THERMOPLASTIC SYNTHETIC FILAMENTS AND PROCESS FOR PRODUCING THE SAME

Abstract: Thermoplastic synthetic filaments having a properly delustered appearance and an adequate frictional property, comprise 85 to 99% by weight of a thermoplastic matrix polymer and 1 to 15% by weight of a dispersed polymer which is incompatible with the matrix polymer and uniformly dis­ persed in the form of fine particles in the matrix polymer, and are characterized by numerous fine protuberances consisting of the dispersed polymer and formed in the number of at least 5 per 10 µ² on the peripheral surface of each individual fila­ ment, the protuberances preferably being each in the form of a hemisphere, hemispheroid or hemiellipsoid extending along the longitudinal axis of each individual filament.

Description: THERMOPLASTIC SYNTHETIC FILAMENTS AND PROCESS FOR PRODUCING THE SAME FIELD OF THE INVENTION The present invention relates to thermoplastic synthetic filaments and a process for producing the same. More particularly, the present invention relates to thermoplastic synthetic filaments each having an uneven peripheral surface thereof and a process for producing the same. BACKGROUND OF THE INVENTION It is known that in order to produce thermoplastic synthetic filament having a desired gloss and frictional property, an inter inorganic substance, for example, titanium dioxide or china clay, in the form of fine solid particles is dispersed in a thermoplastic synthetic matrix polymer. That is, the inorganic particles are effective for modifying the optical and frictional properties of the filaments. The dispersed inorganic particles result in formation of numerous protuberances on the peripheral surface of the resultant individual filament. The number of the protuberances depends on the amount of the inorganic particles dispersed in the matrix polymer. These numerous protuberances create various problems on the filaments. For example, when a mixture of the thermoplastic matrix polymer with dispersed inorganic particles is subjected to a melt-spinning process, the dispersed inorganic particles cause the melt-spun filamentary streams of the melted mixture to be frequently broken. Also, when the resultant filaments are subjected to a weaving or knitting process, the protuberances on the peripheral surfaces of the filaments serve to accelerate the wear of the needs in the weaving machine or the needles in the knitting machine. It is also known that when a fabric consisting of thermoplastic synthetic fibers, for example, polyethylene terephthalate fibers, is subjected to a raising process, it is very difficult to obtain a uniformly raised surface of the fabric having a satisfactory appearance, because of the excessively large tensile strength and snap back phenomenon of the synthetic fibers. The term "snap back phenomenon" used herein refers to a phenomenon whereby the fibers or filaments in the fabric are stretched and, then, broken by the raising action applied to the fabric, the end portions of the stretched and broken fibers or filaments elastically shrunk and irregularly crimped. The irregularly crirr.e end portions of the fibers or filaments cause the appearance of the raised fabric to be poor. Furthermore, it is known that the thermoplastic synthetic filaments, for example, polyethylene terephthalate filaments, exhibit a poor stretch-breaking property in a draft zone system spinning process, because the filaments have too large tensile strength and ultimate elongation. In order to improve the raising and stretch-breaking properties of the synthetic filaments, it was attempted to mix the thermoplastic filament-forming synthetic polymer with inert inorganic particles having a relatively large size, for example, calcium carbonate particles. The calcium carbonate is relatively ineffective for enhancing the stretch-breaking and raising properties of the resultant filaments. Therefore, the addition of calcium carbonate remains unsatisfactory. Moreover, it is known that when a thermplastic synthetic filament yarn is false-twisted at an elevated temperature at which the filaments in the yarn can be fuse-bonded to each other, the resultant false-twisted filament yarn exhibit a preferable hand like that of a strongly twisted filament yarn. However, the above -mentioned fuse-bond of the filaments causes the resultant filament yarn to exhibit an uneven dyeing property and a poor draping property. Also, it is difficult to control the fuse-bond type false-twisting process, and the quality of the resultant product varies widely. Moreover, it is known that thermoplastic synthetic filaments, for example, polyethylene terephthalate filaments, are hydrophobic and, therefore, exhibit a poor water-absorbing property. In order to enhance the water-absorbing property, it was attempted to form numerous pores or concaves in the filaments. The pores or concaves were in the form of a simple line extending along the longitudinal axis of the filament. These pores or concaves cause the resultant filaments to exhibit an undesirably enhanced fibril-forming property and, therefore, to be easily divided into fine fibrils. SUMMARY OF THE INVENTION An object of the present invention is to provide thermoplastic synthetic filaments having preferably a delustered surface appearance and a proper frictional property, and a process for producing the same. Another object of the present invention is to provide thermoplastic synthetic filaments having satisfactory stretch-breaking and raising properties, and a process for producing the same. Still another object of the present invention is to provide thermoplastic synthetic filaments capable of being converted into a false-twisted filament yarn having a hand similar to that of conventional strongly twisted filament yarns and an excellent draping property, and a process for producing the same. A further object of the present invention is to provide thermoplastic synthetic filaments capable of being converted into filaments having an excellent water-absorbing property, and a process for producing the same. The above-mentioned objects can be attained by using the thermoplastic synthetic filaments of the present invention which conprise 85 to 998 by weight of a thermoplastic matrix polymer and 1 to 15% by weight of a dispersed polymer which is incompatible with the matrix polymer and dispersed in the form of fine particles in the matrix polymer, and which filaments are characterized by numerous fine protuberances consisting of the dispersed polymer and formed in the number of least 5 per 10 square microns on the peripheral surface of each individual filament. The above-mentioned thermoplastic synthetic filaments can be produced by the process of the present invention which comprises the steps of: preparing a mixture of 85 to 99% by