EP0035796A1 - Filaments synthétiques thermoplastiques et procédé pour leur fabrication - Google Patents

Filaments synthétiques thermoplastiques et procédé pour leur fabrication Download PDF

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Publication number
EP0035796A1
EP0035796A1 EP81101790A EP81101790A EP0035796A1 EP 0035796 A1 EP0035796 A1 EP 0035796A1 EP 81101790 A EP81101790 A EP 81101790A EP 81101790 A EP81101790 A EP 81101790A EP 0035796 A1 EP0035796 A1 EP 0035796A1
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European Patent Office
Prior art keywords
filaments
filament
polymer
weight
dispersed
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Granted
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EP81101790A
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German (de)
English (en)
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EP0035796B1 (fr
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 JP3394780A external-priority patent/JPS56131663A/ja
Priority claimed from JP3394880A external-priority patent/JPS56134213A/ja
Priority claimed from JP7418480A external-priority patent/JPS57145A/ja
Priority claimed from JP7486280A external-priority patent/JPS571727A/ja
Priority claimed from JP11112080A external-priority patent/JPS5739228A/ja
Priority claimed from JP11111980A external-priority patent/JPS5739227A/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/fr
Publication of EP0035796B1 publication Critical patent/EP0035796B1/fr
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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 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.
  • thermoplastic synthetic filament having a desired gloss and frictional property
  • an inter inorganic substance for example, titanium dioxide or 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 accelerate the wear of the needs in the weaving machine or the needles in the knitting machine.
  • thermoplastic synthetic fibers for example, polyethylene terephthalate fibers
  • polyethylene terephthalate fibers 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 cringed end portions of the fibers or filaments cause the appearance of the raised fabric to be poor.
  • thermoplastic synthetic filaments for example, polyethylene terephthalate filaments
  • 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.
  • thermoplastic synthetic filaments for example, polyethylene terephthalate filaments
  • polyethylene terephthalate filaments are hydrophobic and, therefore, exhibit a poor water-absorbing property.
  • 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.
  • thermoplastic synthetic filaments of the present invention which 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 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.
  • thermoplastic synthetic filaments can be produced by the process of the present invention which comprises the steps of:
  • 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 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 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.
  • 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.
  • 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.
  • 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 limiting (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 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 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 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.
  • 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 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.
  • 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 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 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.
  • 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.
  • 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.
  • 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 s raising process, it is preferable that the filaments exhibit a snap back value of 4% or less.
  • snap back value used herein is defined by the equation (1):
  • the filaments of the present invention exhibit a breaking modulus of 4 g/d or less.
  • breaking modulus used herein is defined by the equation (2): wherein Mb represents a breaking modulus in g /d 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 D 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.
  • 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 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.
  • 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.
  • the alkali treatment applied to the filaments of the present invention does not cause the resistance of the resultant filament to fibrili- zation 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 a filament yarn, are draw-false twisted under the conditions satisfying the relationship (3):
  • 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 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.
  • 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 dyeability of the filament yarn to be significantly changed.
  • 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.
  • 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.
  • the dispersed polymer may contain at least one member selected from the group consisting of polytetrafluoroethylene, tetrafluoroethylene--hexafluoropropylene copolymers, polychlorotrifluoro- ethylene, 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 10 5 poises or more when these are heated to a temperature of or close to the melting point thereof.
  • the mixture was dried and melted in an extruder at a temperature of 315°C and, then, extruded through a spinneret having 24 spinning orifices each having a diameter of 0.3 mm, at a temperature of 290°C.
  • 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 90°C 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 230°C by using a slit heater and, then, wound up at a speed of 800 m/min.
  • 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.
  • Example 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.
  • 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 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 160°C 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 90°C for 0.3 seconds on a heating roll and drawn 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.
  • 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 ) of o 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 (W 1 ) 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 75 denier/36 filaments, and having a weight of 90 g/m 2 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.
  • Example 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 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 denier of 150/36 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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  • Engineering & Computer Science (AREA)
  • Chemical & Material Sciences (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • General Chemical & Material Sciences (AREA)
  • Textile Engineering (AREA)
  • Manufacturing & Machinery (AREA)
  • Artificial Filaments (AREA)
EP81101790A 1980-03-12 1981-03-11 Filaments synthétiques thermoplastiques et procédé pour leur fabrication Expired EP0035796B1 (fr)

