JP4961901B2 - Crimped yarn, method for producing the same, and fiber structure - Google Patents

Description

  The present invention relates to an air stuffer crimped yarn composed of a polymer alloy synthetic fiber in which an aliphatic polyester resin and a thermoplastic polyamide resin are uniformly blended.

  Recently, with increasing awareness of the environment on a global scale, the development of fiber materials that decompose in the natural environment is eagerly desired. For example, since conventional general-purpose plastics use petroleum resources as a main raw material, global warming caused by the future depletion of petroleum resources and mass consumption of petroleum resources has been taken up as major problems.

  For this reason, in recent years, research and development of various plastics and fibers such as aliphatic polyesters have been activated. Among them, attention is focused on plastics that are decomposed by microorganisms, that is, fibers using biodegradable plastics.

  Moreover, by using plant resources that grow by taking in carbon dioxide from the atmosphere, it can be expected that global warming can be suppressed by the circulation of carbon dioxide, and the problem of resource depletion may be solved. Therefore, attention has been focused on plastics starting from plant resources, that is, plastics using biomass.

  Until now, biodegradable plastics using biomass have not been used as general-purpose plastics due to their low mechanical properties and heat resistance, as well as high manufacturing costs. On the other hand, in recent years, polylactic acid using lactic acid obtained by fermentation of starch as a raw material has attracted attention as a biodegradable plastic having relatively high mechanical properties and heat resistance and low production cost.

  Aliphatic polyester resins represented by polylactic acid have been used for a long time in the medical field, for example, as surgical sutures, but recently, due to the improvement of mass production technology, it has become possible to compete with other general-purpose plastics in terms of price. It was. For this reason, product development as a fiber has been activated.

  The development of aliphatic polyester fibers such as polylactic acid is preceded by agricultural materials and civil engineering materials that make use of biodegradability, followed by large-scale applications such as clothing, interiors such as curtains and carpets, and vehicle interiors. Applications to industrial and industrial materials are also expected. However, the low wear resistance of aliphatic polyesters, particularly polylactic acid, is a major problem when applied to clothing and industrial material applications. For example, when polylactic acid fiber is used for clothing, color transfer easily occurs due to rubbing or the like, and when severe, the fiber becomes fibrillated and whitened, or excessive irritation is given to the skin. It has been found that the practical durability is poor. In addition, when used for automobile interiors, especially carpets that are subject to strong rubbing, the polylactic acid may easily fall down and be scraped, and in severe cases, holes may be formed. In addition, it has been found that aliphatic polyesters (particularly polylactic acid) are likely to be hydrolyzed, and that fibrillation and scraping as described above tend to become severe over time, resulting in a short product life.

  As a method for improving the abrasion resistance of polylactic acid, for example, methods for suppressing hydrolysis are disclosed (Patent Document 1 and Patent Document 2). The invention described in Patent Document 1 suppresses hydrolysis in the fiber production process by suppressing the water content of polylactic acid as much as possible. In Patent Document 2, a monocarbodiimide compound is added. Fibers with improved hydrolysis resistance are disclosed. However, although any fiber has a decrease in wear resistance in terms of suppressing the embrittlement of polylactic acid over time, none of them changes the property of polylactic acid “easy to fibrillate” It has been found that the initial wear resistance is no different from that of conventional products.

  In addition, as a method for greatly improving the wear resistance, polylactic acid fibers in which wear is suppressed by adding a lubricant such as fatty acid bisamide to reduce the friction coefficient of the fiber surface are disclosed (Patent Documents 3 to 3). 6). However, these fibers are effective when the applied force is small, but, for example, when a strong stepping force is applied like a carpet, the adhesion between fibers cannot be sufficiently suppressed. The use was limited.

  Moreover, the technique which improves the mechanical characteristics of a resin composition by the blend of polyamide and aliphatic polyester is disclosed (patent document 7). According to the method described in Patent Document 7, mechanical properties such as strength, heat resistance, and wear resistance are improved by the reinforcing effect of the polyamide. However, in this method, the blend ratio of the polyamide is 5 to 40% and a small amount of components. For this reason, the aliphatic polyester forms a sea component, and the aliphatic polyester and the polyamide are incompatible with each other. Therefore, the adhesiveness at the interface between these phases is inferior. It has been found that there is a problem in that it becomes blurred and white and wear speed is high.

In addition, a technique for suppressing the orientation of polyamide fibers and increasing the elongation by finely dispersing polyester in polyamide is disclosed (Patent Document 8). By using the polymer alloy fiber, when the fiber is mixed with a low-stretch polyamide undrawn yarn during false twisting, the crimped yarn can be given a high swell. However, the polymer alloy fiber is suitable as a sheath yarn during false twisting, but when used in the production of the air stuffer crimped yarn which is the object of the present invention, the fiber orientation is rather insufficient. Therefore, heat shrinkage in the air stuffer crimping apparatus is not sufficient, and only a crimped yarn having a low crimp elongation rate can be obtained without three-dimensional crimping.
JP 2000-136435 A (page 4) JP 2001-261797 A (page 3) JP 2004-91968 A (pages 4-5) JP 2004-204406 A (pages 4-5) JP 2004-204407 A (pages 4 to 5) JP-A-2004-277931 (pages 5-6) JP 2003-238775 A (page 3) JP 2005-206961 A (page 3)

  The present invention provides an air stuffer crimped yarn composed of a polymer alloy synthetic fiber excellent in abrasion resistance and excellent in aesthetics after dyeing, and a fiber structure, which solves the above problems. Let it be an issue.

  The above-described problem is an air stuffer crimped yarn composed of a polymer alloy-based synthetic fiber containing an aliphatic polyester resin (A) and a thermoplastic polyamide resin (B). A crimped yarn having a sea-island structure in which A) forms an island component and the thermoplastic polyamide resin (B) forms a sea component, and a fiber structure comprising at least a portion of the crimped yarn Can be achieved by the body.

  According to the present invention, it is possible to provide a synthetic fiber and a fiber structure that are remarkably improved in wear resistance and can provide a high-quality fiber structure, and that are optimal for general clothing use and industrial material use.

  The aliphatic polyester resin (A) in the present invention (hereinafter sometimes referred to as “component A”) refers to a polymer in which aliphatic alkyl chains are linked by ester bonds. As aliphatic polyester resin (A) used by this invention, it is preferable that it is crystalline, and it is more preferable that melting | fusing point is 150-230 degreeC. Examples of the aliphatic polyester resin (A) used in the present invention include polylactic acid, polyhydroxybutyrate, polybutylene succinate, polyglycolic acid, and polycaprolactone. Among these, polylactic acid is most preferable because of its high melting point and excellent thermal stability among aliphatic polyesters.

The above polylactic _{acid, - (O-CHCH 3 -CO} ) n - is a polymer as a repeating unit, and refers to those obtained by polymerizing lactic acid oligomers, such as lactic acid or lactide. Since lactic acid has two types of optical isomers, D-lactic acid and L-lactic acid, the polymer is poly (D-lactic acid) consisting only of D isomer and poly (L-lactic acid) consisting only of L isomer, and There is polylactic acid consisting of both. As the optical purity of D-lactic acid or L-lactic acid in polylactic acid decreases, the crystallinity decreases and the melting point drop increases. The melting point is preferably 150 ° C. or higher and more preferably 160 ° C. in order to maintain the heat resistance of the fiber. More preferably, it is 170 degreeC or more, Most preferably, it is 180 degreeC or more.

  However, apart from the system in which the polymers of the two optical isomers are simply mixed as described above, the two optical isomer polymers are blended and formed into a fiber, and then a high temperature of 140 ° C. or higher. A stereo complex in which racemic crystals are formed by heat treatment is preferable because the melting point can be increased to 220 to 230 ° C. In this case, “component A” refers to a mixture of poly (L lactic acid) and poly (D lactic acid). When the blend ratio is 40/60 to 60/40, the ratio of stereocomplex crystals can be increased. Is the best. In order to efficiently form the stereocomplex crystal by melt spinning, it is preferable to add a crystal nucleating agent. As the crystal nucleating agent, in addition to talc and layered clay mineral, stearic acid, 12-hydroxystearic acid, stearic acid amide, oleic acid amide, erucic acid amide, methylene bis stearic acid amide, ethylene bis, which are highly compatible with polylactic acid Stearic acid amide, ethylene bisoleic acid amide, butyl stearate, monoglyceride stearate, calcium stearate, zinc stearate, magnesium stearate, lead stearate and the like can be applied.

