EP0035796B1 - Thermoplastische synthetische Fasern und Verfahren zu deren Herstellung - Google Patents

Thermoplastische synthetische Fasern und Verfahren zu deren Herstellung Download PDF

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Publication number
EP0035796B1
EP0035796B1 EP81101790A EP81101790A EP0035796B1 EP 0035796 B1 EP0035796 B1 EP 0035796B1 EP 81101790 A EP81101790 A EP 81101790A EP 81101790 A EP81101790 A EP 81101790A EP 0035796 B1 EP0035796 B1 EP 0035796B1
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Prior art keywords
filament
filaments
polymer
dispersed
weight
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EP81101790A
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English (en)
French (fr)
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EP0035796A1 (de
Inventor
Shiro Kumakawa
Toshimasa Kuroda
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Teijin Ltd
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Teijin Ltd
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Priority claimed from JP3025980A external-priority patent/JPS56127660A/ja
Priority claimed from JP3394880A external-priority patent/JPS56134213A/ja
Priority claimed from JP3394780A external-priority patent/JPS56131663A/ja
Priority claimed from JP7418480A external-priority patent/JPS57145A/ja
Priority claimed from JP7486280A external-priority patent/JPS571727A/ja
Priority claimed from JP11111980A external-priority patent/JPS5739227A/ja
Priority claimed from JP11112080A external-priority patent/JPS5739228A/ja
Priority claimed from JP13225580A external-priority patent/JPS5761718A/ja
Application filed by Teijin Ltd filed Critical Teijin Ltd
Publication of EP0035796A1 publication Critical patent/EP0035796A1/de
Publication of EP0035796B1 publication Critical patent/EP0035796B1/de
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    • D—TEXTILES; PAPER
    • D01—NATURAL OR MAN-MADE THREADS OR FIBRES; SPINNING
    • D01F—CHEMICAL FEATURES IN THE MANUFACTURE OF ARTIFICIAL FILAMENTS, THREADS, FIBRES, BRISTLES OR RIBBONS; APPARATUS SPECIALLY ADAPTED FOR THE MANUFACTURE OF CARBON FILAMENTS
    • D01F1/00—General methods for the manufacture of artificial filaments or the like
    • D01F1/02—Addition of substances to the spinning solution or to the melt
    • D01F1/08—Addition of substances to the spinning solution or to the melt for forming hollow filaments
    • D—TEXTILES; PAPER
    • D01—NATURAL OR MAN-MADE THREADS OR FIBRES; SPINNING
    • D01F—CHEMICAL FEATURES IN THE MANUFACTURE OF ARTIFICIAL FILAMENTS, THREADS, FIBRES, BRISTLES OR RIBBONS; APPARATUS SPECIALLY ADAPTED FOR THE MANUFACTURE OF CARBON FILAMENTS
    • D01F1/00—General methods for the manufacture of artificial filaments or the like
    • D01F1/02—Addition of substances to the spinning solution or to the melt
    • D01F1/10—Other agents for modifying properties
    • D—TEXTILES; PAPER
    • D01—NATURAL OR MAN-MADE THREADS OR FIBRES; SPINNING
    • D01F—CHEMICAL FEATURES IN THE MANUFACTURE OF ARTIFICIAL FILAMENTS, THREADS, FIBRES, BRISTLES OR RIBBONS; APPARATUS SPECIALLY ADAPTED FOR THE MANUFACTURE OF CARBON FILAMENTS
    • D01F6/00—Monocomponent artificial filaments or the like of synthetic polymers; Manufacture thereof
    • D01F6/88—Monocomponent artificial filaments or the like of synthetic polymers; Manufacture thereof from mixtures of polycondensation products as major constituent with other polymers or low-molecular-weight compounds
    • D01F6/92—Monocomponent artificial filaments or the like of synthetic polymers; Manufacture thereof from mixtures of polycondensation products as major constituent with other polymers or low-molecular-weight compounds of polyesters