weight of a thermoplastic matrix polymer with 1 to 15% by weight of a dispersed polymer which is incompatible with the matrix polymer, and; melt-spinning the mixture to produce filaments in each of which the dispersed polymer is dispersed in the matrix polymer and numerous fine protuberances consisting of the dispersed polymer are formed with at least 5 per 10 square microns on the peripheral surface of each individual filament. The thermoplastic synthetic filaments in which the matrix polymer is a polyester and which are in the form of a filament yarn and in a partially oriented state, can be converted into drawn-false twisted filament yarn by draw-false twisting the filament yarn under the conditions satisfying the relationship (3): a < 0.02T - 1.5D - 1.05 (3) wherein a represents a twisting coefficient in the range of from 0.4 to 0.9, T represents a false-twisting temperature in a range of from 150 to 2000C and D represents a draw ratio satisfying the relationship (4): 0.80R, < D = < R0 , (4) wherein R0 represents a draw ratio which causes the resultant drawn filaments to exhibit an ultimate elongation of 30%, to produce a drawn-false-twisted filament yarn. The thermoplastic synthetic filaments of the present invention, in which the matrix polymer is a polyester, can be converted into water-absorbing filaments by treating them with an aqueous alkali solution to cause the resultant treated filaments each to be provided with numerous concaves formed on the peripheral surface of each filament, each concave being composed of a hemisphere, hemispheroid or hemiellipsoid-shaped center portion and a pair of hemicone or hemielliptic cone-shaped wing portions thereof each extending from the center portion along the longitudinal axis of the individual filament in opposite direction to the other. BRIEF DESCRIPTION OF THE DRAWINGS Fig. 1 is a scanning electron microscopic photograph (magnification : 3000) showing a peripheral surface of a filament of the present invention having numerous hemispheroidal or hemiellipsoidal protuberances; Fig. 2 is a scanning electron microscopic photograph (magnification : 3000) showing a peripheral surface of a conventional filament containing 1% by weight of titanium dioxide particles and having numerous projections; Fig. 3 is a scanning electron microscopic photograph (magnification : 3000) showing a peripheral surface of a filament modified from the filament of the present invention as shown in Fig. 1 and having numerous specific concaves, and; Fig. 4 is a scanning electron microscopic photograph (magnification : 3000) showing a peripheral surface of a comparative filament modified from the conventional filament as indicated in Fig. 2 and having irregularly shaped concaves. DETAILED DESCRIPTION OF THE INVENTION The individual thermoplastic filament of the present invention comprises 85 to 99% by weight, preferably, 91 to 97% by weight, of a thermoplastic fiber-forming matrix polymer and 1 to 15% by weight, preferably, 3 to 9% by weight, of a dispersed polymer which is different from and incompatible with the matrix polymer. The dispersed polymer is dispersed in the form of numerous fine spheres, spheroids or ellipsoids, extending along the longitudinal aixs of the individual filament, in the matrix polymer. In this type of filament, it is characteristic that a portion of he dispersed polymer located in the peripheral surface of the filament, forms numerous fine protuberances with at least 5 per 10 square microns, on the peripheral surface of the filament. The matrix polymer usable for the present invention is not limited to a special group of thermoplastic polymer, as long as the polymer is capable of being shaped into a filament or fiber and the resultant filament or fiber exhibits satisfactory mechanical properties, for example, elasticity rigidity, and elongation. The matrix polymer may be selected from the group consisting of fiber -forming polyesters, polyamides, polyolefins and polystyrene. The important matrix polymer for the present invention is polyester. The matrix polyester may be a polycondensation product of at least one dicarboxylic compound, for example, terephthalic acid or its reactive derivative, with at least one alkylene glycol component, for example, ethylene glycol, propylene glycol, butylene glycol. Preferably, the matrix polyester is polyethylene terephthalate, polybutylene terephthalate or a copolyester containing 75 molar % or more, more preferably, 85 molar % or more, of the recurring alkylene terephthalate units derived from the esterification reaction of an alkylene glycol with terephthalic acid or its functional derivative. Also, it is preferable that the matrix polyester has a limiting (intrinsic) viscosity of 0.4 or more measured in o-chlorophenol at a temperature of 350C. The matrix polymer may contain, as additives, a catalyst residue, ether-generation-preventing agent, stabilizer, flame retardant, anti-static agent, hydrophilicity-enhancing agent, coloring material, optical brightening agent, and/or delustering agent. The dispersed polymer usable for the present invention is not limited to a special group of polymers, as long as the polymer is different from, non-reactive to and incompatible with the matrix polymer. It is preferable that the dispersed polymer is non-crystalline and has a glass transition temperature of at least 1500C. The glass transition temperature of the dispersed polymer can be determined by the method described in U. S. Patent No. 2,556,295. The non-crystallinity of the dispersed polymer can be determined by the X-ray wide angle diffractometry. Fken no diffraction point or line is found in the diffraction X-ray photograph of the dispersed polymer, it is deemed that the dispersed polymer is non-crystalline. The dispersed polymer may be selected from polysulfons having the recurring units of the formulae (I) through (IV): EMI7.1 The preferable polysulfone is one of the formula (IV) having a degree of polymerization of 60 to 120. The dispersed polymer is used in an amount of from 1 to 15% by weight, preferably, from 3 to 9% by weight. When the amount of the dispersed polymer is less than 1% by weight, the number of the resultant protuberances is less than 5 per 10 square microns of the peripheral surface of the resultant filament, and, therefore, the surface appearance and the frictional property of the resultant filament are unsatisfactory. Also, more than 15% by weight of the dispersed polymer causes the resultant filament to exhibit a poor mechanical strength and, therefore, to be practically useless. When a mixture of the matrix polymer and the dispersed polymer is melt-spun into filaments, at an elevated temperature higher than the melting point of the matrix polymer, the resultant filaments are provided with numerous fine