  In addition, residual lactide exists in polylactic acid as low molecular weight residues, but these low molecular weight residues induce staining abnormalities such as heating heater stains in stretching and bulky processing processes and dyeing spots in dyeing processing processes. It may cause. Moreover, hydrolysis of a fiber or a fiber molded product is promoted, and durability may be reduced. Therefore, the amount of residual lactide in polylactic acid is preferably 0.3% by weight or less, more preferably 0.1% by weight or less, and still more preferably 0.03% by weight or less.

  Component A may be a copolymer of components other than lactic acid, for example, within a range that does not impair the properties of polylactic acid. The components to be copolymerized include polyalkylene ether glycols such as polyethylene glycol, aliphatic polyesters such as polybutylene succinate and polyglycolic acid, aromatic polyesters such as polyethylene isophthalate, and hydroxycarboxylic acids, lactones, dicarboxylic acids, and diols. An ester bond-forming monomer such as Among these, a polyalkylene ether glycol having good compatibility with the thermoplastic polyamide resin (B) (hereinafter sometimes referred to as “component B”) is preferable. The copolymerization ratio of such a copolymer component is preferably 0.1 to 10 mol% with respect to polylactic acid as long as the heat resistance deterioration due to the melting point drop is not impaired.

  Component A may further contain particles, coloring pigments, crystal nucleating agents, flame retardants, plasticizers, antistatic agents, antioxidants, ultraviolet absorbers, lubricants, and the like as modifiers. Color pigments include carbon black, titanium oxide, zinc oxide, barium sulfate, iron oxide, and other inorganic pigments, as well as cyanine, styrene, phthalocyanine, anthraquinone, perinone, isoindolinone, and quinophthalone. Organic pigments such as quinocridone and thioindigo can be used. Similarly, modifiers such as various inorganic particles such as calcium carbonate, silica, silicon nitride, clay, talc, kaolin, and zirconium acid, and particles such as crosslinked polymer particles and various metal particles can also be used. Furthermore, waxes, silicone oils, various surfactants, various fluororesins, polyphenylene sulfides, polyamides, polyacrylates such as ethylene / acrylate copolymers, methyl methacrylate polymers, various rubbers, ionomers, polyurethanes And other polymers such as thermoplastic elastomers can be contained in small amounts.

  Examples of the lubricant preferably used for the component A include fatty acid amides and / or fatty acid esters. Examples of the fatty acid amide include lauric acid amide, palmitic acid amide, stearic acid amide, erucic acid amide, behenic acid amide, methylol stearic acid amide, methylol behenic acid amide, dimethylol oil amide, dimethyl lauric acid amide, and dimethyl stearic acid. A compound having two amide bonds in one molecule such as amide, saturated fatty acid bisamide, unsaturated fatty acid bisamide, aromatic bisamide, etc., for example, methylene biscaprylic acid amide, methylene biscapric acid amide, methylene bislauric acid amide , Methylene bis myristic acid amide, methylene bis palmitic acid amide, methylene bis stearic acid amide, methylene bis isostearic acid amide, methylene bis behenic acid amide, methylene bis oleic acid amide, methyle Biserucic acid amide, ethylene biscaprylic acid amide, ethylene biscapric acid amide, ethylene bislauric acid amide, ethylene bismyristic acid amide, ethylene bispalmitic acid amide, ethylene bisstearic acid amide, ethylene bisisostearic acid amide, ethylene bisbehe Ninamide, Ethylene bisoleic acid amide, Ethylene bis erucic acid amide, Butylene bis stearic acid amide, Butylene bis behenic acid amide, Butylene bis oleic acid amide, Butylene bis erucic acid amide, Hexamethylene bis stearic acid amide, Hexa Methylene bis behenic acid amide, hexamethylene bis oleic acid amide, hexamethylene bis erucic acid amide, m-xylylene bis stearic acid amide, m-xylylene bis-12-hydro Sistearic acid amide, p-xylylene bis stearic acid amide, p-phenylene bis stearic acid amide, p-phenylene bis stearic acid amide, N, N′-distearyl adipic acid amide, N, N′-distearyl sebacic acid Amide, N, N′-dioleyl adipic acid amide, N, N′-dioleyl sebacic acid amide, N, N′-distearyl isophthalic acid amide, N, N′-distearyl terephthalic acid amide, methylenebishydroxystearin Acid amide, ethylene bishydroxystearic acid amide, butylene bishydroxystearic acid amide, hexamethylene bishydroxystearic acid amide, etc., and other alkyl-substituted fatty acid monoamides such as saturated fatty acid monoamides and unsaturated fatty acid monoamides. For example, N-lauryl lauric acid amide, N-palmityl palmitic acid amide, N-stearyl stearic acid amide, N-behenyl behenic acid amide, N-oleyl Examples include oleic acid amide, N-stearyl oleic acid amide, N-oleyl stearic acid amide, N-stearyl erucic acid amide, N-oleyl palmitic acid amide and the like. The alkyl group may have a substituent such as a hydroxyl group introduced into its structure. For example, methylol stearamide, methylol behenic acid amide, N-stearyl-12-hydroxystearic acid amide, N- Oleyl 12 hydroxystearic acid amide and the like are also included in the alkyl-substituted fatty acid monoamide of the present invention.

  Examples of fatty acid esters include lauric acid cetyl ester, lauric acid phenacyl ester, myristic acid cecil ester, myristic acid phenacyl ester, palmitic acid isopropylidene ester, palmitic acid dodecyl ester, palmitic acid tetradodecyl ester, and palmitic acid pentadecyl ester. Aliphatic monocarboxylic acid esters such as ester, palmitic acid octadecyl ester, palmitic acid cecil ester, palmitic acid phenyl ester, palmitic acid phenacyl ester, stearic acid, cecil ester, behenic acid ethyl ester; monolauric acid glycol, monopalmitic acid Glycols, monoesters of ethylene glycol such as monostearate glycol, glycol dilaurate, glycosyl dipalmitate Diesters of glycols such as glyceryl distearate; monoesters of glycerin such as monolauric acid glycerin ester, monomyristylic acid glycerin ester, monopalmitic acid glycerin ester, monostearic acid glycerin ester; dilauric acid glycerin ester, dimistylic acid glycerin ester Glycerin diesters such as glycerin dipalmitate, glyceryl distearate; glyceryl trilaurate, glyceryl trimristylate, glycerin tripalmitate, glyceryl tristearate, palmitodiolein, palmitodistearin and oleodistearin And the like, and the like.

  Among these compounds, it is preferable to use fatty acid bisamides and alkyl-substituted fatty acid monoamides. Fatty acid bisamides and alkyl-substituted fatty acid monoamides are less reactive than amides of ordinary fatty acid monoamides, so that they do not easily react with polylactic acid during melt molding, and are also heat resistant due to their high molecular weight. It is high and does not sublime easily by melt molding, and exhibits excellent slipperiness without impairing the function as a lubricant. In particular, fatty acid bisamides can be used more preferably because the reactivity of amides is even lower, and ethylene bisstearic acid amide is more preferred.

  Two or more fatty acid amides and fatty acid esters may be used, or fatty acid amides and fatty acid esters may be used in combination.

  The content of the fatty acid amide and / or fatty acid ester needs to be 0.1% by weight or more based on the fiber weight in order to exhibit the above characteristics. Further, if the content is too large, the mechanical properties of the fiber may be lowered, or the color tone may be deteriorated when dyed with yellowishness, so the content is preferably 5% by weight or less. The content of the fatty acid amide and / or fatty acid ester is more preferably 0.2 to 4% by weight, still more preferably 0.3 to 3% by weight.

  The molecular weight of the polylactic acid polymer is preferably high in order to increase the wear resistance. However, if the molecular weight is too high, the moldability and stretchability in melt spinning tend to decrease. The weight average molecular weight is preferably 80,000 or more, more preferably 100,000 or more in order to maintain wear resistance. More preferably, it is 120,000 or more. On the other hand, when the molecular weight exceeds 350,000, the stretchability is lowered as described above. As a result, the molecular orientation is deteriorated and the fiber strength is sometimes lowered. Therefore, the weight average molecular weight is preferably 350,000 or less, and more preferably 300,000 or less. More preferably, it is 250,000 or less. The weight average molecular weight is a value determined by gel permeation chromatography (GPC) and calculated in terms of polystyrene.

