the recurring units of formula (1) is preferable in this invention. The poly(arylene ether ketone) has inherent viscosity (η inh) of 0.3 to 2.0 measured at 30°C in conc. sulfuric acid. Inherent viscosity is preferably 0.4 to 2.0, more preferably 0.5 to 1.5. Desirous moldability is achieved by a poly(arylene ether ketone) having the above suitable inherent viscosity. The high second-order transition temperature is one of the characteristics of the poly(arylene ether ketone). The second-order transition temperature (Tg) is preferably at least 170°C, more preferably at least 175°C as measured by differential scanning calorimetry (DSC). The melting point (Tm) is preferably 300°C to 380°C, more preferably 320 to 370°C as measured by DSC. The poly(arylene ether ketone) can be produced, according to this invention, by a process characterized by heat-polycondensing a starting material composed principally of bis(p-fluorobenzoyl)-naphthalene represented by formula (2) wherein Ar 1 is as defined in formula (1), and an aromatic dihydroxy compound represented by formula (3) HO-Ar 2 -OH wherein Ar 2 is as defined in formula (1), at a temperature of 300 to 350°C in an inert medium in the presence of at least one alkaline compound selected from the group consisting of hydroxides, carbonates and bicarbonates of alkali metals to produce a crystalline poly(arylene ether ketone) principally comprising the recurring units of formula (1) and having inherent viscosity of 0.3 to 2.0 measured at 30°C in conc. sulfuric acid. In formula (2), Ar 1 is as defined in formula (1). The bis(p-fluorobenzoyl)naphthalene of formula (2) therefore includes bis-1,5-(p-fluorobenzoyl)naphthalene, bis-2,6-(p-fluorobenzoyl)naphthalene, bis-2,7-(p-fluorobenzoyl)naphthalene, and a combination of them. In formula (3), Ar 2 is as defined in formula (1). The aromatic dihydroxy compound of formula (3) therefore includes hydroquinone, 4,4'-dihydroxybiphenyl, 1,5-dihydroxy naphthalene, 2,6-dihydroxynaphthalene, 2,7-dihydroxynaphthalene and a combination of them. The production process is performed by heating a starting material principally comprising bis(p-fluorobenzoyl)naphthalene of formula (2) and the aromatic dihydroxy compound of formula (3) in an inert solvent in the presence of an alkali compound. Examples of the other starting compound that can be used besides the compounds of formula (2) and (3) are 4,4'-difluorobenzophenone, 1,4-bis(p-fluorobenzoyl)-benzene, 4,4'-bis(p-fluorobenzoyl)diphenyl, 1,3-bis(p-fluorobenzoyl)benzene, 4,4'-bis(p-fluorobenzoyl)diphenyl ether, 4,4'-dihydroxybenzophenone, 2,2-bis(p-hydroxy-phenyl)propane, bis(p-hydroxyphenyl)sulfone, 4-fluoro-4'-hydroxybenzophenone, 4-chloro-4'-hydroxybenzophenone, 4-(p-fluorobenzoyl)-4'-hydroxydiphenyl ether, 2-(p-fluorobenzoyl)-6-hydroxynaphthalene, and 4-chloro-4'-hydroxydiphenylsulfone. It is advisable that the compounds of formula (2) and (3) are used such that the amount of the aromatic dihydroxy compound of formula (3) is 0.98 to 1.02 mols per mol of bis(p-fluorobenzoyl)naphthalene of formula (2). It is readily understandable that in using the other starting compound, its amount is such that all the starting compounds are reacted with one another to form an aryl ether ketone polymer chain. It is advisable that the compounds of formula (2) and (3) are contained in amounts of at least 70 mol%, especially preferably at least 80 mol% of all the starting materials. Examples of the inert medium used in the reaction include diphenylsulfone, N-methyl-2-pyrrolidone and sulforan. Among them, diphenyl sulfone is most preferable. Examples of the alkali compound include hydroxides, carbonates and bicarbonates of alkali metals. They may be used either singly or in combination. Preferable examples of the alkali compound include potassium hydroxide, sodium hydroxide, potassium carbonate, sodium carbonate, potassium bicarbonate and sodium bicarbonate. Of these, potassium carbonate and sodium carbonate are most preferable. The alkali compound is used at an enough ratio to catch all the fluorine atoms in the starting material, preferably at such ratio that the equivalent of the alkali metal atom is approximately equal to that of the fluorine compound in the starting material. The reaction is conducted by finally heating at a temperature of 300 to 360°C. When the starting material contains a compound having