protuberances formed on the peripheral surface of each individual filament. The density of the protuberances is at least 5 per 10 square microns of the peripheral surface of the individual filament. In this density, the protuberances are effective for delustering the surface of the resultant filament and for decreasing the dynamic friction of the filament peripheral surfaces with each other and with metal surfaces. Therefore, the filament can exhibit a satisfactory delustered surface appearance and a satisfactory frictional property and hand. The decreased dynamic frictional property of the filament is effective in increasing the draping property of the fabric made from the filament. Preferably, the protuberances are each in the form of a hemispheroid or hemiellipsoid extending along the longitudinal axis of the individual filament. Also it is preferable that the area of the bottoms of the protuberances is 0.5 square microns or more. The filaments of the present invention may have a circular cross-sectional profile or an irregular crosssectional profile, for example, trilobal or another multilobal cross-sectional profile. The irregular cross-sectional profile is effective for imparting a silk-like gloss and hand to the filament. The dispersed polymer particles dispersed in the matrix polymer in the filaments are effective for enhancing the dyeing property of the filaments, because numerous small voids are formed in the interface between the matrix polymer phase and the dispersed polymer phase. Also, since there is a small difference in the termal shrinkage between the matrix polymer phase and the dispersed polymer phase, the woven or knitted fabric made from the filaments of the present invention can have a preferable bulkiness and hand. Fig. 1 shows an electron microscopic view of a peripheral surface of the filaments of the present invention in a magnification of 3000. Also, Fig. 2 shows an electron microscopic view of a peripheral surface of a conventional filament containing 1% by weight of titanium dioxide. The peripheral surface of the filament as indicated in Fig. 2 is provided with extremely small projections having irregular shapes. The extremely small projections do not cause the resultant filament to exhibit the properly delustered surface appearance and a proper frictional property like those of the present invention. In the preparation of the termoplastic synthetic filaments of the present invention, a mixture of 85 to 99% by weight of a thermoplastic matrix polymer with 1 to 15% by weight of a dispersed polymer which is incompatible with the matrix polymer, is prepared. This mixture may be prepared in such a manner that the dispersed polymer is admixed to a polymerization mixture containing monomers for producing the matrix polymer and, then, the admixed polymerization mixture is subjected to a polymerization of the monomers. The resultant polymerization mixture contains the resultant matrix polymer and the dispersed polymer which is non-reactive with the matrix polymer. Otherwise, the mixture may be prepared by mixing the matrix polymer with the dispersed polymer. The mixture is subjected to a spinning process which may be a melt spinning process, dry spinning process or wet spinning process. When the matrix polymer is a polyester, the mixture containing the polyester is subjected to a melt-spinning process. When the filaments of the present invention are subjected to a draft zone system spinning process or a fabric made from the filaments is subjected to s raising process, it is preferable that the filaments exhibit a snap back value of 4% or less. The term "snap back value" used herein is defined by the equation (1): : SB = (eb - esb) - eb x rb/100 (1) wherein SB represents a snap back value in % of the filaments, eb represents a breaking elongation in % of the filaments, rb represents a tensile recovery in 8 of the filaments at its break and esb represents an elongation of the filaments determined from the difference between the length of the filament at its break and the original length of the filament. then the snap back value is more than 4%, the filaments sometimes exhibit a poor stretch-breaking property in the draft zone system spinning process and the fabric made from the filaments sometimes exhibit an unsatisfactory reaising property in the raising process. That is, sometimes, the resultant spun yarn is uneven and the resultant raised fabric exhibits an uneven surface appearance. Also, it is preferable that the filaments of the present invention exhibit a breaking modulus of 4 g/d or less. The term "breaking modulus" used herein is defined by the equation (2): sb x (100 + eb) (2) Mb = (2) D@ wherein Mb represents a breaking modulus in gid of a filament, sb represents a gradient in g/% of a tangential line drawn through a breaking point of the filament on the stress-strain curve of the filament, eb represents a breaking elongation in % of the filament and Do represents a denier of the filament. The filaments having a breaking modulus of 4 g/d or less can exhibit a proper stretch-breaking property and raising property. The filaments of the present invention, in which the matrix polymer is a polyester, may be treated with an alkali aqueous solution. The alkali treatment results in formation of numerous concaves on the peripheral surface of the individual filament. Each concave is composed of a center portion thereof, which is in the form of a hemisphere, hemispheroid or hemiellipsoid, and a pair of wing portions thereof each of which is in the form of a hemicone or hemielliptic cone and extends from the center portion in opposite direction to the other along the longitudinal axis of the individual filament. The bottom of each wing portion is connected to the center portion. The center portion of the concave is derived from the removal of the protuberance by the alkali treatment. Also, the wing portion of the concave is derived from the removal of a portion of the matrix polymer located just adjacent to the protuberance. The alkali may be selected from the group consisting of sodium hydroxide, potassium hydroxide, tetramethylammonium hydroxide, sodium carbonate and potassium carbonate. The most preferable alkali is sodium hydroxide or potassium hydroxide. The concentration of the alkali in its aqueous solution is variable depending on the type of alkali and treating conditions. However, it is preferable that the concentration of the alkali is usually in the range of from 0.1 to 40E by weight, more preferably, from 0.1 to 30% by weight. The alkali treatment is preferably carried out at a temperature of from room temperature to 1000C, for one minute to 4 hours. Also, it is preferable that the alkali treatment causes a reduction in the weight of the filaments to an extent of at least 10% of the