  The production method of polylactic acid preferably used for component A of the present invention is not particularly limited, but specifically, a direct dehydration condensation method in which lactic acid is dehydrated and condensed as it is in the presence of an organic solvent and a catalyst (Japanese Patent Laid-Open No. 6-65360). And a method in which at least two homopolymers are copolymerized and transesterified in the presence of a polymerization catalyst (see JP-A-7-173266). An indirect polymerization method (see U.S. Pat. No. 2,703,316) in which ring-opening polymerization is carried out after the formation of the polymer is mentioned.

  The thermoplastic polyamide resin (B) used in the present invention refers to a polymer having an amide bond. Examples of the thermoplastic polyamide resin (B) used in the present invention include polycapramide (nylon 6), Polytetramethylene adipamide (nylon 46), polyhexamethylene adipamide (nylon 66), polyundecanamide (nylon 11), polydodecanamide (nylon 12), polyhexamethylene sebamide (nylon 610), poly And pentamethylene sebacamide (nylon 510). Among these, nylon 6 is preferable in terms of raw material cost, and in order to increase compatibility with component A and enhance interfacial adhesion, it is better that the methylene chain length of the polyamide is long. 12, nylon 610 and nylon 510 are preferred. The polyamide may be a homopolymer or a copolymer. In addition, to Component B, particles, a flame retardant, an antistatic agent, the lubricant preferably used for Component A, and the like may be added. The solution viscosity of the thermoplastic polyamide is measured using a 98% sulfuric acid solution described later in the case of nylon 6 or nylon 610, and the intrinsic viscosity of nylon 11 is measured using a metacresol solution. Can be measured by the method.

  In general, when an aliphatic polyester has a melting point, the melting point is usually not higher than 200 ° C., and thus the heat resistance is not high. If the temperature exceeds 250 ° C. during melt storage, the physical properties tend to deteriorate rapidly. . Therefore, the thermoplastic polyamide resin (B) to be blended preferably has a melting point of 150 to 250 ° C, and more preferably 150 to 225 ° C. More preferably, it is 150-205 degreeC. However, in consideration of the heat resistance of the crimped yarn, the melting point of the thermoplastic polyamide resin (B) is preferably higher than that of the aliphatic polyester (A). As described above, the thermoplastic polyamide resin may be a copolymer. However, since the wear resistance tends to decrease when the crystallinity is lowered, the thermoplastic polyamide resin is preferably crystalline.

  In the present invention, the presence or absence of crystallinity can be determined to be crystalline if the melting peak can be observed by differential scanning calorimetry (DSC) measurement. Further, the higher the crystallinity, the better. The index can be determined by the magnitude of the crystal melting peak calorific value in DSC. The crystal melting peak heat quantity ΔH is preferably 30 J / g, more preferably 40 J / g, and still more preferably 60 J / g.

  The blend ratio of component A and component B of the present invention is not particularly limited, but in order to make a polymer alloy having a sea-island structure in which component A is an island component and component B is a sea component, a blend of component A / component B The ratio (% by weight) is preferably in the range of 5/95 to 55/45. Further, when increasing the ratio of component A, it is necessary to increase the melt viscosity ηa of component A, and when increasing the ratio of component B, it is necessary to increase the melt viscosity ηb of component B.

In the present invention, it is necessary that component A is an island component and component B is a sea component. Therefore, the blending ratio of component A and component B becomes easier as the ratio of component B is increased. Therefore, it is more preferably 10/90 to 45/55, more preferably 15/85 to 40/60, and most preferably 20 / 80 to 35/65. The ratio of melt viscosity (ηb / ηa) is preferably in the range of 0.1-2. More preferably, it is 0.15-1.5, More preferably, it is 0.2-1. Although the method for measuring the melt viscosity η will be described in detail later, the measurement temperature is the same as the spinning temperature and is a value measured at a shear rate of 1216 sec ⁻¹ .

  In the present invention, it is important that the component A and the component B are uniformly blended. Here, the term “uniformly blended” refers to the following state. That is, when a cross-sectional slice of the synthetic fiber is observed with a transmission electron microscope (TEM) (40,000 times), a continuous matrix component (black portion) is formed into a sea component and a substantially circular shape as shown in FIG. The island size is taken as a so-called sea-island structure, and the domain size of the component A constituting the island component is converted into a diameter (the domain is assumed to be a circle, and converted from the area of the domain). This means that the diameter is reduced to 0.001 to 2 μm. By setting the domain size of the island component within the above range, the abrasion resistance of the fiber can be dramatically improved. The adhesion with the component B constituting the sea component is improved because the stress concentration at the interface is dispersed as the domain size is smaller. On the other hand, when the domain size is a certain size or less, the initial wear resistance is improved. It tends to decrease. Therefore, the size of the island domain is preferably 0.005 to 1.5 μm, and more preferably 0.02 to 1.0 μm. Moreover, in order to control the glossiness of the crimped yarn, it is preferable that the domain diameter is further in a specific range. The domain diameter covers the visible light wavelength range (0.4 to 0.8 μm) and up to 1/5 wavelength (0.08 to 0.16 μm) of the wavelength, thereby allowing moderate light scattering inside the fiber. It is possible to provide a moist and lustrous gloss. In order to express beautiful glossiness, the domain diameter is preferably in the range of 0.08 to 0.8 μm.

  The domain size in the present invention is measured for 100 domains per crimped yarn sample as will be described later in section G of the examples, and the 10 largest and 10 smallest domain diameters are measured. Refers to 80 distributions excluding values.

  Further, since the material constituting the crimped yarn of the present invention is a polymer alloy, unlike a block copolymer in which an aliphatic polyester block and a polyamide block are alternately present in one molecular chain, an aliphatic polyester molecular chain ( It is important that component A) and the polyamide molecular chain (component B) exist substantially independently. The difference in this state is that the melting point drop of the thermoplastic polyamide resin before and after blending, that is, how much the melting point derived from the thermoplastic polyamide resin in the polymer alloy fell from the melting point of the thermoplastic polyamide resin before blending is observed. Can be estimated. If the melting point drop of the thermoplastic polyamide resin is 3 ° C. or less, the aliphatic polyester and the polyamide are hardly copolymerized (almost no ester-amide exchange occurs), and the aliphatic polyester molecular chain is substantially The polyamide molecular chain is a polymer alloy that exists independently. Further, since the fiber surface layer is a thermoplastic polyamide resin that is substantially a sea component, the inherent properties of the thermoplastic polyamide resin are reflected, and the wear resistance is dramatically improved. Therefore, in the present invention, the melting point drop of the blended polyamide is preferably 2 ° C. or less.

  As described above, the crimped yarn of the present invention comprises a synthetic fiber composed of an aliphatic polyester resin and a polymer alloy containing a thermoplastic polyamide resin. The aliphatic polyester resin is an island component, and the thermoplastic polyamide resin is a seawater. It forms a sea-island structure with components. In addition, by controlling the domain size of the island component, the wear resistance is drastically improved and a high-quality gloss is exhibited.

  Here, as described above, since the aliphatic polyester and the polyamide usually hardly react (ester-amide exchange hardly occurs), the interfacial adhesion of the two polymers is not so high as it is. Therefore, the wear resistance can be improved by adding a compatibilizing agent (hereinafter sometimes referred to as “component C”) to drastically improve the interfacial adhesion. Component C is not particularly limited as long as it improves the interfacial adhesion between Component A and Component B, but when it is a compound having two or more active hydrogen reactive groups in one molecule, Interfacial adhesion can be dramatically improved, which is preferable. A compound having two or more active hydrogen reactive groups in one molecule is added to component A and / or component B and melt blended to perform spinning, so that the compound is any component of component A and component B. Since both react with each other to form a cross-linked structure, interfacial peeling can be suppressed.