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
JP3394880A JPS56134213A (en) 1980-03-19 1980-03-19 Polyester fiber
JP3394780A JPS56131663A (en) 1980-03-19 1980-03-19 Production of thermoplastic molded article
JP33947/80 1980-03-19
JP33948/80 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
JP11112080A JPS5739228A (en) 1980-08-14 1980-08-14 Production of hard twisted type processed yarn with improved drapeng property
JP11111980A JPS5739227A (en) 1980-08-14 1980-08-14 Production of hard twisted type processed yarn
JP13225580A JPS5761718A (en) 1980-09-25 1980-09-25 Polyester fiber

Publications (2)

Publication Number Publication Date
EP0035796A1 true EP0035796A1 (fr) 1981-09-16
EP0035796B1 EP0035796B1 (fr) 1986-06-04

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Cited By (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0080274A2 (fr) * 1981-11-23 1983-06-01 Imperial Chemical Industries Plc Procédé pour le filage au fondu d'un mélange d'un polymère constituant la fibre et un polymère incompatible et fibres filés par ce procédé
EP0129317A2 (fr) * 1983-06-15 1984-12-27 Imperial Chemical Industries Plc Procédé pour la fabrication de fibres de polyamide et nouvelles fibres à surface rugueuse obtenues par ce procédé
EP0318137A2 (fr) * 1987-11-24 1989-05-31 Magyar Tudomanyos Akademia Termeszettudomanyi Kutatolaboratoriumai Procédé de fabrication de corps, d'éléments de construction, en particulier à partir de mélanges durcissants hydrauliquement contenant des fibres de renforcement et procédé de fabrication de fibres en matière plastique présentant une surface rendue rugueuse
EP0570227A2 (fr) * 1992-05-14 1993-11-18 Teijin Limited Fibre de polyester ayant une forte affinité tinctoriale et procédé pour sa fabrication
US5993712A (en) * 1997-02-25 1999-11-30 Lurgi Zimmer Aktiengesellschaft Process for the processing of polymer mixtures into filaments
WO2004000938A1 (fr) 2002-06-21 2003-12-31 Effeci Engineering S.A.S. Di Fochesato Antonio & C. Melanges polymeres et leur utilisation
US7267884B2 (en) 2004-03-05 2007-09-11 E. I. Du Pont De Nemours And Company Ethylene copolymer-modified polyamide product
US8448286B2 (en) 2008-12-19 2013-05-28 Braun Gmbh Bristle tufts and toothbrush with bristle tufts
WO2021035122A1 (fr) * 2019-08-22 2021-02-25 Penn Color, Inc. Fibre délustrée
CN116043362A (zh) * 2022-12-13 2023-05-02 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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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 (fr) 2008-05-20 2009-11-25 Braun Gmbh Brosse à dents, filament de brosse à dents et son procédé de fabrication

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GB1169106A (en) * 1966-03-15 1969-10-29 Teijin Ltd Artificial Fiber having Voids and method of manufacture thereof
US3640944A (en) * 1969-01-31 1972-02-08 Minnesota Mining & Mfg Modified polyester film for punched tapes
US3786822A (en) * 1968-10-11 1974-01-22 Toa Wool Spinning & Weaving Co Artificial hair articles and process for the preparation thereof
GB2016364A (en) * 1978-03-08 1979-09-26 Kururay Co Ltd Polyester fibre

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DE3071272D1 (en) * 1979-07-26 1986-01-16 Teijin Ltd Process for producing the same of hollow water-absorbing polyester filaments
EP0033592A3 (fr) * 1980-01-31 1982-12-22 Imperial Chemical Industries Plc Polymères conducteurs, fibres en étant constituées et procédé pour la fabrication de celles-ci
US4357390A (en) * 1980-03-25 1982-11-02 Teijin Limited Antistatic polyester fibers
JPS56144237A (en) * 1980-04-07 1981-11-10 Teijin Ltd Polyester type fiber woven and knitted fabric
JPS5761716A (en) * 1980-09-25 1982-04-14 Teijin Ltd Polyester multifilaments and their production
SE8101413L (sv) * 1981-03-05 1982-09-06 Nordiskafilt Ab Forfarande for framstellning av en vevnad med smutsavvisande egenskaper, foretredesvis formeringsviror for pappers- och cellulosamaskiner samt filterdukar for pappers-, cellulosa- och liknande industrier