original weight of the filaments. By this alkali treatment, the protuberances on the peripheral surface of the individual filament are removed so as to form the concaves in the form of hemispheroid or hemiellipsoid. In the alkali-treated individual filament, it is preferable that each concave has an opening area of at least 5 square microns. Also, it is preferable that the number of the concaves is at least one per 300 square microns of the peripheral surface of the individual filament. Fig. 3 shows an electron microscopic view of a peripheral surface of an alkali-treated individual filament which has been prepared from the individual filament of the present invention as indicated in Fig. 1. Referring to Fig. 3, each concave formed on the peripheral surface of the filament is composed of a hemisphere, hemispheroid or hemiellipsoid-shaped, caved center portion and a pair of hemicone or hemielliptic cone-shaped, caved wing portions, extending from the center portion in opposite directions to each other along the longitudinal axis of the filament. This configuration of the concave is very specify and was obtained only by alkali treating the filament of the present invention. Also, it is important that the alkali treatment applied to the filaments of the present invention does not cause the resistance of the resultant filament to fibrilization to be reduced. That is, the alkali treated filaments exhibit a satisfactory resistance to abrasion. When the conventional filament as shown in Fig. 2 is treated with the alkali aqueous solution, the treated filament is provided with numerous concaves as shown in Fig. 4. The concaves as shown in Fig. 4 are significantly smaller than and different in configuration from the specific concaves as shown in Fig. 3. That is, the configuration of the concaves shown in Fig. 4 is irregular. The filaments of the present invention can be converted into a false-twisted filament yarn having an appearance and touch similar to those of conventional hard twist filament yarn. That is, the filaments, which are polyester filaments in a partially oriented state and in the form a filament yarn, are draw-false twisted under the conditions satisfying the relationship (3): a < 0.02T - l.5D - 1.05 (3) wherein a represents a twist multiplier to be applied to the filament yarn in the range of from 0.4 to 0.9, T represents a false twisting temperature to be applied to the filament yarn in the range of from 150 to 2000C and D represents a draw ratio to be applied to the filament yarn satisfying the relationship (4): : 0.80 R < D < Rio , wherein R represents a draw ratio which causes the 0 resultant drawn filament yarn to exhibit an ultimate elongation of 30%. The twist multiplier (a) of the filament yarn can be calculated in accordance with the equation (5): EMI13.1 wherein TN represents the number of twists applied to the filament yarn and De represents a denier of the resultant drawn, false-twisted filament yarn. The filament yarn to be subjected to the above mentioned draw-false twisting procedure is a partially oriented filament yarn preferably having an ultimate elongation of from 70 to 200%. The partially oriented filament yarn can be produced by a conventional high speed spinning process. the spinning speed adquate to produce the partially oriented filament yarn is variable depending on the intrinsic viscosity of the matrix polymer, the type and concentration of the dispersed polymer and the denier of the resultant individual filament. Usually, the spinning process is performed at a high speed of 2000 to 5500 m/sec. In the above-mentioned draw-false twisting procedure, the filament yarn may consist of the filaments of the present invention alone or a blend of the filaments of the present invention with another type of filament. The draw-false twisting procedure is distinctive in the relatively low draw-false twisting temperature of from 150 to 2000C, from the conventional draw-false twisting procedure for conventional polyester filament yarn. In order to produce a drawn, false twisted polyester filament yarn having a hard twist yarn-like touch, it is necessary that the draw-false twisting temperature to be applied to the polyester filament yarn is 215"C or more. However, such high temperature causes the individual filaments in the yarn to be fuse-bonded to each other and the dyeability of the filament yarn to be significantly changed. However, in the ve-mentioned draw-false twisting procedure, the draw-false twisting temperature is relatively low. Therefore, the change in the dyeability of the filament yarn is very small and the filament yarn exhibits a satisfactory draping property. However, the individual filaments in the filament yarn are fuse-bonded to each other to a satisfactory extent. The drawn, false-twisted filament yarn exhibits a satisfactory weaving and knitting property. In order to stabilize the filament yarn, it is preferable to relax the filament yarn at an elevated temperature, for example, 210 to 2300 C, more preferably, while overfeeding the filament yarn at a degree of overfeed of 2 to 7% so that the resultant relaxed filament yarn exhibits a torque of 50 turns/m or less. In the filament of the present invention, when the matrix polymer is a polyester, the dispersed polymer may contain at least one member selected from the group consisting of polytetrafluoroethylene, tetrafluoroethylene -hexafluoropropylene copolymers, polychlorotrifluoroethylene, polyvinylidene fluoride and polyvinyl fluoride which are inconpatible with the polyester and have a glass transition temperature of 150 C or less, and, also which exhibit a melt viscosity of 105 poises or more when these are heated to a temperature of or close to the melting point thereof. SPECIFIC EXAMPLES OF THE INVENTION The following specific examples are presented for the purpose of clarifying the present invention. However, it should be understood that these are intended only to be examples of the present invention and are not intended to limit the present invention in any way. Examples 1 through 5 and Comparative Examples 1 and 2 In each of the Examples 1 through 5 and Comparative Examples 1 and 2, the amount as indicated in Table 1 of a dispersed polymer consisting of a polysulfone having a recurring unit of the formula: EMI15.1 was mixed with the balance consisting of a matrix polymer, that is, a polyethylene terephthalate having an intrinsic viscosity of 0.64 determined in O-chlorophenol at a temperature of 35"C, and containing 0.03% by weight of titanium dioxide. The mixture was dried and melted in an extruder at a temperature of 3150C and, then, extruded through a spinneret having 24 spinning orifices each having a diameter of 0.3 mm, at a temperature of 2900C. The filamentary streams of the extruded mixture were introduced into