Here, the active hydrogen reactive group is a group having reactivity with a COOH terminal group, an OH terminal group, or an NH ₂ terminal group present at the terminal of a polylactic acid resin or a thermoplastic polyamide resin, such as a glycidyl group or an oxazoline. Group, carbodiimide group, aziridine group, imide group, isocyanate group, maleic anhydride group and the like are preferably used. In the melt spinning, which is a method for producing a crimped yarn according to the present invention, molding is performed at a relatively low temperature of 250 ° C. or lower, and therefore, one having excellent low temperature reactivity is selected. Among the reactive groups, a glycidyl group, an oxazoline group, a carbodiimide group, an acid anhydride group (a group formed from maleic anhydride (sometimes referred to as a maleic anhydride group), etc.) is preferably used, and in particular, a glycidyl group or a carbodiimide. A group is preferably used. If there are two or more reactive groups, the role as a compatibilizing agent can be satisfied. On the other hand, if there are more than 20 reactive groups in one molecule, the viscosity tends to be excessively increased during spinning and the spinnability tends to decrease, so the number of active hydrogen reactive groups in one molecule is two. More than 20 and 20 or less are preferable. More preferably, it is 10 or less, and more preferably 3 or less. Moreover, the kind of reactive group in one molecule may include a plurality. In addition, the compound having two or more active hydrogen reactive groups is preferably a compound having a weight average molecular weight of 250 to 30,000 because of excellent heat resistance and dispersibility during melt molding. More preferably, it is 250-20,000.

  Moreover, as a compound having such a reactive group, a copolymer obtained by graft copolymerizing a side chain having a reactive group on the main chain of the polymer may introduce a large number of functional groups in one molecule. In addition, the thermal properties such as the melting point are generally stable. The polymer to be the main chain to which this reactive group is grafted can be arbitrarily selected, but for ease of synthesis, polyester polymer, polyacrylate, polymethyl methacrylate, poly (alkyl) meta. It can be appropriately selected from the group of acrylate polymers such as acrylate, polystyrene polymers, polyolefin polymers and the like.

  Among the components C that can be used in the present invention, as the compound having a glycidyl group, for example, a polymer having a monomer unit of a compound having a glycidyl group, or a glycidyl group graft-copolymerized to a main chain polymer. And those having a glycidyl group at the end of the polyether unit. Examples of the monomer unit having a glycidyl group described above include glycidyl acrylate and glycidyl methacrylate. In addition to these monomer units, a long-chain alkyl acrylate or the like may be copolymerized to control the reactivity of the glycidyl group. Moreover, the polymer whose monomer unit is a compound having a glycidyl group or the average molecular weight of the polymer as the main chain is in the range of 250 to 30,000, suppresses an increase in melt viscosity when a high concentration is added. This is preferable. The weight average molecular weight is more preferably in the range of 250 to 20,000. In addition, a compound having two or more glycidyl units in the triazine ring is preferable because of high heat resistance. For example, triglycidyl isocyanurate (TGIC), monoallyl diglycidyl isocyanurate (MADGIC) and the like are preferably used.

  The same applies to the oxazoline group, carbodiimide group, aziridine group, imide group, isocyanate group, and maleic anhydride group. Among the above, those having a carbodiimide group are more preferable because of extremely excellent low-temperature reactivity. For example, examples of the carbodiimide compound include diphenylcarbodiimide, di-cyclohexylcarbodiimide, di-2,6-dimethylphenylcarbodiimide, diisopropylcarbodiimide, dioctyldecylcarbodiimide, di-o-toluylcarbodiimide, di-p-toluylcarbodiimide, di- p-nitrophenylcarbodiimide, di-p-aminophenylcarbodiimide, di-p-hydroxyphenylcarbodiimide, di-p-chlorophenylcarbodiimide, di-o-chlorophenylcarbodiimide, di-3,4-dichlorophenylcarbodiimide, di -2,5-dichlorophenylcarbodiimide, p-phenylene-bis-o-toluylcarbodiimide, p-phenylene-bis-dicyclohexylcarbodiimide, p-phene Len-bis-di-p-chlorophenylcarbodiimide, 2,6,2 ', 6'-tetraisopropyldiphenylcarbodiimide, hexamethylene-bis-cyclohexylcarbodiimide, ethylene-bis-diphenylcarbodiimide, ethylene-bis-dicyclohexylcarbodiimide N, N′-di-o-triylcarbodiimide, N, N′-diphenylcarbodiimide, N, N′-dioctyldecylcarbodiimide, N, N′-di-2,6-dimethylphenylcarbodiimide, N-triyl- N′-cyclohexylcarbodiimide, N, N′-di-2,6-diisopropylphenylcarbodiimide, N, N′-di-2,6-di-tert-butylphenylcarbodiimide, N-toluyl-N′-phenylcarbodiimide, N, N'-Di-p- Nitrophenylcarbodiimide, N, N'-di-p-aminophenylcarbodiimide, N, N'-di-p-hydroxyphenylcarbodiimide, N, N'-di-cyclohexylcarbodiimide, N, N'-di-p-toluyl Carbodiimide, N, N′-benzylcarbodiimide, N-octadecyl-N′-phenylcarbodiimide, N-benzyl-N′-phenylcarbodiimide, N-octadecyl-N′-tolylcarbodiimide, N-cyclohexyl-N′-tolylcarbodiimide, N-phenyl-N'-tolylcarbodiimide, N-benzyl-N'-tolylcarbodiimide, N, N'-di-o-ethylphenylcarbodiimide, N, N'-di-p-ethylphenylcarbodiimide, N, N ' -Di-o-isopropylphenylcarbodiimide N, N'-di-p-isopropylphenylcarbodiimide, N, N'-di-o-isobutylphenylcarbodiimide, N, N'-di-p-isobutylphenylcarbodiimide, N, N'-di-2,6- Diethylphenylcarbodiimide, N, N'-di-2-ethyl-6-isopropylphenylcarbodiimide, N, N'-di-2-isobutyl-6-isopropylphenylcarbodiimide, N, N'-di-2,4,6 Mono- or dicarbodiimide compounds such as trimethylphenylcarbodiimide, N, N′-di-2,4,6-triisopropylphenylcarbodiimide, N, N′-di-2,4,6-triisobutylphenylcarbodiimide, poly ( 1,6-hexamethylenecarbodiimide), poly (4,4'-methylenebiscyclohexylca) Rubodiimide), poly (1,3-cyclohexylenecarbodiimide), poly (1,4-cyclohexylenecarbodiimide), poly (4,4'-diphenylmethanecarbodiimide), poly (3,3'-dimethyl-4,4'- Diphenylmethanecarbodiimide), poly (naphthylenecarbodiimide), poly (p-phenylenecarbodiimide), poly (m-phenylenecarbodiimide), poly (tolylcarbodiimide), poly (diisopropylcarbodiimide), poly (methyl-diisopropylphenylenecarbodiimide), poly ( And polycarbodiimides such as triethylphenylenecarbodiimide) and poly (triisopropylphenylenecarbodiimide). Of these, polymers of N, N′-di-2,6-diisopropylphenylcarbodiimide and 2,6,2 ′, 6′-tetraisopropyldiphenylcarbodiimide are preferable.

  Further, the two or more active hydrogen reactive groups may be the same reactive group or different ones, but the same reactive group is preferable in order to control the reactivity.

  As the compound used as Component C, polyalkylene ether glycol is preferable because it specifically improves wear resistance in addition to the compound having the active hydrogen reactive group. Examples of the compound include polyethylene glycol, polypropylene glycol, polybutylene glycol, etc. Among them, polyethylene glycol having a molecular weight of 400 to 20,000 is preferable in terms of heat resistance, dispersibility, and price. More preferred is polyethylene glycol having a molecular weight of 600 to 6,000. Moreover, it is more preferable if both ends of the compound are modified to glycidyl groups. It is also preferred to use in combination with a compound having two or more active hydrogen reactive groups.

  Moreover, since the compound used as Component C is usually melt-molded into a fiber at 200 to 250 ° C. in producing the synthetic fiber of the present invention, high heat resistance that can withstand it is required. Therefore, it is preferable that the thermal weight loss rate at the 200 ° C. arrival point by thermogravimetry (TG) measurement is 3% or less. If the heat loss rate exceeds 3%, the pyrolyzed product bleeds out during spinning and soils the spinneret and spinning device, so that the spinnability deteriorates and the working environment tends to deteriorate due to fuming of pyrolysis gas. There may be a problem in the point. More preferably, the heat loss rate is 2% or less, and further preferably 1% or less. The 200 ° C. heat loss rate is measured by measuring the weight loss rate at 200 ° C. by raising the temperature from normal temperature (10-30 ° C.) to 300 ° C. at a rate of 10 ° C./min. It is what I have sought.