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GB1169106A (en) * 1966-03-15 1969-10-29 Teijin Ltd Artificial Fiber having Voids and method of manufacture thereof
US3786822A (en) * 1968-10-11 1974-01-22 Toa Wool Spinning & Weaving Co Artificial hair articles and process for the preparation thereof
US3640944A (en) * 1969-01-31 1972-02-08 Minnesota Mining & Mfg Modified polyester film for punched tapes
GB2016364A (en) * 1978-03-08 1979-09-26 Kururay Co Ltd Polyester fibre

Cited By (17)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0080274A2 (fr) * 1981-11-23 1983-06-01 Imperial Chemical Industries Plc Procédé pour le filage au fondu d'un mélange d'un polymère constituant la fibre et un polymère incompatible et fibres filés par ce procédé
EP0080274A3 (en) * 1981-11-23 1984-03-28 Imperial Chemical Industries Plc Process of melt spinning of a blend of a fibre-forming polymer and an immiscible polymer and melt spun fibres produced by such process
EP0129317A2 (fr) * 1983-06-15 1984-12-27 Imperial Chemical Industries Plc Procédé pour la fabrication de fibres de polyamide et nouvelles fibres à surface rugueuse obtenues par ce procédé
EP0129317A3 (fr) * 1983-06-15 1987-04-15 Imperial Chemical Industries Plc Procédé pour la fabrication de fibres de polyamide et nouvelles fibres à surface rugueuse obtenues par ce procédé
GR880100735A (el) * 1987-11-24 1994-03-31 Magyar Tydomanyos Akademia Ter Μέ?οδος για την παρασκευή σωμάτων ειδικά δομικών μονάδων με την αναμιξή υδραυλικά συνδεομένων, μετασκληραινομένων υλικών & ενισχυτικών ινών, προσέτι μέ?οδος παρασκευής συν?ετικών ινών που έχουν ανώμαλη επιφάνεια.
EP0318137A3 (fr) * 1987-11-24 1990-05-16 Magyar Tudomanyos Akademia Termeszettudomanyi Kutatolaboratoriumai Procédé de fabrication de corps, d'éléments de construction, en particulier à partir de mélanges durcissants hydrauliquement contenant des fibres de renforcement et procédé de fabrication de fibres en matière plastique présentant une surface rendue rugueuse
BE1002500A4 (fr) * 1987-11-24 1991-03-05 Mta Termeszettu Domanyi Kutato Procede de fabrication de corps et, en particulier, d'elements de construction en melanges de materiaux lies hydrauliquement et durcissables et de fibres de renfort qui y sont ajoutees, ainsi que procede de production de fibres de matiere plastique avec surfaces rendues rugueuses.
EP0318137A2 (fr) * 1987-11-24 1989-05-31 Magyar Tudomanyos Akademia Termeszettudomanyi Kutatolaboratoriumai Procédé de fabrication de corps, d'éléments de construction, en particulier à partir de mélanges durcissants hydrauliquement contenant des fibres de renforcement et procédé de fabrication de fibres en matière plastique présentant une surface rendue rugueuse
EP0570227A2 (fr) * 1992-05-14 1993-11-18 Teijin Limited Fibre de polyester ayant une forte affinité tinctoriale et procédé pour sa fabrication
EP0570227A3 (en) * 1992-05-14 1994-06-15 Teijin Ltd Polyester fiber having excellent deep dyeability and process for producing the same
US5993712A (en) * 1997-02-25 1999-11-30 Lurgi Zimmer Aktiengesellschaft Process for the processing of polymer mixtures into filaments
WO2004000938A1 (fr) 2002-06-21 2003-12-31 Effeci Engineering S.A.S. Di Fochesato Antonio & C. Melanges polymeres et leur utilisation
US7267884B2 (en) 2004-03-05 2007-09-11 E. I. Du Pont De Nemours And Company Ethylene copolymer-modified polyamide product
US8448286B2 (en) 2008-12-19 2013-05-28 Braun Gmbh Bristle tufts and toothbrush with bristle tufts
WO2021035122A1 (fr) * 2019-08-22 2021-02-25 Penn Color, Inc. Fibre délustrée
CN116043362A (zh) * 2022-12-13 2023-05-02 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
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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