a spinning chimney and cooled by blowing cooling air laterally through the chimney at a flowing linear speed of 0.2 m/sec to solidify them. After oiling, the solidified filaments were wound up at a winding speed of 1400 m/min. The resultant undrawn filament yarn was preheated at 900C for 0.35 seconds by using a heating roll and drawn at a draw ratio of 3.0. Finally, the drawn filament yarn was bent treated at a temperature of 2300C by using a slit heater and, then, wound up at a speed of 800 m/min. In Comparison Example 1, the resultant drawn individual filament had substantially no hemisphere or hemiellipsoid protuberance. This filament had only very small irregular shaped protuberances which were derived from the titanium dioxide particles. Also, in Comparison Example 2, the resultant drawn individual filaments exhibited extremely poor tensile strength and ultimate elongation and, therefore, were useless for practical use. The resultant drawn individual filaments in Examples 1 through 5 each exhibited satisfactory coefficients of fiber-fiber dynamic friction and tensile strength and ultimate elongation, and had an adequately delustered appearance thereof. Table l Protuberance coefficient Item of fiber Amount of The number Bottom -fiber dynamic Denier/ dispersed per 10 area friction the number Tensile Ultimate Example folymer square (square at a speed of strength elongation (wt%) Configuration microns micron) of 3600 cm/min filaments (g/d) (%) Conparative Example l 0.5 Substantially no hemisphere or 0.389 51/24 4.5 25.0 hemielliproid protuberance 1 1.5 Hemisphere 6.5 0.55 0.75 0.323 50/24 4.0 26.0 2 3.0 Hemisphere 8.0 0.50 0.80 0.300 50/24 3.8 24.8 hemielliproid Ex@mple 3 6.0 ditto 12.0 0.60 0.85 0.286 51/24 3.4 16.5 4 9.0 ditto 15.5 0.55 0.90 0.264 53/24 3.2 15.0 5 12.0 Hemisphere 18.0 0.60 0.85 0.225 50/24 3.0 12.5 Conparative Example 2 16.0 ditto 20.5 0.55 0.90 0.203 51/24 1.8 4.8 Comparative Example 3 The same procedures as those described in Example 1 were carried out, except that no dispersed polymer was used and the matrix polymer contained 1.0% by weight of titanium dioxide. The resultant drawn filament had a satisfactorily delustered appearance thereof close to that in Example 4 but not hemisphere, hemispheroid or hemiellipsoid protuberance. Example 6 The drawn filaments obtained in Example 3 were converted into a tricot fabric. This fabric exhibited a satisfactory high bulkiness and dyeability and a desirable dry touch. Examples 7 through 11 and Comparative Examples 4 and 5 In each of the Examples 7 through 11 and Comparative Examples 4 and 5, the same procedures as those described in Example 1 were carried out with the following exception. The used dispersed polymer consisted of a polysulfone compound which was produced and sold in the trademark of Udel by Union Carbide Co., U.S.A. and which was non-crystalline and incompatible with the polyethylene terephthalate used and had a glass transition temperature of 175 0C. The mixture of the matrix polymer and the dispersed polymer in the amount as indicated in Table 2 was dried at a temperature of 160"C for 4 hours before the melt-extruding procedure. The spinneret used had 36 spinning orifices each having a diameter of 0.4 mm, and the extruded filamentary streams of the melted mixture was cooled by blowing cooling air at a flow linear speed of 0.3 m/sec across a spinning chimney to solidify them. The solidified filament was oiled and, then, wound up at a winding speed of 1200 m/min. The resultant undrawn filaments were preheated at a temperature of 900C for 0.3 seconds, and drawn at a draw ratio of 3.3. The properties of the resultant filaments are indicated in Table 2. Table 2 Prtuberance Coefficient Item of fiber -fiber Amount of The number Bottom dynamic Denier/ dispersed pr 2 area friction the number Tensile ultimate Example polymer configuration 10 2 ( 2) at a speed of strength elongation (wt%) ( ) of 3600 cm/min filaments (g/d) (%) Comparative Example 4 0.5 Substantially no hemisphere or 0.398 52/36 4.6 28.0 hemielliproid protuberance 7 1.5 Hemielliproid - - 0.323 51/36 3.8 25.0 8 3.0 Hemisphere and - - 0.3000 50/36 3.6 23.5 Hemielliproid Example 9 6.0 " - - 0.286 51/36 3.3 18.2 10 9.0 " - - 0.264 51/36 3.0 14.6 11 12.0 Hemisphere - - 0.225 50/36 2.8 12.9 Comparative Example 5 16.0 " - - 0.203 52/36 1.6 6.0 In Comparative Example 4, the resultant drawn individual filament had very small irregular protuberances which were derived from the fine particles of titanium dioxide, but had substantially no hemisphere or hemiellipsoid protuberance. Also, the resultant individual filament in Comparative Example 5 exhibited extremely poor tensile strength and ultimate elongation and therefore, was useless for practical use. Examples 12 through 16 and Comparative Examples 6, 7 and 8 In each of the Examples 12 through 16 and Comparative Examples 6, 7 and 8, the amount as indicated in Table 3 of the same dispered polymer as that described in Example 6 was mixed with the balance consisting of the same polyethylene terephthalate as that described in Example 1. The mixture was dried at 1600C for 4 hours and meltextruded in the same manner as that described in Example 1, and the solidified filaments were oiled and, then, wound at a speed of 1500 m/min. The resultant undrawn filament yarn was preheated at 900C for 0.3 seconds on a heating roll and dram at a draw ratio of 2.8. The drawn filament yarn was benttreated at 210 C by using a slit heater and wound at a speed of 800 m/min. The results are shown in Table 3. Table 3 Item Drawn filament yarn Amount of dispersed Tensile Ultimate Breaking Sanp back polymer Denier strength elongation modulus value Example No. (wt%) (de/24 fil) (g/de) (%) (g/de) (%) Comparative Example 6 0 75 5,2 29.5 6.6 7.0 7 0.5 76 4.6 28.0 5.4 5.8 12 1.5 75 3.8 25.0 4.1 3.9 13 3.0 76 3.6 23.5 3.8 3.6 14 6.0 78 3.3 18.2 3.4 3.1 15 9.0 77 3.0 14.6 3.2 2.7 16 12.0 74 2.8 12.9 3.1 2.2 Comparative Example 8 16.0 75 1.6 6.0 3.0 2.0 In each of Comparative Examples 6 and 7, the resultant filament yarn exhibited a large snap back value and breaking modulus and, therefore, is not suitable for the draft zone system spinning process and raising process. Also, the resultant filament yarn in Comparative Example 8 exhibited an extremely poor tensile strength and ultimate elongation and, therefore, is useless for practical use. The filament yarns obtained in Examples 12 through 16 exhibited a satisfactory tensile strength, ultimate elongation, breaking modulus and snap back value. Therefore, these filament yarns are useful for the draft zone system spinning process and for producing a raised fabric. Examples 17 through 21 and Comparison Examples 9 through 11 In each of the Exampl-es 17 through 21 and Comparative Examples 9 through 11, the same procedures as