  The amount of component C added is appropriately determined according to the equivalent weight per unit weight of the reactive group of the compound used, the dispersibility and reactivity at the time of melting, the size of the island component domain, and the blend ratio of component A and component B. Can do. In terms of suppressing interfacial peeling, the content is preferably 0.005% by weight or more with respect to the total amount (100% by weight) of Component A, Component B and Component C. More preferably, it is 0.02 weight% or more, More preferably, it is 0.1 weight% or more. If the amount of component C added is too small, the diffusion and reaction amount at the interface between the two components is small, and the effect of improving the interfacial adhesion may be limited. On the other hand, the amount of component C added is preferably 5% by weight or less in order for component C to exhibit performance without impairing the properties of component A and component B, which are the base material of the fiber, and the spinning performance. % Or less is more preferable. More preferably, it is 1 weight% or less.

  As described above, by adding Component C, the terminal carboxyl group of the aliphatic polyester can be blocked, and the hydrolysis resistance of the aliphatic polyester can be improved. The concentration of the terminal carboxyl group having an autocatalytic action should be low, and the total carboxyl end group concentration in the aliphatic polyester is preferably 15 equivalents / ton or less, more preferably 10 equivalents / ton or less, and still more preferably 0 to 7 equivalents / ton.

  Furthermore, for the purpose of promoting the reaction of the compound having a reactive group, it is preferable to add a metal salt of a carboxylic acid, particularly a catalyst in which the metal is an alkali metal or an alkaline earth metal because the reaction efficiency can be increased. Among these, it is preferable to use a catalyst based on lactic acid such as sodium lactate, calcium lactate and magnesium lactate. In addition, a catalyst having a relatively large molecular weight such as a metal stearate can be used alone or in combination for the purpose of preventing the heat resistance of the resin from being lowered due to the addition of the catalyst. The added amount of the catalyst is preferably 5 to 2000 ppm with respect to the synthetic fiber in order to control dispersibility and reactivity. More preferably, it is 10-1000 ppm, More preferably, it is 20-500 ppm.

  The crimped yarn of the present invention preferably contains at least one crystal nucleating agent selected from talc, sorbitol derivatives, phosphate metal salts, basic inorganic aluminum compounds, and melamine compound salts. The crystal nucleating agent is a crystal nucleating agent having high effectiveness mainly for the aliphatic polyester resin (A), particularly polylactic acid. By adding the crystal nucleating agent, it is possible to obtain a crimped yarn excellent in fastness that is difficult to crimp.

  As the talc used as the crystal nucleating agent, talc having an average particle diameter D50 of talc of 5 μm or less and a particle diameter of 10 μm or more is based on the total amount of talc, while maintaining high mechanical properties of the fiber and exhibiting high crystallization characteristics. It is preferable that it is 0 to 4.5 volume% or less. By making the average particle diameter D50 of talc 5 μm or less, the effect as a crystal nucleating agent is dramatically improved by increasing the specific surface area. Therefore, the particle diameter of talc is preferably 4 μm or less, and more preferably 3 μm or less. Most preferably, it is 1.5 μm or less. The lower limit of the average particle diameter D50 of talc is not particularly limited, but it is preferably 0.2 μm or more because the agglomeration becomes higher and the dispersibility in the polymer becomes worse as the particle diameter becomes smaller. . Moreover, it is preferable that the talc with a particle diameter of 10 micrometers or more is 4.5 volume% or less with respect to the total amount of talc. When coarse talc is contained, not only the spinnability is lowered but also the mechanical properties of the fiber tend to be lowered. Therefore, the content of talc having a particle diameter of more than 10 μm is more preferably 0 to 3% by volume, further preferably 0 to 2% by volume, and most preferably 0% by volume with respect to the total amount of talc.

  In addition, the particle diameter of the talc as described in said (1) and (2) term is the value calculated | required from the particle size distribution measured by the laser diffraction method using Shimadzu Corporation SALD-2000J.

  Examples of the sorbitol derivative preferably used for the crystal nucleating agent include bisbenzylidene sorbitol, bis (p-methylbenzylidene) sorbitol, bis (p-ethylbenzylidene) sorbitol, bis (p-chlorobenzylidene) sorbitol, and bis (p-bromo). Benzylidene) sorbitol and sorbitol derivatives obtained by chemically modifying the sorbitol derivatives.

  Moreover, as a phosphoric acid ester metal salt and a basic inorganic aluminum compound, the compounds described in JP-A-2003-192883 are preferably used.

  As the melamine compound, melamine, a substituted melamine compound in which the amino group hydrogen of melamine is substituted with an alkyl group, an alkenyl group or a phenyl group (Japanese Patent Laid-Open No. 9-143238), the hydrogen of the amino group of melamine is a hydroxyalkyl group , Substituted melamine compounds substituted with hydroxyalkyl (oxaalkyl) n group and aminoalkyl group (Japanese Patent Laid-Open No. 5-202157), deammonium condensation products of melamine such as melam, melem, melon, methone, benzoguanamine, acetoguanamine, etc. Guanamines can be used. Moreover, organic acid salt and inorganic acid salt are mentioned as a melamine compound salt. Examples of organic acid salts include carboxylates such as isocyanurate, formic acid, acetic acid, oxalic acid, malonic acid, lactic acid and citric acid, and aromatic carboxylates such as benzoic acid, isophthalic acid and terephthalic acid. These organic acid salts may be used alone or in combination of two or more. Of these organic acid salts, melamine cyanurate is most preferred. Melamine cyanurate is surface-treated with a metal oxide sol such as silica, alumina or antimony oxide (Japanese Patent Laid-Open No. 7-224049), or surface-treated with polyvinyl alcohol or cellulose ethers (Japanese Patent Laid-Open No. 5-310716). JP, 6-157820, A) which surface-treated with nonionic surfactant of HLB1-8. The molar ratio of the melamine compound and the organic acid is not particularly limited, but it is preferable that the salt compound does not contain a free melamine compound or an organic acid that does not form a salt. The method for producing the organic acid salt of the melamine compound is not particularly limited, but in general, it can be obtained as a crystalline powder by mixing and reacting the melamine compound and the organic acid in water and then filtering or distilling the water and drying. it can. Inorganic acid salts include hydrochlorides, nitrates, sulfates, pyrosulfates, alkyl sulfonates such as methanesulfonic acid and ethanesulfonic acid, alkylbenzene sulfonates such as paratoluenesulfonic acid and dodecylbenzenesulfonic acid, and sulfamic acid. Salts, phosphates, pyrophosphates, polyphosphates, phosphonates, phenylphosphonates, alkylphosphonates, phosphites, borates, tungstates and the like. Among these inorganic acid salts, melamine polyphosphate, melamine polyphosphate / melam / melem double salt, and paratoluenesulfonate are preferable. The molar ratio of the melamine compound and the inorganic acid is not particularly limited, but it is preferable that the salt compound does not contain a free melamine compound or an inorganic acid that does not form a salt. The method for producing the inorganic acid salt of the melamine compound is not particularly limited, but generally it can be obtained as a crystalline powder by mixing and reacting the melamine compound and the inorganic acid in water and then filtering or distilling the water and drying. it can. Further, methods for producing pyrophosphate and polyphosphate are described in, for example, US Pat. No. 3,920,796, JP-A-10-81691, JP-A-10-306081, and the like.

  Since the addition amount of the crystal nucleating agent has an inverse correlation with the mechanical properties of the fiber, the addition amount is preferably 0.01 to 2% by weight with respect to the aliphatic polyester (A). If the added amount is 0.01% by weight or more, the aliphatic polyester quickly crystallizes in the cooling step after coming out of the air jet stuffer device, so that the crimped yarn has excellent crimp fastness. Can do. Moreover, it can be set as the crimped yarn excellent in the crimp fastness, suppressing the fall of a mechanical characteristic by making addition amount into 2 weight% or less. The amount of the crystal nucleating agent added is more preferably 0.05 to 1.5% by weight, still more preferably 0.2 to 1% by weight.

  Moreover, it is preferable to add Cu salt, K salt, Mn salt, Cr salt, tannin, etc. to the crimped yarn of the present invention in order to increase light fastness. In particular, CuI and KI are effective in improving the light resistance of the polyamide resin. One or more compounds may be used in combination. The addition amount may be 0.001 to 0.5% by weight with respect to the thermoplastic polyamide resin (B), more preferably 0.005 to 0.2% by weight, and still more preferably 0.01 to 0.1%. % By weight.