Definitions

  • the present invention relates to 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, and a process for producing the same.
  • thermoplastic synthetic filament having a desired gloss and frictional property
  • an inert inorganic substance for example, titanium dioxide of china clay
  • 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.
  • the dispersed inorganic particles 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
  • 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 200°C
  • D represents a draw ratio satisfying the relationship (4): wherein R o 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.
  • thermoplastic synthetic filaments of the present invention are capable of being converted into filaments having an excellent water-absorbing property by treating them with an aqueous alkali solution in order to remove said protuberances and to cause formation of numerous corresponding 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.
  • 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 axis of the individual filament, in the matrix polymer.
  • this type of filament it is characteristic that a portion of the dispersed polymer located in the peripheral surface of the filament, forms numerous fine protuberances with a number of at least 5 per 10 pm 2 , 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 of fibers from corresponding starting materials and about dissolving one of the components by means of a suitable dissolving agent.
  • thermoplastic synthetic filaments having a satisfactory tensile strength, ultimate elongation, breaking modulus and snap-back value without being subject to fibrillation.
  • thermoplastic synthetic filaments of the type indicated above being characterized in that said dispersed polymer consists of at least one polysulfone polymer, and numerous fine protuberances consisting of said dispersed polysulfone polymer are formed in the number of at least 5 per 10 pm 2 on the peripheral surface of each individual filament.
  • thermoplastic synthetic filaments Furthermore, it is the object of the present invention to provide a process for producing such thermoplastic synthetic filaments. This object is accomplished by the process according to patent claim 11.
  • filaments according to this invention are 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.
  • the inventive 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 a drawn-false twisted filament yarn by draw-false twisting the filament yarn under the conditions satisfying the relationship (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 200°C and D represents a draw ratio satisfying the relationship (4): wherein R o 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.
  • thermoplastic synthetic filaments of the present invention are capable of being converted into filaments having an excellent water-absorbing property by treating them with an aqueous alkali solution in order to remove said protuberances and to cause formation of numerous corresponding 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.
  • 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 axis of the individual filament, in the matrix polymer.
  • this type of filament it is characteristic that a portion of the dispersed polymer located in the peripheral surface of the filament, forms numerous fine protuberances with a number of at least 5 per 10 pm 2 , 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.
  • 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.
  • the matrix polyester has a limited (intrinsic) viscosity of 0.4 or more measured in o-chlorophenol at a temperature of 35°C.
  • 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 consists of at least one polysulfone polymer which 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 150°C.
  • 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. When 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): and
  • 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.
  • amount of the dispersed polymer is less than 1% by weight, the number of the resultant protuberances is less than 5 per 10 J.lm2 of the peripheral surface of the resultant filament, and, therefore, the surface appearance and the frictional property of the resultant filament are unsatisfactory.
  • 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.
  • 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 ⁇ m 2 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 exhibits 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.
  • 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 pm 2 or more.
  • the filaments of the present invention may have a circular cross-sectional profile or an irregular cross-sectional 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 thermal 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.
  • 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.
  • thermoplastic 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 consists of at least one polysulfone polymer and 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.
  • a spinning process which may be a melt spinning process, dry spinning process or wet spinning process.
  • the matrix polymer is a polyester
  • the mixture containing the polyester is subjected to a melt-spinning process.
  • the filaments of the present invention 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 a 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): 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 of % 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.
  • the filaments sometimes exhibit a poor stretch-breaking property in the draft zone system spinning process and the fabric made from the filaments sometimes exhibits an unsatisfactory raising property in the raising process. That is, sometimes, the resultant spun yarn is uneven and the resultant raised fabric exhibits as uneven surface appearance.
  • the filaments of the present invention exhibit a breaking modulus of 3.64 g/dtex (4 g/den) or less.
  • breaking modulus used herein is defined by the equation (2): wherein Mb represents a breaking modulus in g/dtex (g/den) 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 titer in (dtex/den) of the filament.
  • the filaments having a breaking modulus of 3.64 g/dtex (4 g/den) or less can exhibit a proper stretch-breaking property and raising property.
  • the filaments of the present invention in which the matrix polymer is preferably 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.
  • 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 40% 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 100°C, 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.
  • each concave has an opening area of at least 5 pm 2. Also, it is preferable that the number of the concaves is at least one per 300 pm 2 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.
  • 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 specific and was obtained only by alkali treating the filament of the present invention.
  • the alkali treatment applied to the filaments of the present invention does not cause the resistance of the resultant filament to fibrillation to be reduced. That is, the alkali treated filaments exhibit a satisfactory resistance to abrasion.
  • 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 of a filament yarn, are draw-false twisted under the conditions satisfying the relationship (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 200°C and D represents a draw ratio to be applied to the filament yarn satisfying the relationship (4): wherein R o represents a draw ratio which causes the 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): wherein TN represents the number of twists applied to the filament yarn and De and De' represent a titer in dtex(den) 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 adequate 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 titer of the resultant individual filament.
  • the spinning process is performed at a high speed of 2000 to 5500 m/sec.
  • 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 200°C, from the conventional draw-false twisting procedure for conventional polyester filament yarn.
  • the draw-false twisting temperature to be applied to the polyester filament yarn is 215°C or more.
  • such high temperature causes the individual filaments in the yarn to be fuse-bonded to each other and the dyeing affinity of the filament yarn to be significantly changed.
  • the draw-false twisting temperature is relatively low. Therefore, the change in the dyeing affinity of the filament yarn is very small and the filament yarn exhibits a satisfactory draping property.
  • 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.
  • Example 1 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 3 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.
  • 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°C.
  • 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 90°C for 0.3 seconds, and drawn at a draw ratio of 3.3.
  • Example 1 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 3 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.
  • 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°C.
  • 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 90°C for 0.3 seconds, and drawn at a draw ratio of 3.3.
  • Example 1 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 3 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.
  • 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°C.
  • 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 90°C for 0.3 seconds, and drawn at a draw ratio of 3.3.
  • 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.
  • Example 12 through 16 and Comparative Examples 6, 7 and 8 the amount as indicated in Table 3 of the same dispersed 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 160°C for 4 hours and melt-extruded 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 90°C for 0.3 seconds on a heating roll and drawn at a draw ratio of 2.8.
  • the drawn filament yarn was bent-treated at 210°C by using a slit heater and wound at a speed of 800 m/min. The results are shown in Table 3.
  • 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.
  • Example 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 295°C, 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 220°C.
  • the properties of the resultant filament yarn are indicated in Table 4.
  • 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.
  • Example 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 295°C, 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 220°C.
  • the properties of the resultant filament yarn are indicated in Table 4.
  • 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.
  • 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.
  • the water absorption was determined as follows. A test specimen was completely dried and the weight (W o ) of the dried specimen was measured. The specimen was immersed in water at room temperature for 30 minutes and, then, centrifugalized for 5 minutes by using a home centrifuge. The weight (W i ) of the centrifugalized specimen was measured. The water absorption (WA) of the specimen was calculated from the following equation.
  • 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 82.5 dtex/36 filaments, and having a weight of 90 g/m 2 under a load of 5 N 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.
  • Example 22 through 26 and Comparative 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 230°C.
  • Example 17 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.
  • Example 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 titer of 165 dtex/36 filaments. That is, the resultant filaments were partially oriented filaments.
  • the results are indicated in Table 8.
  • 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 yarn-like configuration and touch.
  • Example 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.