a boiling point lower than 300°C, e.g. hydroquinone, it is advisable to conduct the reaction first at a temperature lower than 300°C, e.g. 200 to 250°C and then finally 300 to 360°C. As the reaction advances, an alkali metal fluoride is formed as a by-product in a reaction system, while the poly(arylene ether ketone) of this invention is formed as an end product. After the polymerization reaction proceeds to a desirous extent, a monofunctional end capping agent can be added to the reaction system to block the terminal hydroxyl group of the resulting polymer with the end capping agent. Preferable examples of the monofunctional end capping agent are p-chlorobenzophenone, p-fluorobenzophenone and methyl chloride. The end-capped polymer shows good stability in molding, e.g. melt-molding. After the polycondensation reaction, the poly(arylene ether ketone) can be isolated from the reaction system by, for example, solidifying the reaction system, pulverizing the resulting product if required, and removing the inert medium and the alkali metal fluoride as the by-product with e.g. acetone, methanol and water by extraction either simultaneously or stepwise. The bis(p-fluorobenzoyl)naphthalene of formula (2) can advantageously be producted by either a method (A) in which an acid halide of a corresponding naphthalenedicarboxylic acid is reacted with at least 2 mols, per mol of the acid halide, of benzene fluoride in a reaction solvent in the presence of Lewis acid or a method (B) in which naphthalene is reacted with at least 2 mols, per mol of naphthalene, of a p-fluorobenzoyl halide in a reaction solvent in the presence of Lewis acid. The above methods (A) and (B) will be clearly explained as follows. The poly(arylene ether ketone) used according to this invention can be used in various fields by utilizing its excellent solvent resistance and high second-order transition temperature. For example, the poly(arylene ether ketone) of this invention is advantageously used to produce fibers, films, matrix resins of fiber-reinforced composite materials and other molded articles. The fibers of the poly(arylene ether ketone) in this invention can be produced from the poly(arylene ether ketone) by melt molding. For instance, the fibers can be obtained by melting said polymer at a temperature of Tm+20°C to Tm+100°C (Tm is a melting point of the polymer), melt extruding it through a spinneret, and cooling and solidifying the extrudate, followed by winding up. It is advisable to mount a heating cylinder for slowly cooling a spun yarn just under the spinneret. The temperature of the atmosphere in the heating cylinder is desirously Tm-50°C to 600°C. The unstretched fibers obtained by melt spinning are subsequently hot stretched in, or under contact with, a heating medium held at a temperature of at least the glass transition point (Tg) of the poly(arylene ether ketone) but at most its melting point (Tm), preferably at least Tg-10°C but at most Tm-20°C, thereby exhibiting excellent mechanical properties. Stretching can be conducted at one or more stages. Multistage stretching is preferably that first stage stretching is conducted at Tg-10 to Tc-5°C and second stage stretching at Tc to Tc-20°C, and more preferably that first stretching is conducted at Tg-10 to Tc-5°C, second stretching at Tc to Tc+60°C and third stage stretching at (Tc+67°C or second stage stretching temperature+20°C whichever is higher) to Tm-20°C (Tc is a crystallization temperature of an unstretched yarn measured by DSC). This results in high orientation. The fibers of the poly(arylene ether ketone) in this invention are fibers excellent in heat resistance and mechanical characteristics which have a naphthalene ring in the main chain of the starting polymer, are higher in second-order transition temperature than the fibers comprising a polyether ketone composed of a phenylene ring alone and exhibit Young's modulus of more than 1,000 kg/mm 2 by stretching and orientation. The fibers of the poly(arylene ether ketone) in this invention find wide acceptance as industrial fibers. They are useful, for example, as monofilaments in heat-resistant, wear-resistant brushes and dryer canvuses and wear-resistant, highly elastic strings, and as multifilaments in heat-resistant chemical-resistant filters and packings, and matrices for composite materials with high-strength, highly