Further, the fiber surface of the crimped yarn of the present invention, streak-like grooves extending in the fiber axis direction that is formed. The streak-like groove is a concave groove existing on the fiber surface as shown in FIG. 2, and extends substantially parallel to the fiber axis direction (an angle within 10 ° with respect to the fiber axis). Due to the streak-like grooves, the light incident on the fiber surface can be appropriately scattered and absorbed to give a moist and glossy gloss. Width of the striations, the scattering Ri effectively 0.01~1μm der to produce the, more preferably 0.05～0.9Myuemu, more preferably 0.08～0.8Myuemu. Further, when the aspect ratio of the streak groove (long axis length of streak groove / width of streak groove) is in a range of about 10 to 500, a good gloss feeling is given without impairing wear resistance. . The streak groove can be captured by observation with an electron microscope (SEM). In the SEM image, the width of the streak groove is usually 5,000 times, and if necessary, the maximum value of the streak groove width is taken as the width of the streak groove from the photograph enlarged to 1,000 to 10,000 times. The width of ten streak grooves is measured and the average value is defined as the width of the streak grooves of the present invention. Further, with respect to the ten streak grooves, both ends of the streak grooves are connected with straight lines, the straight line distance is defined as the long axis length of the streak grooves, and the aspect ratio is obtained for each of the streak grooves (see FIG. 3). . Furthermore, the number of the streak-like grooves is preferably in the range of 1 to 50 in the range of 10 μm × 10 μm in the SEM image, since it exhibits good gloss without impairing wear resistance. More preferably, it is 3-40, More preferably, it is 5-30.

  The crimped yarn of the present invention preferably has a strength of 1 cN / dtex or more, more preferably 1.5 cN / dtex or more in order to keep the process passability and the mechanical strength of the product high. More preferably, it is 2 cN / dtex or more, and particularly preferably 3 cN / dtex or more. An air stuffer crimped yarn having such strength can be produced by a melt spinning / drawing / bulky method described later. Moreover, it is preferable that the elongation at break is 15 to 70% because the process passability is good when it is made into a textile product. More preferably, it is 20-65%, More preferably, it is 30-55%. A crimped yarn having such a degree of elongation can be produced by a melt spinning / drawing / bulky method described later. At this time, it may be preferable to set the strength to 4 cN / dtex or less from the viewpoint of obtaining a high-performance crimped yarn having a breaking elongation in the above range.

  Further, if the boiling water shrinkage of the crimped yarn is 0 to 15%, the dimensional stability of the fiber and the fiber product is good, which is preferable. More preferably, it is 0-12%, More preferably, it is 0-8%, Most preferably, it is 0-3.5%.

  In addition, the polymer alloy fiber of conventional aliphatic polyester and polyamide causes a bulge having a diameter of 1.5 to 10 times the diameter of the discharge hole, which is called the ballast effect, immediately below the discharge hole during melt spinning due to the interfacial tension between the polymers. To do. For this reason, thinning is likely to occur in the thinning deformation process during spinning, and yarn breakage may occur, and quality problems such as yarn unevenness may occur. As will be described later, the fiber of the present invention minimizes the ballast effect by polymer type, optimum design of melt viscosity, control of die discharge linear velocity, optimization of cooling conditions directly under the die, and control of spinning speed. At the same time, even if bulging occurs due to the ballast, the stretched flow region is as close as possible to the die surface, and the fibers can be stably formed by swiftly (shortening the distance from discharge until the thinning deformation is completed). Succeeded in doing. Therefore, the yarn unevenness in the longitudinal direction of the yarn is also small. In the crimped yarn of the present invention, the yarn spot (Woster spot, U%, Normal value) is preferably 2% or less, and more preferably 1.5% or less, in order to suppress process passability and dyed spots after dyeing. More preferably, it is 1% or less.

  The crimped yarn of the present invention is an “air stuffer crimped yarn” obtained using an air jet stuffer device described later. The air stuffer crimped yarn has an irregular entangled loop-shaped crimped shape using a turbulent flow effect of a heating fluid (dry air, etc.). The form is described in detail in Chapter 1 (pages 25-39) of "Processing Technology Manual (Volume 2)".

  In the crimped yarn of the present invention, the crimp elongation after the boiling water treatment is preferably 3 to 30%, more preferably 5 to 30%, still more preferably 8 to 30%, and particularly preferably 12 to 30. %. Here, the crimp elongation rate after the boiling water treatment is measured as follows.

A crimped yarn unwound from a package (crimped yarn winding drum or bobbin) left in an atmosphere of an ambient temperature of 25 ± 5 ° C. and a relative humidity of 60 ± 10% for 20 hours or more is boiled for 30 minutes under no load. Immerse with. After the treatment, it is air-dried for 1 day and night (about 24 hours) in the above environment, and this is used as a sample of crimped yarn after the boiling water treatment. An initial load of 1.8 mg / dtex is applied to this sample, and after 30 seconds, marking is performed on a sample length of 50 cm (L1). Next, the sample length (L2) is measured after 30 seconds have elapsed by applying a measurement load of 90 mg / dtex instead of the initial load. And the crimp expansion | extension rate (%) after a boiling water process is calculated | required by the following Formula.
Crimp elongation (%) = [(L2-L1) / L1] × 100.

  If the crimp elongation after boiling water treatment of such a crimped yarn is lower than 3%, the expression of crimp is not sufficient, the bulky property is poor, and, for example, when it is made into a carpet or the like, there is no volume feeling. Sometimes. On the other hand, it is difficult to produce a crimped yarn having a crimped elongation rate of greater than 30% after the boiling water treatment. If the crimped elongation rate is increased beyond 30%, the strength of the crimped yarn is reduced. It may decrease significantly, or may cause crimped spots, thread thickness spots, and the like.

  The crimped yarn of the present invention is difficult to crimp in a processing step for forming a fabric structure such as dyeing or bulky processing, or in a long-term use after making the product, and the appearance of the product is long-lasting. It is preferred that it be retained. For this reason, it is preferable that the crimp elongation rate after boiling water treatment under a 2 mg / dtex load (hereinafter referred to as “elongation rate under constraint load”), which is an index of fastness of crimp, is 2% or more. . The elongation rate under restraint load is more preferably 3% or more, and further preferably 5% or more. The upper limit is not particularly limited, but in the technique of the present invention, the upper limit is about 15%. In addition, the elongation rate under restraint load can be measured by the method described in Examples.

  The cross-sectional shape of the single fiber constituting the crimped yarn of the present invention can be freely selected from a round cross-section, a hollow cross-section, a porous hollow cross-section, a multi-leaf cross-section such as a trilobal cross-section, a flat cross-section, a W cross-section, an X cross-section However, in order to increase the bulkiness of the crimped yarn and make it a voluminous fiber structure, the profile should have an irregular section (D1 / D2) of 1.2-7. Is preferred. The higher the irregularity of the irregular cross-section yarn, the more the fiber structure can be made with a sense of volume. On the other hand, if the irregularity is excessively high, the bending rigidity of the fiber increases, the flexibility decreases, and the fiber cracks. There may be problems such as the occurrence of (fibrillation) and a lustrous gloss. Therefore, the degree of deformity is more preferably in the range of 1.3 to 5.5, and further preferably in the range of 1.5 to 3.5.

  The form of the crimped yarn of the present invention may be a long fiber, or the obtained crimped yarn may be cut into an appropriate length and treated as a short fiber.

  Moreover, when using the crimped yarn of this invention as a fiber structure, it can apply to a textile fabric, a knitted fabric, a nonwoven fabric, a pile, cotton, etc., and may contain the other fiber. For example, it may be natural fiber, recycled fiber, semi-synthetic fiber, alignment with synthetic fiber, twisted yarn, mixed fiber. Other fibers include natural fibers such as cotton, hemp, wool, and silk, regenerated fibers such as rayon and cupra, semi-synthetic fibers such as acetate, nylon, polyester (polyethylene terephthalate, polybutylene terephthalate, etc.), polyacrylonitrile In addition, synthetic fibers such as polyvinyl chloride are applicable.