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  • Chemical & Material Sciences (AREA)
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Claims (26)

1. Thermoplastische synthetische Fasern, welche 85 bis 99 Gew.-% eines thermoplastischen Matrixpolymers und 1 bis 15 Gew.-% eines mit dem Matrixpolymer nicht kompatiblen, dispergierten Polymers enthalten, welches in Form feiner Partikel in dem Matrixpolymer dispergiert ist, wobei die Fasern dadurch gekennzeichnet sind, daß das dispergierte Polymer aus mindestens einem Polysulfonpolymer besteht und daß zahlreiche feine Vorsprünge, die aus dem dispergierten Polysulfonpolymer bestehen, in einer Anzahl von mindestens 5 pro 10 pm2 an der Mantelfläche jeder einzelnen Faser ausgebildet sind.
2. Fasern gemäß Anspruch 1, bei denen jeder der Vorsprünge die Form einer Halbkugel, eines Halbsphäroids oder eine Halbellipsoids hat, welches sich längs der Längsache der einzelnen Faser erstreckt.
3. Fasern gemäß Anspruch 1, bei denen die Bodenfläche der Vorsprünge 0,5 pmz oder mehr beträgt.
4. Fasern gemäß Anspruch 1, bei denen das Matrixpolymer ein thermoplastischer Polyester ist.
5. Fasern gemäß Anspruch 4, bei denen der Polyester im wesentlichen aus wiederkehrenden Ethylenterephthalat-Einheiten besteht.
6. Fasern gemäß Anspruch 1, bei denen das dispergierte Polymer nicht-kritstallin ist und eine Glas-Übergangstemperatur von mindestens 150°C besitzt.
7. Fasern gemäß Anspruch 1, bei denen das Polysulfon wiederkehrende Einheiten gemäß (folgender) Formel umfasst:
Figure imgb0032
8. Fasern gemäß Anspruch 1, bei denen die Menge des dispergierten Polymers in dem Bereich von 3 bis 9 Gew.-% liegt.
9. Fasern gemäß Anspruch 1, bei denen die einzelnen Fasern einen Rücksprungwert von 4% oder weniger besitzen, wobei der Rücksprungwert durch die (folgende) Gleichung (1) definiert ist:
Figure imgb0033
wobei SB für einen Rücksprungwert der Fasern in % steht, wobei eb für eine Bruchdehnung der Fasern in % steht, wobei rb für eine Dehnungsrückbildung der Fasern bei ihrem Brechen in % steht und wobei esb für eine Dehnung der Fasern in % steht, die aus der Differenz zwischen der Länge der Faser bei ihrem Brechen und der ursprünglichen Länge der Faser bestimmt wird.
10. Fasern gemäß Anspruch 1, bei denen jede einzelne Faser einen Bruch-Modul von 3,64 g/dtex oder weniger besitzt, wobei der Bruch-Modul durch die (folgende) Gleichung (2) definiert ist:
Figure imgb0034
wobei Mb für einen Bruch-Modul des Filaments in g/dtex steht, wobei sb für einen Gradienten in g/% einer Tangente steht, die durch einen Bruch-Punkt des Filaments auf der Spannungs-Dehnungs-Kurve des Filaments gezogen ist, wobei eb für eine Bruchdehnung des Filaments in % steht und wobei Do für eine Titer des Filaments in dtex steht.
11. Verfahren zum Herstellen thermoplastischer, synthetischer Fasern gemäß Anspruch 1, welches die (folgenden) Schritte umfasst:
Es wird eine Mischung von 85 bis 99 Gew.-% eines thermoplastischen Matrixpolymers mit 1 bis 15 Gew.-% eines dispergierten Polymers hergestellt, welches aus mindestens einem Polysulfonpolymer besteht und welches mit dem Matrixpolymer nicht kompatibel ist, und
diese Mischung wird versponnen, um Fasern zu erzeugen, in jeder von denen das dispergierte Polymer in dem Matrixpolymer dispergiert ist, wobei an der Mantelfläche jeder einzelnen Faser zahlreiche feine Vorsprünge erzeugt werden, die aus dem dispergierten Polymer bestehen, und zwar in einer Anzahl von mindestens 5 pro 10 µm2.