those described in Example 12 were carried out, except that the amount of the dispersed polymer was as indicated in Table 4, the spinning orifices each had a diameter of 0.27 mm, the extrusion of the melted mixture was carried out at a temperature of 2950C, the oiled undrawn filaments were wound at a speed of 1200 m/min and the heat treatment for the drawn filament yarn was carried out at a temperature of 2200 C. The properties of the resultant filament yarn are indicated in Table 4. Table 4 Item Drawn filament yarn Amount of Configuration Denier dispersed of per 24 Tensile Ultimate polymer protuberance fiolaments strength elongation Example No. (wt%) (d/24 fil) (g/d) (%) Comparative Example 9 0 no protuberance 76/24 5.1 31.2 10 0.5 substantially no hemisphere or 75/24 4.7 29.1 hemielliproid protuberance 17 1.5 Hemiellipsoid 76/24 4.3 25,8 Example 18 3.0 Hemisphere and hemiellipsoid 73/24 3.6 23.1 19 6.0 " 74/24 3.3 18.8 20 9.0 " 75;24 3.0 16.1 21 12.0 Hemisphere 74/24 2.7 14.3 Comparative Example 11 16.0 " 76/24 1.8 6.2 Each filament yarn was converted into a knitted fabric. The fabric was scoured and dried in an ordinary manner. The dried fabric was treated with an aqueous solution of sodium hydroxide in concentration as shown in Table 5 at a boiling temperature of the solution for the time period as indicated in Table 5. The decrease in the weight of the filament yarn is indicated in Table 5. Also, the configuration, opening area and the numbers of concaves formed on the peripheral surface of the alkali-treated individual filament and the water-absorption and fibril -forming property of the alkali-treated filament yarn are shown in Table 5. Table 5 Item Alkali treatment Alkali-treated filament Decrease Type of in weight opening The number filament Concentratio of filament Configuration area of of concaves Water- Formation yarn used of @aOH Time yarn of conceve concave per 300 ê -absorption of fibril (min) (wt%) ( ê) (%) Comparison Example 9 - - 15 Linear - 0 22.3 no 10 - - 15 " - 0 31.1 " Example 17 - - 15 (#) 5.2¯6.3 1 42.2 " Example 18 - - 5 Linear - 0 38.5 " " - - 15 (#) 5.9¯7.8 2 45.6 " " ¯ - 25 " 6.5¯9.2 3 53.2 " Example 19 - - 15 " 6.4¯9.4 4 46.2 " " - - 25 " 7.0¯11.2 58.3 " Example 20 - - 15 " 6.8¯10.2 5 61.5 " Example 21 - - 15 " 6.9¯9.8 5 65.8 " Comparative Example 11 - - 15 " 7.2¯10.8 6 64.2 yes Note: (#) - The Concave was composed for a hemisphere, hemispheroid or hemiellipsoid-shaped center portion thereof and a pair of hemicone or hemielliptic cone-shaped wing portions thereof. The water absorption was determined as follows. A test specimen was completely dried and the weight (W ) of the dried specimen was measured. The specimen was immensed in water at room temperature for 30 minutes and, then, centrifugalized for 5 minutes by using a home centrifuge. The weight (per1) of the centrifugalized specimen was measured. The water absorption (WA) of the specimen was calculated from the following equation. w - W 1 0 WA (%) = - x 100 W o The fibril-forming property was observed in the following manner. A test specimen (fabric) was rubbed 500 times with a crepe suzette fabric made of polyethylene terephthalate multifilament yarns having a yarn count of 75 denier/36 2 filaments, and having a weight of 90 g/m under a load of 500 g by using a rubbing tester. After the rubbing procedure, the surface of the specimen was observed by the naked eye. The opening area of the concaves were measured in the following manner. That is, after the alkali treatment, the peripheral surface of the individual filament was photographed for an electron microscopic observation at a magnification of 3000. From the photograph, the opening area of the concave was measured. Examples 22 through 26 and Comparative Examples 12 through 14 In each of the Examples 22 through 26 and Comparison Examples 12 through 14, the same procedures as those in Example 12 were carried out, except that the amount of the dispersed polymer was as indicated in Table 6, the number of the spinning orifices was 48, the linear flow speed of the cooling air was 0.3 m/sec, the winding speed for the solidified filaments was 1200 m/min, the draw ratio was 3.3 and the heat-treatment temperature for the drawn filament yarn was 2300C. The properties of the resultant filament yarn are indicated in Table 6. Table 6 Item Drawn filament yarn Amount of Denier dispersed Configuration per 48 Tensile Ultimate Example No. polymer of protuberance filaments strength elongation (wt%) (g/de) (%) Comparative Example 12 0 none 151/48 5.0 29.6 13 0.5 Irregular 150/48 4.8 28.0 22 1.5 Hemiellipsoid 149/48 4.2 25.0 23 3.0 Hemisphere and 152/48 3.6 24.2 Example hemiellipsoid 24 6.0 " 151/48 3.3 18.1 25 9.0 150/58 3.0 15.2 26 12.0 Hemisphere 150/48 2.8 13.1 Comparative Example 14 16.0 " 151/48 1.7 5.8 The same alkali treatment as mentioned in Example 17 was applied to each filament yarn which was converted into a knitted fabric, except that the concentration of sodium hydroxide in the aqueous solution was 3.0%. The results are indicated in Table 7. Table 7 EMI30.1 Item <SEP> Alkali <SEP> treatment <SEP> alkali-treated <SEP> filament <SEP> yarn <tb> The <SEP> number <tb> Type <SEP> of <SEP> and <tb> filament <SEP> Decrease <SEP> Water- <SEP> Configuration <SEP> Formation <tb> yarn <SEP> Time <SEP> in <SEP> weight <SEP> -absorption <SEP> of <SEP> concaves <SEP> of <SEP> fibrils <tb> (min) <SEP> (%) <SEP> (%) <tb> Comparison <SEP> Example <SEP> 12 <SEP> - <SEP> 15 <SEP> 24.1 <SEP> a <SEP> few. <SEP> no <tb> linear <tb> 13 <SEP> - <SEP> 15 <SEP> 33.4 <SEP> many. <SEP> no <tb> linear <tb> Example <SEP> 22 <SEP> - <SEP> 15 <SEP> 40.9 <SEP> a <SEP> few, <SEP> no <tb> Example <SEP> 23 <SEP> - <SEP> 5 <SEP> 39.8 <SEP> a <SEP> few. <SEP> no <tb> linear <tb> " <SEP> - <SEP> 15 <SEP> 44.6 <SEP> many, <SEP> no <tb> (#) <tb> " <SEP> - <SEP> 25 <SEP> 51.2 <SEP> many, <SEP> no <tb> Example <SEP> 24 <SEP> - <SEP> 15 <SEP> 47.9 <SEP> many, <SEP> no <tb> (#) <tb> " <SEP> - <SEP> 25 <SEP> 57.7 <SEP> many, <SEP> no <tb> (#) <tb> Example <SEP> 25 <SEP> - <SEP> 14 <SEP> 60.6 <SEP> very <SEP> many, <SEP> no <tb> (#) <tb> Example <SEP> 26 <SEP> - <SEP> 15 <SEP> 61.8 <SEP> very <SEP> many, <SEP> no <tb> (#) <tb> Comparative <SEP> Example <SEP> 14 <SEP> - <SEP> 15 <SEP> 58.9 <SEP> very <SEP> many, <SEP> no <tb> (#) <tb> Note (#) - The same as that described under Table 5. From Tables 5 and 6, it is clear that when the filament yarn of the present invention (Examples 17 through 26) was alkali treated to an extent that the decrease in weight was 10% or more, the resultant concaves had a specific shape and exhibited an excellent water absorption of 40% or more and a satisfactory resistance to the formation of fibrils. Examples 27 through 44 and Comparative Examples 15 through 18 In each of the Examples 27 through 44 and