  In addition, the use of the fiber structure using the crimped yarn of the present invention includes clothing that requires wear resistance, for example, sports such as outdoor wear, golf wear, athletic wear, ski wear, snowboard wear, and pants thereof. There are women's and men's outerwear such as clothing, casual clothing such as blousons, coats, winter clothes and rainwear. In addition, applications that require excellent durability and moisture aging characteristics over a long period of use include uniforms, comforters and mattresses, skin comforters, kotatsu comforters, cushions, baby comforters, blankets, etc., pillows, cushions, etc. There are uses for bedding materials such as side covers and covers, mattresses and bed pads, hospital sheets, medical sheets, hotel sheets and baby sheets, as well as covers for sleeping bags, cradle and strollers, etc. be able to. Moreover, it can be used suitably for interior materials for automobiles, and among them, it is optimal to use for automobile carpets that require high wear resistance and moisture aging characteristics. In addition, it is not limited to these uses, For example, you may use for the grassproof sheet for agriculture, the waterproof sheet for building materials, etc.

  The production method of the crimped yarn of the present invention is not particularly limited, but for example, the following method can be adopted using a direct spinning / drawing / crimping apparatus shown in FIG.

That is, in the combination of the above-described aliphatic polyester resin (component A) and thermoplastic polyamide resin (component B), the blend ratio (% by weight) of component A and component B is in the range of 5/95 to 55/45. At the same time, the melt viscosity ratio (ηb / ηa) is preferably in the range of 0.1 to 2. At this time, when the blend ratio of component A is close to the lower limit of the blend range, for example, when the ratio of component A is 5 to 15% by weight, the ratio of melt viscosity may be increased to 0.8 to 2, but component A When the blend ratio is close to the upper limit, for example, when the component A ratio is 45 to 55% by weight, the melt viscosity ratio is 0.1 to 0.3, that is, the melt viscosity of the thermoplastic polyamide resin (component B) is It is necessary to reduce the aliphatic polyester resin (component A) to 1/10 to 3/10. This is because the crimped yarn formed of the polymer alloy fiber of the present invention has a sea-island structure yarn in which the aliphatic polyester resin (A) forms an island component. In addition, if the component A ratio is in the range of 15 to 45% by weight in the above range, the aliphatic polyester can be made into an island component by setting the melt viscosity ratio in the range of 0.2 to 1. . As the melt viscosity η for calculating the above-described melt viscosity ratio (ηb / ηa), a value measured at a shear rate of 1216 sec ⁻¹ at the same temperature as the spinning temperature is used.

  Next, using a combination of the above polymer characteristics and blend ratio, pelletization is performed once using a biaxial kneader or the like, or melt spinning is performed continuously with the kneading to fiberize the polymer alloy. The addition timing of the compatibilizing agent (component C) may be added in accordance with the kneading of the component A and the component B. The adding method is to simultaneously supply the compatibilizing agent to the kneader and simultaneously knead together with the components A and B. Alternatively, master pellets containing component C at a high concentration may be prepared in advance, mixed with the pellets of component A and component B, and supplied to the biaxial kneader. In addition, when master pelletizing is performed in advance, it is important to suppress the reaction of the compatibilizing agent as much as possible. Therefore, it is preferable that the pellet is prepared with the component A that can lower the molding temperature. The reason for suppressing the reaction of the compatibilizer as much as possible is to prevent the reactive group from reacting to one component as much as possible when the compatibilizer is a reaction system.

The jacket temperature during kneading in melt extrusion is preferably Tmb + 3 ° C. to Tmb + 30 ° C. based on the melting point of the thermoplastic polyamide (component B) (hereinafter referred to as Tmb), and the shear rate is preferably 300 to 9800 sec ^−1. . By setting the jacket temperature and the shear rate in this range, the domain diameter of the present invention can be achieved when the fiber is used, and the polymer alloy fiber is not colored. If the jacket temperature exceeds this range, or if the shear rate exceeds 10,000 sec ⁻¹ and shear heat generation occurs, the use of the obtained crimped yarn may be limited due to the coloring of the polymer.

  Similarly, in order to prevent the above-described sea-island structure from being broken and to prevent coloring, the spinning temperature is preferably as low as possible, and is preferably set to Tmb + 3 ° C. to Tmb + 40 ° C. The spinning temperature is more preferably Tmb + 3 ° C. to Tmb + 30 ° C., further preferably Tmb + 3 ° C. to Tmb + 20 ° C.

  Also, in order to control the domain diameter by suppressing the reaggregation of island domains in the spinning pack, a high mesh filter layer (# 100 to # 200), a porous metal, a non-woven filter with a small filter diameter (filter diameter 5) ˜30 μm), an in-pack blend mixer (static mixer or high mixer) may be incorporated.

  Furthermore, the polymer blend of aliphatic polyester and polyamide is incompatible, and the melt shows a strong behavior with an elastic term, and the swelling due to the ballast effect tends to increase. Therefore, the discharge linear velocity at the die discharge hole is set to 0.02 to 0.4 m / second in order to suppress the swelling of the yarn due to the ballast effect and to improve the spinning tone by stably stretching and thinning. It is preferably 0.03 to 0.3 m / sec, more preferably 0.04 to 0.2 m / sec. Increasing the depth of the discharge hole is also effective in suppressing ballast. Here, the discharge hole depth refers to the length from the lower end of the introduction hole to the discharge surface as shown in FIG. Further, the depth of the discharge hole in the case of a round hole indicates the length from the lower end of the throttle portion to the discharge surface as shown in FIG. The depth of the discharge hole is preferably 0.3 to 5 mm, more preferably 0.4 to 5 mm, and further preferably 0.5 to 5 mm.

  Further, it is necessary for the discharge yarn to make the extension flow region as close as possible to the base surface and promptly (shorten the distance from the discharge until the thinning deformation is completed). For this reason, the cooling start point of the discharged yarn is preferably closer to the base surface, and it is preferable to start cooling from a position substantially 0.01 to 0.15 m vertically below the base surface. As shown in FIG. 6 in which the spinning section is enlarged, the cooling start point substantially vertically below is a line a drawn horizontally from the upper end of the cooling air blowing surface and a perpendicular line b drawn downward from the base surface. , Means an intersection c between the line a and the line b, and means that the distance cd from the base surface d to the c on the perpendicular b is preferably 0.01 to 0.15 m. The cooling start point is more preferably 0.01 to 0.12 m substantially vertically downward from the die surface, and further preferably 0.01 to 0.08 m substantially vertically downward from the die surface.

  The cooling method may be a uniflow type chimney that cools from one direction, or an annular chimney that applies cooling air from the inside to the outside of the yarn or from the outside to the inside of the yarn, but preferably the inside of the yarn. An annular chimney that is cooled from the outside to the outside is preferable in that it can be uniformly and rapidly cooled. At this time, it is desirable to cool the multifilament by applying a gas from a direction substantially perpendicular to the multifilament. Here, the substantially orthogonal direction means that the stream line of the cooling air is substantially perpendicular to the line b (inclination 70 to 110 °) as shown in FIG. There are no particular restrictions on the gas used for the cooling air, but rare gases such as argon and helium, nitrogen, or air that are stable at room temperature (very low reactivity), nitrogen, or air are preferably used. Nitrogen that can be used or air is particularly preferably used.

  Further, the speed of the cooling air at this time is preferably 0.3 to 1 m / sec, and more preferably 0.4 to 0.8 m / sec. Further, the temperature of the cooling air is preferably lower in order to rapidly cool the yarn, but it is realistic and preferable to be 15 to 25 ° C. in consideration of the cost of air conditioning. As described above, the sea-island structure of the present invention is formed by a specific polymer combination, and can be discharged without breaking the sea-island structure by controlling the spinning temperature, and further control of the discharge linear velocity at the die discharge hole, By controlling the cooling method and its conditions, the polymer alloy fiber of the present invention can be stably spun and taken out only for the first time. The spun multifilament is coated with a known spinning finish, and the amount of adhesion at this time is 0.3 to 3% by weight (oil agent component: water or low-viscosity mineral oil) = 10: 90, the emulsion is attached to the yarn 3-30% by weight).

  Further, the spinning speed is 500 to 5000 m / min, and the film is wound once or continuously stretched and bulked. However, if the polymer alloy fiber of the present invention is left in an unstretched state, orientation relaxation tends to occur, and if there is a time difference between stretching and bulking between unstretched packages, the fiber's strong elongation characteristics and heat shrinkage can be easily achieved. Variations in characteristics and crimp elongation occur. Therefore, it is preferable to employ a direct spinning stretch bulk processing method that performs spinning, stretching, and bulk processing in one step.