elastic fibers such as inorganic fibers, e.g. glasss fibers, carbon fibers and ceramic fibers or aromatic polyamide fibers. For instance, mixed woven fabrics of the fibers of this invention and the high-strength, highly elastic fibers are hot pressed at a temperature above the melting point of the fibers of this invention to form a fiber-reinforced composite material wherein the poly(arylene ether ketone) is a matrix resin. The film of the poly(arylene ether ketone) of this invention can be formed by melt-molding the poly(arylene ether ketone). Though the film of the poly(arylene ether ketone) can be used in unstretched state, biaxial orientation and crystallization can give a film higher in heat resistance and mechanical strength. Stretching may be either simultaneous biaxial stretching or stepwise biaxial stretching. Multistage stretching is also available. It is preferable that the stretching temperature is (Tg of the unstretched film)-10°C to (Tm of the unstrethed film)-20° (Tg: second-order transition temperature). In the simultaneous biaxial stretching, Tg-10°C to Tc+80°C (Tc: a crystallization temperature) is more preferable. In the stepwise biaxial stretching, it is more preferable that the first stage stretching temperature is T 1 =Tg-10 to Tc+10°C, the second stage stretching temperature is T 2 =T 1 +10°C to (Tc+100°C or Tm-20°C whichever is lower). The stretch ratio is not particularly limited. It is however desirous that an area ratio is at least 4X, especially preferably at least 6X. The stretched film is preferably heat treated at a temperature above a crystallization temperature of the poly(arylene ether ketone) but below its melting point. The temperature of the heat treatment is most preferably Tc+10°C to Tc+100°C. Relaxing heat treatment can be conducted if required. The biaxial orientation and crystallization can give Young's modulus of more than 400 kg/mm 2 and further improve thermal properties. The film of the poly(arylene ether ketone) in this invention preferably exhibits a tan δ peak temperature of higher than 160°C in measuring dynamic viscosity (1Hz) by the biaxial orientation and crystallization. The poly(arylene ether ketone) of this invention has the naphthalene ring in the main chain of the starting polymer and, compared to the polyether ketone composed of the phenylene group alone, shows high second-order transition temperature and good melt-moldability. By stretching and orientation, the film having as high mechanical properties as the commercial polyethylene terephthalate film results. For example, a film having both a second-order transition temperature of higher than 160°C and Young's modulus of higher than 400 kg/mm 2 is provided. The film of the poly(arylene ether ketone) of this invention can find wide use by utilizing these characteristics. For example, it is available in electrically insulating materials, motor insulation, cable covering and high-quality condensers of high use temperatures, as well as in flexible printed circuits, base films for magnetic recording and films for temperature sensitive transfer. The poly(arylene ether ketone) of this invention can be used also as a matrix resin for a fiber-reinforced composite material or as materials of molded articles such as heat-resistant containers and electrical insulating parts. EXAMPLES This invention is illustrated by the following Examples specifically, but is not limited thereto. In said Examples, "parts" mean "parts by weight". The inherent viscosity (η inh) of the polymer was measured at 30°C in conc. sulfuric acid in a concentration of 0.5 g/dl. The second-order tran sition temperature (Tg) and the melting point (Tm) of the polymer were measured by DSC at a ratio of temperature rise of 10°C/min. Example 1 (1) Seventy parts of 2,6-naphthalenedicarboxylic acid chloride, 74 parts of fluorobenzene, 74 parts of AlCl 3 and 200 parts of nitrobenzene were reacted at 80°C for 10 hours with stirring. The reaction mixture was then charged in 1000 parts of methanol, and the precipitate was filtered. The product was 2,6-bis(p-fluorobenzoyl)naphthalene and its amount was 78 parts. The melting point of the product recrystallized with dimethylformamide was 265°C. Elemental analysis of the product showed C=77.2 wt.%, H=3.90 wt.% and F=10.1 wt.