Comparative Examples 15 through 18, the same procedures as those described in Example 22 were carried out, except that the amount of dispersed polymer was as indicated in Table 8, the number of the spinning orifices was 36, the oiled filaments were wound at a high speed as indicated in Table 8, and the undrawn filament yarn had an ultimate elongation of about 120% and a denier of 150/36 filaments. That is, the resultant filaments were partially oriented filaments. Each resultant filament yarn was draw-false twisted under the conditions as indicated in Table 8 by using a Draw-False twister (Type FW-III, made by Teijin Seiki K.K. Japan; the length of heater = 1.0 m), and the drawn, false twisted filament yarn was relaxed at a temperature of 2000C while overfeeding the yarn at an overfeed of 5% by using a non-contact type heater, and wound at a speed of 100 m/min. The results are indicated in Table 8. Table 8 Item Draw-false twisting process Drawn, false-twisted filament yarn Amount of Hard twist dispersed Winding Twist yern-like Degree of polymer speed multiplier Draw ratio Temperature touch fuse-bonding Torque (a) (D) #1) (T) (class #4) (class #3) (wt%) (m/min) ( C) (T/m) #) Comparative Example 15 0 3300 0.65 1.3 235 otfinsty otfinsty 43 #) 16 " " 0.40 1.2 200 poor poor 30 #) 17 0.5 " " " " " " 35 EXample 27 1.5 3000 0.45 1.3 195 ordinary ordinary 20 28 3.0 2800 0.50 1.4 190 " " 35 29 4.5 2600 0.75 1.5 200 poor poor 45 30 " " 0.75 1.4 195 ordinary ordinary 40 31 " " 0.75 1.3 190 " " 35 32 " " 0.60 1.3 190 axcellent excellent 30 33 " " 0.50 1.3 190 " " 20 34 " " 0.50 1.3 180 ordinary ordinary 25 35 " " 0.50 1.3 170 poor poor 30 36 " " 0.50 1.2 170 ordinary ordinary 25 37 " " 0.40 1.2 170 " excellent 18 38 6.0 2500 0.80 1.4 195 poor poor 42 39 " " 0.75 1.4 195 ordinary excellent 38 40 " " 0.6 1.4 190 " " 33 41 " " 0.5 1.3 180 excellent " 26 42 " " 0.4 1.2 170 " " 19 43 9.0 2300 0.6 1.4 180 " " 37 44 23.0 2100 " " " " " " 35 Comparative Example 18 16,0 2000 " " " Extremely poor strength Note: #1) -R = 1.5 #2) - R#laking temperature = 25 C #3) - Degree of fuse-bonding was determined by observing the crss-sectional profie of the drawn, false twisted filament yarn by using a microscope . In Comparative Examples 16 and 17 in which the dispersed polymer was used in an amount less than 1%, the draw-false twisting procedure applied to the resultant filament yarns having substantially no protuberances failed to obtain hard twist filament yarn-like false twisted yarns, even when a high draw-false twisting temperature of 200"C was applied to the filament yarns. In the Comparative Example 15 in which no dispersed polymer was used and the resultant filaments had no protuberance, an exessively high draw-false twisting temperature of 2350C was applied to the filament yarn in order to cause the resultant yarn to exhibit a hard twist filament yarn-like configuration and touch. In Comparative Example 18, the resultant filament yarn containing 16.0% of the dispersed polymer exhibited an extremely poor mechanical strength. In Examples 27, 28, 30 through 34, 36, 37 and 39 through 44 wherein the draw-false twisting procedures were carried out under the conditions satisfying the relationship (3), the resultant filament yarns all exhibited satisfactory hard twist filament yarn-like configuration and touch. However, in Examples 29, 35 and 38 wherein the draw-false twisting procedures were carried out under conditions not satisfying the relationship (3), the resultant filament yarns exhibited unsatisfactory touch and degree of fuse fonding of the individual filaments. Table 8 shows that as long as the relationship (3) is satisfied, the larger the amount of the dispersed polymer and the lower the twist multiplier and the draw ratio and the higher the draw-false twisting temperature, the better the hard twisted filament yan-like configuration and touch. Examples 45 through 62 and Comparative Examples 19 through 22 In each of the Examples 45 through 62 and Comparative Examples 19 through 22, the same procedures as those described in Example 27 were carried out, except that the dispersed polymer was used in the amount as indicated in Table 9, the winding speed for the solidified filaments were as indicated in Table 9, and the draw-false twisting procedure was carried out under the conditions as indicated in Table 9. The results are indicated in Table 9. Table 9 Drawn, false twi sted Item Draw-false twisting process filament yarn Amount of Hard twist dispersefd Winding Twist Draw ratio Temperature yarn-like Draping Example No. polyer speed multfplier (D) #l) (T) touch property Torque (wt%) (m/min) (a) ( C) (T/m) #2) Comparative Example 19 0 3300 0.65 1.30 235 remarkable poor 43 #2) 20 " " 0.40 1.20 160 poor excellent 53 #2) 21 0.5 " " " " " " 60 45 1.5 3000 0.45 1.30 170 ordinary remarkable 38 46 3.0 2800 0.50 1.40 180 " " 46 47 " " 0.75 1.50 2.00 " ordinary 45 48 " " 0.75 1.40 190 " " 47 49 " " 0.75 1.30 180 " " 43 50 " " 0.60 1.30 185 " " excellent very poor 37 51 " " 0.50 1.30 175 " " ordinary ordinary 44 52 " " 0.50 1.30 165 " " 41 53 " " 0.50 1.30 160 " " 48 54 " " 0.50 1.20 170 " very poor 43 55 " " 0.40 1.20 160 " ordinary 38 56 6.0 2500 0.80 1.40 195 " " 42 57 " " 0.75 1.40 180 " " 43 58 " " 0.60 1.40 180 " " 38 59 " " 0.50 1.30 180 excellent very poor 26 60 " " 0.40 1.20 160 ordinary ordinary 30 61 9.0 2300 0.60 1.40 170 " " 43 62 12.0 2100 0.60 1.40 170 " " 41 Comparative Example 22 16.0 2000 0.60 l.40 170 extremely poor strength Note: #1) - ho = 1.5 #2) - Rclaxing temperature = 235 C In Comparative Example 19 wherein the filaments contained no dispersed polymer, the draw-false twisting procedure was carried out at an excessively high temperature of 2350C. The resultant filament yarn exhibited poor draping property. In Comparative Example 20 and 21 wherein the filaments contained zero or 0.5e by weight of the dispersed polymer, the draw-false twisting procedures were carried out at a relatively low twist multiplier of 0.40, draw ratio of 1.2 and temperature of 1600C. The resultant filament yarns exhibited an unsatisfactory hard twist filament yarn like configuration and touch. In Comparative Example 22 wherein the dispersed polymer was used in a large amount, 16% by weight, the resultant filament yarn could not be draw-false twisted because of its extremely poor mechanical strength. In Examples 45 through 49, 51 through 53, 55 through 58 and 60 through 62, wherein the draw-false twisting conditions satisfied the relationship (3), the resultant filament yarns exhibited satisfactory hard twist filament yarn-like configuration and touch and draping property. However, in Examples 50, 54, and 59, wherein the draw-false twisting conditions did not satisfy the relationship (3), the resultant filament yarns exhibited a poor draping property.