12. Verfahren gemäß Anspruch 11, bei dem die Mischung in einer solchen Weise zubereitet wird, daß das dispergierte Polymer einem Polymerisationsgemisch beigemischt wird, welches Monomere zur Erzeugung des Matrixpolymers enthält, und daß dann das Polymerisationsgemisch mit dem beigemischten Anteil einer Polymerisation der Monomere unterworfen wird.
13. Verfahren gemäß Anspruch 11, bei dem das Matrixpolymer ein thermoplastischer Polyester ist.
14. Verfahren nach Anspruch 13, bei dem der Polyester im wesentlichen aus wiederkehrenden Ethylenterephthalat-Einheiten besteht.
15. Verfahren nach Anspruch 11, bei dem das dispergierte Polymer nicht-kristallin ist und eine Glasübergangstemperatur von mindestens 150°C besitzt.
16. Verfahren nach Anspruch 11, bei dem das Polysulfon die wiederkehrende Einheit gemäß (folgender) Formel umfasst:
Figure imgb0035
17. Verfahren gemäß Anspruch 11, bei dem die Menge des dispergierten Polymers in dem Bereich von 3 bis 9 Gew.-% liegt.
18. Verfahren nach Anspruch 11, bei dem die Fasern, welche Polyesterfasern in einem teilweise orientierten Zustand sind und in Form eines Filamentgarns vorliegen, einer Streck- Falschdrahttexturierung unter Bedingungen unterworfen werden, welche die (folgende) Beziehung (3) erfüllen:
Figure imgb0036
wobei a für einen Drehungsmultiplikator steht, dem das Filamentgarn zu unterwerfen ist und der im Bereich von 0,4 bis 0,9 liegt, wobei T für eine Falschdrahterzeugungstemperatur steht, die in dem Filamentgarn zu erzeugen ist und die in dem Bereich von 150 bis 200°C liegt, und wobei D für ein Verstreckungsverhältnis steht, welchem das Filamentgarn zu unterwerfen ist und welches die (folgende) Beziehung (4) erfüllt:
Figure imgb0037
wobei Ro für ein Verstreckungsverhältnis steht, welches bewirkt, daß das resultierende gestreckte Filamentgarn eine Bruchdehnung von 30% zeigt, um (auf diese Weise) ein gestrecktes, falschdrahttexturiertes Filamentgarn zu erhalten.
19. Verfahren nach Anspruch 18, bei dem das teilweise orientierte Filamentgarn eine Bruchdehnung von 70 bis 200% besitzt.
20. Verfahren nach Anspruch 11, bei dem das Matrixpolymer vorzugsweise ein Polyester ist und derart modifiziert wird, daß die resultierenden Fasern zusätzlich mit einer wässrigen alkalischen Lösung behandelt werden, um zu bewirken, daß die einzelnen behandelten Fasern zahlreiche Hohlräume haben, von denen jeder aus einem mittleren Teil in Form einer Halbkugel, eines Halbsphäroids oder eines Halbellipsoids und einem Paar von Flügelteilen zusammengesetzt ist, von denen jeder die Form eines Halbkegels oder eines elliptischen Halbkegels hat, und die sich, ausgehend von dem mittleren Teil, in entgegengesetzte Richtungen erstrecken, und zwar längs der Längsachse der einzelnen Faser.
21. Verfahren gemäß Anspruch 20, bei dem die wässrige alkalische Lösung 0,01 bis 40 Gew.-% des alkalischen Stoffes enthält.
22. Verfahren nach Anspruch 20, bei dem die Alkalibehandlung bei einer Temperatur durchgeführt wird, die von der Raumtemperatur bis zu 100°C reicht.
23. Verfahren gemäß Anspruch 20, bei dem die Alkalibehandlung eine Gewichtsreduzierung der Filamente in einem Umfang von mindestens 10% des ursprünglichen Gewichts derselben bewirkt.
24. Poröse Faser, welche nach dem Verfahren gemäß Anspruch 20 erhältlich ist.
25. Faser nach Anspruch 24, bei dem die Hohlräume jeweils eine Öffnungsfläche von mindestens 5 um2 besitzen.
26. Faser nach Anspruch 24, bei dem die Anzahl der Hohlräume mindestens 1 pro 300 gM 2 der Mantelfläche der einzelnen Faser beträgt.
EP81101790A 1980-03-12 1981-03-11 Thermoplastische synthetische Fasern und Verfahren zu deren Herstellung Expired EP0035796B1 (de)