%. This product was also ascertained by measurement with IR (nujol method) and NMR (dimethyl sulfoxide-d 6 solvent). (2) A reaction vessel fitted with a stirrer and a distillation system was charged with 37.24 parts of 2,6-bis(p-fluorobenzoyl)naphthalene obtained in (1) above, 11.1 parts of hydroquinone and 67 parts of diphenyl sulfone, purged with nitrogen and then heated at 200°C. About 15 minutes later, the contents were melted into a uniform solution. Subsequently, 4.15 parts of anhydrous potassium carbonate and 7.42 parts of anhydrous sodium carbonate were added, and the mixture was reacted in a nitrogen stream under normal pressure at 200°C for 1 hour and then at 250°C for 1 hour. The reaction temperature was then raised to 340°C. When the reaction was run at the same temperature for 90 minutes, the reaction product gradually became viscous. The resulting reaction product was cooled and pulverized into chips having a particle size of 500 micrometers or less, and then said chips were extracted twice under reflux in acetone, twice under reflux in water and once under reflux in acetone, followed by removing diphenyl sulfone and the inorganic salts. The resulting polymer had η inh=1.08, Tg=178°C and Tm=367°C. Example 2 A reaction vessel fitted with a stirrer and a distillation system was charged with 4.47 parts of 2,6-bis(p-fluorobenzoyl)naphthalene, 1.92 parts of 2,6-dihydroxynaphthalene and 23.6 parts of diphenyl sulfone, purged with nitrogen and then heated at 250°C. About 10 minutes later, the contents were melted into a uniform solution. Subsequently, 1.66 parts of anhydrous potassium carbonate was added, and the mixture was reacted in a nitrogen stream at 250°C for 120 minutes under normal pressure and then heated to 300°C, followed by the reaction for 60 minutes. The resulting reaction product was cooled and pulverized into chips having a particle size of 500 micrometers or less. Said chips were extracted thrice under reflux in acetone and thrice under reflux in water. Diphenyl sulfone and the inorganic salts were removed, and the residue was dried at 150°C for 4 hours. The resulting polymer had η inh=0.86, Tg=196°C and Tm=354°C. Example 3 The polymer obtained in Example 1 was dried at 200°C for 4 hours, and injection-molded at a barrel temperature of 390°C and a mold temperature of 160°C with a molding cycle of about 2 minutes. The properties of the resulting molded article (plate) are as follows, ensuring that the polymer of this invention was excellent in heat resistance and mechanical properties. Heat distortion temperature (load 18.5 kg) 185°C Tensile strength 1020 kg/cm 2 Tensile modulus 18900 kg/cm 2 Elongation at break 42 % Flexural strength 2190 kg/cm 2 Flexural modulus 33300 kg/cm 2 Impact strength (Izod, notched) 6.6 kg.cm/cm Example 4 The same reaction vessel as used in Example 2 was charged with 4.47 parts of 2,6-bis(p-fluorobenzoyl)-naphthalene, 1.92 parts of 2,7-dihydroxynaphthalene and 13.8 parts of diphenyl sulfone, purged with nitrogen and then heated at 250°C. About 10 minutes later, the contents were melted into a uniform solution. Subsequently, 1.66 parts of anhydrous potassium carbonate was added, and the mixture was reacted at 250°C for 60 minutes under normal pressure, and then heated to 300°C, followed by the reaction for 60 minutes. The temperature was further raised to 320°C and the reaction was run for 30 minutes. The reaction product was then cooled and pulverized into chips. Said chipes were extracted and dried as in Example 2. The resulting polymer had η inh=0.91, Tg=196°C and Tm=330. Example 5 Using a Koka-type flow tester, the polymer obtained in Example 2 was melt-extruded at 390°C through a nozzle 0.5 mm in diameter and 1 mm in length. As a result, pale yellow, transparent, tough monofilaments were obtained. Example 6 The polymers obtained in Examples 2 and 4 were dipped in solvents, i.e. methanol, acetone, xylene, trichlene and dioxane at room temperature for 10 days, but dissolution and swelling did not occur at all. Example 7 A polyaryl ether ketone comprising the recurring units represented by formula and having an inherent viscosity of 0.6, which was produced in the same way as in Example 1 was melted at 400°C, and then spun at a spinneret temperature of 390°C using an ordinary spinneret 0.2 mm in diameter and 0.6 mm in length. The spun yarns were passed through a heating cylinder having a temperature of 380°C, then cooled with air