Claims: CLAIMS 1. Thermoplastic synthetic filaments comprising 85 to 99% by weight of a thermoplastic matrix polymer and 1 to 15% by weight of a dispersed polymer which is incompatible with said matrix polymer and dispersed in the form of fine particles in said matrix polymer, which filaments are characterized by numerous fine protuberances consisting of said dispersed polymer and formed in the number of at least 5 per 10 square microns on the peripheral surface of each individual filament. 2. The filaments as claimed in claim 1, wherein said protuberances are each in the form of a hemisphere, hemispheroid or hemiellipsoid extending along the longitudinal axis of the individual filament. 3. The filaments as claimed in claim 1, wherein the area of bottoms of said protuberances is 0.5 square microns or more. 4. The filaments as claimed in claim 1, wherein said matrix polymer is thermoplastic polyester. 5. The filaments as claimed in claim 1, wherein said polyester consists essentially of recurring ethylene terephthalate units. 6. The filaments as claimed in claim 1, wherein said dispersed polymer is non-crystalline and has a glass transition temperature of at least 1500C. 7. The filaments as claimed in claim 1, wherein said dispersed polymer is a polysulfone. 8. The filaments as claimed in claim 7, wherein said polysulfone comprises the recurring unit of the formula; EMI37.1 9. The filaments as claimed in claim 1, wherein the amount of said dispersed polymer is in the range of from 3 to 9% by weight. 10. The filaments as claimed in claim 1, wherein the individual filaments exhibit a snap back value of 4% or less, said snap back value being defined by the equation (1): SB = (eb - esb) - eb x rb/100 (1) wherein SB represents a snap back value in % of the filaments, eb represents a breaking elongation in % of the filaments, rb represents a tensile recovery in 8 of the filaments at its break and esb represents an elongation in % of the filament determined from the difference between the length of the filament at its break and the original length of the filament. 11. A fiber as claimed in claim 1, wherein the individual fiber exhibits a breaking modulus of 4 g/d or less, said breaking modulus being defined by the equation (2): sb x (100 + eb) Mb = (2) D o wherein Mb represents a breaking modulus in g/d of the filament, sb represents a gradient in g/% of a tangential line drawn through a breaking point of the filament on the stress-strain curve of the filament, eb represents a breaking elongation in % of the filament and D represents 0 a denier of the filament. 12. A process for producing thermoplastic synthetic filaments comprising the steps of: preparing a mixture of 85 to 99% by weight of a thermoplastic matrix polymer with 1 to 15 by weight of a dispersed polymer which is incompatible with said matrix polymer and; melt-spinning said mixture to produce filaments in each of which said dispersed polymer is dispersed in said matrix polymers, and numerous fine protuberances consisting of said dispersed polymer are formed in the number of at least 5 per 10 square microns on the peripheral surface of each individual filament. 13. The process as claimed in claim 12, wherein said mixture is prepared in such a manner that said dispersed polymer is admixed to a polymerization mixture containing monomers for producing said matrix polymer and, then; said admixed polymerization mixture is subjected to a polymerization of said monomers. 14. The process as claimed in claim 12, wherein said matrix polymer is a thermoplastic polyester. 15. The process as claimed in claim 12, wherein said polyester consists essentially of recurring ethylene terephthalate units. 16. The process as claimed in claim 12, wherein said dispersed polymer is non-crystalline and has a glass transition temperature of at least 150 C. 17. The process as claimed in claim 12, wherein said dispersed polymer is a polysulfone. 18. The process as claimed in claim 17, wherein said polysulfone comprises the recurring unit of the formula; EMI39.1 19. The process as claimed in claim 12, wherein the amount of said dispersed polymer is in the range of from 3 to 9% by weight. 20. The process as claimed in claim 12, wherein said filaments, which are polyester filaments in a partially oriented state, and in the form of a filament yarn, are draw-false twisted under the conditions satisfying the relationship (3): a < 0.02 T - 1.5 D - 1.05 (3) wherein a represents a twist multiplier to be applied to the filament yarn in the range of from 0.4 to 0.9, T represents a false-twisting temperature to be applied to the filament yarn in the range of from 150 to 2000C and D represents a draw ratio to be applied to the filament yarn satisfying the relationship (4): 0.80 R0= < D < Ro, wherein R represents a draw ratio which causes the resultant drawn 0 filament yarn to exhibit an ultimate elongation of 30%, to produce a drawn-false-twisted filament yarn. 21. The process as claimed in claim 20, wherein said partially oriented filament yarn has an ultimate elongation of from 70 to 200%. 22. The process as claimed in claim 12, wherein said matrix polymer is a polyester and the resultant filaments are additionally treated with an aqueous alkali solution to cause the treated individual filament to have numerous concaves each of which is composed of a center portion thereof in the form of a hemisphere, hemispheroid or hemiellipsoid and a pair of wing portions thereof each in the form of a hemicone or hemielliptic cone and each extending from the center portion in opposit direction to the other along the longitudinal axis of the individual filament. 23. The process as claimed in claim 22, wherein said aqueous alkali solution contains 0.01 to 40% by weight of the alkali. 24. The process as claimed in claim 22, wherein said alkali treatment is carried out at a temperature of room temperature to 1000C. 25. The process as claimed in claim 22, wherein said alkali treatment causes the weight of said filaments to be reduced to an extent of at least 10% of the original weight thereof. 26. The filament as claimed in claim 1, wherein said protuberances are removed to cause formation of neumerous concaves on the peripheral surface of the individual filament, each concave being composed of a center portion thereof in the form of a hemisphere, hemispheroid or hemiellipsoid and a pair of wing portions thereof each in the form of a hemicone or hemielliptic cone and each extending from the ceter portion in opposit direction to the other along the longitudinal axis of the individual filament. 27. The filaments as claimed in claim 1, wherein said concaves each have an opening area of at least 5 square microns. 28. The filaments as claimed in claim 1, wherein the number of said concaves is at least one per 300 square microns of the peripheral surface of the individual filament.

Inventors: KUMAKAWA, SHIRO, KURODA, TOSHIMASA
Applicants: TEIJIN LIMITED
Application year: 1981
Main classification: D01F1
IPC codes: D01F1, D01F6