Applications Claiming Priority (11)

Application Number Priority Date Filing Date Title
JP30259/80 1980-03-12
JP3025980A JPS56127660A (en) 1980-03-12 1980-03-12 Thermoplastic formed product
JP33948/80 1980-03-19
JP3394780A JPS56131663A (en) 1980-03-19 1980-03-19 Production of thermoplastic molded article
JP3394880A JPS56134213A (en) 1980-03-19 1980-03-19 Polyester fiber
JP33947/80 1980-03-19
JP7418480A JPS57145A (en) 1980-06-04 1980-06-04 Porous molded article
JP7486280A JPS571727A (en) 1980-06-05 1980-06-05 Manufacture of porous molded form
JP11111980A JPS5739227A (en) 1980-08-14 1980-08-14 Production of hard twisted type processed yarn
JP11112080A JPS5739228A (en) 1980-08-14 1980-08-14 Production of hard twisted type processed yarn with improved drapeng property
JP13225580A JPS5761718A (en) 1980-09-25 1980-09-25 Polyester fiber

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Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP2123189A1 (de) 2008-05-20 2009-11-25 Braun Gmbh Zahnbürste, Zahnbürstenfaser und Verfahren zu deren Herstellung
US7943699B2 (en) 2003-10-21 2011-05-17 E. I. Du Pont De Nemours And Company Ethylene copolymer modified oriented polyester films, tapes, fibers and nonwoven textiles