and wound up at a rate of 30 m/min. Tm of the polymer was 367°C. The spun yarns had Tg=176°C and Tc=215°C. The unstretched yarns were stretched to 3.4 times at 180°C and heat treated with a fixed length at 240°C. The properties of the resulting fibers are as follows. Young's modulus 1032 kg/mm 2 Tensile strength 57 kg/mm 2 Tensile elongation 9 % Examples 8 to 10 The experiments were run in the same way as in Example 7 except that the heat treatment was conducted at 260 to 300°C. The properties of the resulting fibers are shown in Table 1. Heat treatment temperature (°C) Young's Modulus (kg/mm 2 ) Tensile strength (kg/mm 2 ) Tensile elongation (%) Example 8 260 1042 58 9 Example 9 280 1021 57 9 Example 10 300 1000 56 8 Example 11 Unstretched yarns were obtained in the same way as in Example 7 except that the inherent viscosity of the polymer used was 0.8. Said unstretched yarns were stretched to 3.4 times at 180°C and then to 1.15 times at 260°C. The properties of the resulting fibers are as follows. Young's modulus 1047 kg/mm 2 Tensile strength 70 kg/mm 2 Tensible elongation 10 % Examples 12 to 15 The same unstretched yarns as used in Example 11 were stretched at three stages under the conditions shown in Table 2. 1st stage stretching 2nd stage stretching 3nd stage stretching Young's modulus (kg/mm 2 ) Tensile strength (kg/mm 2 ) Tensile elongation (%) Temp. Ratio Temp. Ratio Temp. Ratio Example 12 180 2.3 240 1.57 280 1.25 1071 71 7 Example 13 180 2.3 240 1.57 280 1.31 1095 70 6 Example 14 180 2.3 240 1.57 300 1.38 1188 70 6 Example 15 180 2.3 240 1.57 320 1.38 1097 69 7 Example 16 A polyaryl ether ketone comprising recurring units represented by formula and having inherent viscosity of 0.8 was extracted at 390°C by an extruder and cast onto a casting drum kept at 100°C to obtain a 100 micrometer-thick unstretched film. Tm of the polymer was 367°C. The unstretched film had Tg=176°C and Tc=215°C measured by DSC. The unstretched film was subjected to simultaneous biaxial stretching at an area ratio of 6X at 180°C, and then heat treated at 250°C under a fixed area. The obtained film showed excellent mechanical property of Young's modulus of 460 kg/mm 2 . Regarding the heat-treated film, Tg by DSC was not measured and a tan δ peak temperature corresponding to a glass transition temperature in measurement of dynamic viscosity was 191°C (1 Hz). The inherent viscosity was measured at 30°C in conc. sulfuric acid in a concentration of 0.5 g /dl by RSA-II (a tradename for a machine of Rheometrics) with an expansion/contraction mode. Example 17 A reaction vessel fitted with a stirrer and a distillation system was charged with 37.24 parts of 2,6-bis(p- fluorobenzoyl)naphthalene, 9.91 parts of hydroquinone, 1.86 parts of 4,4'-dihydroxydiphenyl and 70 parts of diphenyl sulfone, purged with nitrogen and then heated at 200°C. About 15 minutes later, the contents were melted into a uniform solution. Then, 12.5 parts of anhydrous potassium carbonate was added, and the mixture was reacted in a nitrogen stream at 200°C for 1 hour under normal pressure, then at 250°C for 1 hour and further at 340°C for 120 minutes. The resulting polymer was pulverized into chips having a particle size of 500 micrometers or less, and said chips were extracted twice under reflux in acetone, twice under reflux in water and once under reflux in acetone. The obtained polymer had η inh=0.68, Tg=175°C and Tm=366°C. Example 18 Polymerization was carried out as in Example 17 except that the amount of hydroquinone was changed into 7.71 and the amount of 4,4'-dihydroxydiphenyl into 5.59 parts, respectively. The resulting polymer had η inh=0.76, Tg=179°C and Tm=339°C. Example 19 The unstretched yarns obtained in Example 7 and carbon fibers (TORAYCA T-300: a tradename for a product of Toray Industries, Inc.) were interweaved such that a volume of the carbon fibers became about 60 % to prepare a mixed fabric. Eight plies of the mixed fabric were laminated, and the laminate was put in a mold frame and molded under the following temperature and pressure conditions. 1) 300 to 350°C, 10 kg/cm 2 2) pumping at 350°C (0 to 30 kg/cm 2 , 10 times) 3) elevated to 400°C (30 kg/m 2 ) and then kept for 20 minutes 4) cooled to 150°C The resulting molded sample had excellent surface properties, showed a heat distortion temperature of 300°C or higher and was quite tough.

Claims: Use of a crystalline poly(arylene ether ketone) having fiber forming ability and film forming ability, and comprising at least 70 mol% of recurring units represented by formula (1) wherein Ar 1 denotes a 2,6-naphthalene ring, and Ar 2 denotes p-phenylene, p,p'-biphenylene, a 2,6-naphthalene ring, or a combination of them, and having inherent viscosity of 0.3 to 2.0 measured at 30°C in conc. sulfuric acid for producing a film or a fiber, wherein said film is a biaxially oriented film having Young's modulus of at least 400 kg/mm 2 and said fiber is a stretched fiber having Young's modulus of at least 1000 kg/mm 2 . A biaxially oriented film of a crystalline poly(arylene ether ketone) comprising at least 70 mol% of recurring units represented by formula (1) wherein Ar 1 denotes a 2,6-naphthalene ring, and Ar 2 denotes p-phenylene, p,p '-biphenylene, a 2,5-naphthalene ring, or a combination of them, and having inherent viscosity of 0.3 to 2.0 measured at 30°C in conc. sulfuric acid produced by heat-polycondensing a starting material composed principally of bis(p-fluorobenzoyl)naphthalene represented by formula (2) wherein Ar 1 is as defined in formula (1) , and an aromatic dihydroxy compound represented by formula (3) HO-Ar 2 -OH wherein Ar 2 is as defined in formula (1), in an inert medium in the presence of at least one alkali compound selected from hydroxides, carbonates and bicarbonates of alkali metals at a temperature of 300 to 360°C , said film having Young's modulus of at least 400 kg/mm 2 . The use of claim 1 wherein the tan δ peak temperature measured at 1 Hz is 160°C or higher. The film of claim 2 wherein the tan δ peak temperature measured at 1 Hz is 160°C or higher. A stretched fiber of a crystalline poly(arylene ether ketone) comprising at least 70 mol% of recurring units represented by formula (1) wherein Ar 1 denotes a 2,6-naphthalene ring, and Ar 2 denotes p-phenylene, p,p'-biphenylene, a 2,6-naphthalene ring, or a combination of them, and having inherent viscosity of 0.3 to 2.0 measured at 30°C in conc. sulfuric acid produced by heat-polycondensing a starting material composed principally of bis(p-fluorobenzoyl)naphthalene represented by formula (2) wherein Ar 1 is as defined in formula (1) , and an aromatic dihydroxy compound represented by formula (3) HO-Ar 2 -OH wherein Ar 2 is as defined in formula (1), in an inert medium in the presence of at least one alkali compound selected from hydroxides, carbonates and bicarbonates of alkal) metals at a temperature of 300 to 360°C, said fiber having Young's modulus of at least 1000 kg/mm 2 .

Inventors: INATA HIROO, ITOH SEIJI, MATSUMURA SHUNICHI, SADANOBU JIRO, INATA, HIROO, ITOH, SEIJI, MATSUMURA, SHUNICHI, SADANOBU, JIRO
Applicants: TEIJIN LTD, TEIJIN LIMITED
Application year: 1990
Main classification: C08G65
IPC codes: C08J5, D01F6, C08G65