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EP0080274B1 (de) * 1981-11-23 1986-05-14 Imperial Chemical Industries Plc Verfahren zum Schmelzspinnen einer Mischung eines faserformenden Polymers und eines unvermischbaren Polymers und entsprechend hergestellte Fasern
GB8316323D0 (en) * 1983-06-15 1983-07-20 Ici Plc Producing polyamide fibre
HUT51579A (en) * 1987-11-24 1990-05-28 Mta Termeszettu Domanyi Kutato Process for producing hydraulic bonded objects containing synthetic strengthening fibres
KR940005836A (ko) * 1992-05-14 1994-03-22 히로시 이따가끼 심색성이 우수한 폴리에스테르섬유 및 그의 제조방법
US5993712A (en) * 1997-02-25 1999-11-30 Lurgi Zimmer Aktiengesellschaft Process for the processing of polymer mixtures into filaments
ITMI20021373A1 (it) 2002-06-21 2003-12-22 Effeci Engineering S A S Di Fo Mescole polimeriche e loro uso
EP1730236A1 (de) 2004-03-05 2006-12-13 E.I.Du pont de nemours and company Ethylencopolymer-modifiziertes polyamidprodukt
EP2198744B1 (de) 2008-12-19 2011-11-09 Braun GmbH Borstenbüschel und Zahnbürste mit Borstenbüschel
WO2021035122A1 (en) * 2019-08-22 2021-02-25 Penn Color, Inc. Delustered fiber
CN116043362B (zh) * 2022-12-13 2024-02-27 东华大学 一种具有表面凹凸结构的聚合物纤维及其制备方法

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EP0022182A1 (de) * 1979-06-11 1981-01-14 Teijin Limited Synthetischer Polyester-Papierfaserstoff und Verfahren zu seiner Herstellung
EP0023664A1 (de) * 1979-07-26 1981-02-11 Teijin Limited Verfahren zur Herstellung von hohlen hydrophilen Polyester-Filamenten
EP0033592A2 (de) * 1980-01-31 1981-08-12 Imperial Chemical Industries Plc Leitende Polymere, daraus hergestellte Fasern und Verfahren zur Herstellung
EP0037968A2 (de) * 1980-04-07 1981-10-21 Teijin Limited Gewebte oder gestrickte Stoffbahn aus Polyester-Multifilamentgarn
EP0038429A2 (de) * 1980-03-25 1981-10-28 Teijin Limited Antistatische Polyesterfasern
EP0049412A1 (de) * 1980-09-25 1982-04-14 Teijin Limited Multifilament-Polyestergarn und Verfahren zu dessen Herstellung
EP0060819A1 (de) * 1981-03-05 1982-09-22 Nordiskafilt Ab Verfahren zur Herstellung von schmutzabweisenden Geweben, insbesondere von Geweben, die bei Papier- und Zellstoffmaschinen verwendet werden, und von Filtertüchern für die Papier- und Zellstoffindustrie und anverwandte Industrien

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EP0022182A1 (de) * 1979-06-11 1981-01-14 Teijin Limited Synthetischer Polyester-Papierfaserstoff und Verfahren zu seiner Herstellung
EP0023664A1 (de) * 1979-07-26 1981-02-11 Teijin Limited Verfahren zur Herstellung von hohlen hydrophilen Polyester-Filamenten
EP0033592A2 (de) * 1980-01-31 1981-08-12 Imperial Chemical Industries Plc Leitende Polymere, daraus hergestellte Fasern und Verfahren zur Herstellung
EP0038429A2 (de) * 1980-03-25 1981-10-28 Teijin Limited Antistatische Polyesterfasern
EP0037968A2 (de) * 1980-04-07 1981-10-21 Teijin Limited Gewebte oder gestrickte Stoffbahn aus Polyester-Multifilamentgarn
EP0049412A1 (de) * 1980-09-25 1982-04-14 Teijin Limited Multifilament-Polyestergarn und Verfahren zu dessen Herstellung
EP0060819A1 (de) * 1981-03-05 1982-09-22 Nordiskafilt Ab Verfahren zur Herstellung von schmutzabweisenden Geweben, insbesondere von Geweben, die bei Papier- und Zellstoffmaschinen verwendet werden, und von Filtertüchern für die Papier- und Zellstoffindustrie und anverwandte Industrien

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US7943699B2 (en) 2003-10-21 2011-05-17 E. I. Du Pont De Nemours And Company Ethylene copolymer modified oriented polyester films, tapes, fibers and nonwoven textiles
EP2123189A1 (de) 2008-05-20 2009-11-25 Braun Gmbh Zahnbürste, Zahnbürstenfaser und Verfahren zu deren Herstellung
US8099821B2 (en) 2008-05-20 2012-01-24 Braun Gmbh Toothbrush, toothbrush filament and method for manufacturing same

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