  Stretching may be performed in one, two, or three stages, but when high strength of 2 cN / dtex or more is required, stretching is preferably performed in two or more stages. FIG. 4 is a schematic view of an apparatus that continuously performs two-stage drawing / crimping after spinning. In this case, 1FR is taken up at 500 to 5000 m / min, and 1FR is set at about 50 to 100 ° C. at the same time. The first stage of stretching is performed between 1FR (single hot roll) to 1DR (tandem roll), and then the second stage of stretching is performed between 1DR and 2DR (tandem roll). At this time, it is important to improve the process stability that the stretching temperature (1DR temperature in FIG. 4) when performing the second stage stretching is at least 20 ° C. higher than 1FR. Therefore, when the 1FR temperature is 50 to 100 ° C, the 1DR temperature may be set in the range of 70 to 130 ° C and 1FR temperature + 20 ° C or higher. Further, the ratio between 1FR and the final drawn roll after drawing (2DR in the case of FIG. 4) may be adjusted so that the breaking elongation of the drawn yarn sampled at the final drawn roll outlet is 15 to 65%. Preferably it is 20 to 60%. Here, as means for bringing the breaking elongation into the above range, the amount of the polymer discharged, the spinning speed, the draw ratio between the rolls, and the breaking elongation of the drawn yarn sampled at the outlet of the final drawing roll are preliminarily determined. When the relationship is recorded in a PLC (programmable controller), the draw ratio is automatically adjusted, or the drawn yarn is sampled at the final draw roll outlet, and the sampled drawn yarn break elongation is lower than the above range. When the draw ratio is set low and the elongation at break is high, a method of adjusting the break elongation by setting the draw ratio high so that the break elongation of the drawn yarn is in the range of 15 to 65%. For example, the stretching ratio may be determined by adjustment.

  By setting the above drawing temperature and draw ratio, it is possible to obtain a drawn yarn having high process stability, high strength, and small yarn unevenness (Uster unevenness U%). Furthermore, by setting the final drawing roll temperature as Tma-30 ° C. to Tma + 30 ° C. based on the melting point of the aliphatic polyester resin (component A) (hereinafter referred to as Tma), a drawn yarn having a desired heat shrinkage rate is obtained. can do. Further, by performing heat setting at such a high temperature and performing high-temperature bulking in the next step, it becomes possible to form fine streak-like grooves on the fiber surface of the crimped yarn. As a result, the product can be given a moist and highly aesthetic gloss. For bulky processing, an air jet stuffer device is used, and crimping is performed at a nozzle temperature of the device that is 5 to 100 ° C. higher than the final stretching roll temperature.

  The air jet stuffer device is described in detail in Chapter 1 (pages 25-39) of “Filament Processing Technology Manual (Volume 2)” edited by the Japan Textile Machinery Society. In other words, it is a crimping apparatus that is used for the production of crimped yarns for BCF carpets, and it imparts irregularly entangled loop-like bulkiness to the filament using the turbulent flow effect of the air jet. is there. Examples of the apparatus are described in FIGS. 1-16 to 30 of the above-mentioned filament processing technical manual. Examples of the apparatus are described in terms of the fineness of the multifilament, the fineness and deformity of the single filament, and the rigidity of the yarn. What is necessary is just to select suitably collectively.

  Here, when it is desired to lower the crimp elongation rate after the boiling water treatment, the nozzle temperature may be lowered, and when it is desired to increase the crimp elongation rate, the nozzle temperature may be increased. However, if the nozzle temperature is set higher than Tmb, the process passability deteriorates rapidly, so the upper limit of the nozzle temperature is Tmb + 10 ° C. The heating fluid introduced into the nozzle is not particularly limited, such as dry air, dry nitrogen, or air containing steam, but it is preferable to use heated air containing steam from the viewpoint of thermal efficiency and running cost.

  The yarn to which the three-dimensional crimp has been applied through the air jet stuffer device is subsequently applied to the cooling drum and rapidly cooled to fix the crimped structure. Thereafter, an appropriate tension is applied to the crimped yarn to improve the uniformity of the crimp, and the wound yarn is wound at a speed 10% to 30% lower than the peripheral speed of the final drawing roll to obtain a package. At this time, the relaxation rate between the final drawing roll (2DR in FIG. 1) and the winding machine is such that the winding tension is in the range of 0.05 to 0.12 cN / dtex so that excessive tension is not applied to the crimped yarn. The one with a high crimp elongation rate is wound at a relaxation rate of 20-30%, and the one with a low crimp elongation rate is wound at a relaxation rate of 10-20%.

  Hereinafter, the present invention will be described in detail with reference to examples. In addition, the measuring method in an Example used the following method.

A. Weight average molecular weight of aliphatic polyester Tetrahydrofuran was mixed with a chloroform solution of a sample (aliphatic polyester polymer) to obtain a measurement solution. This was measured by gel permeation chromatography (GPC), and the weight average molecular weight was determined in terms of polystyrene. When measuring the weight average molecular weight of the aliphatic polyester in the fiber, the sample was dissolved in chloroform, the polyamide residue was removed by filtration, the chloroform solution was dried and the aliphatic polyester was taken out and measured. .

B. Residual lactide amount of polylactic acid 1 g of a sample (polylactic acid polymer) was dissolved in 20 ml of dichloromethane, and 5 ml of acetone was added to this solution. Furthermore, it was made to deposit with cyclohexane, it was made to precipitate, it analyzed by the liquid chromatograph using Shimadzu GC17A, and the amount of lactide was calculated | required with the absolute calibration curve. In the case of polylactic acid in the fiber, the blend ratio of polylactic acid and polyamide was obtained in advance from a TEM image, which will be described later, and the lactide amount was corrected by the blend ratio.

C. Carboxyl group end concentration A precisely weighed sample (aliphatic polyester polymer extracted by the following method) was dissolved in o-cresol (water 5%), and an appropriate amount of dichloromethane was added to this solution, followed by 0.02N KOH methanol solution. Determined by titration with At this time, an oligomer such as lactide, which is a cyclic dimer of lactic acid, is hydrolyzed to generate a carboxyl group terminal, so that all of the carboxyl group terminal of the polymer, the monomer-derived carboxyl group terminal, and the oligomer-derived carboxyl group terminal are totaled. The carboxyl group terminal concentration was determined. The method for extracting the aliphatic polyester from the polymer alloy fiber (synthetic fiber) is not particularly limited, but in the present invention, the aliphatic polyester is dissolved and filtered using chloroform to remove the polyamide, and the filtrate is dried. Extracted.

D. Relative Viscosity and Intrinsic Viscosity of Thermoplastic Polyamide The relative viscosity of nylon 6 was measured at 25 ° C. by preparing a 98% sulfuric acid solution of 0.01 g / mL. The intrinsic viscosity of nylon 11 was measured at 20 ° C. after preparing a 0.5% by weight metacresol solution.

E. Polymer melting point and crystal melting calorie A temperature giving an extreme value of a melting endothermic curve obtained by measuring 20 mg of a sample at a heating rate of 10 ° C./min using a differential scanning calorimeter DSC-7 manufactured by Perkin Elmer. The melting point (° C.) was used. Further, from the area surrounded by the peak forming the extreme value and the base line (crystal melting peak area), the heat of crystal melting ΔH (J / g) of the polymer was determined.

F. Melt viscosity η
Using Capillograph 1B manufactured by Toyo Seiki Co., Ltd., the measurement temperature was set to the same as the spinning temperature in a nitrogen atmosphere, and the melt viscosity of each of the aliphatic polyester resin and the thermoplastic polyamide resin was measured at a shear rate of 1216 sec ⁻¹ . . The measurement was performed 3 times and the average value was taken as the melt viscosity.

G. Size and blend ratio of island domains of crimped yarn Pull out one single fiber constituting the crimped yarn, cut out an ultrathin section in the direction perpendicular to the fiber axis (fiber cross-sectional direction), and remove the polyamide component of the section The metal was stained with tungstic acid, and the blend state was observed and photographed with a 40,000 times transmission electron microscope (TEM). Using the image analysis software “WinROOF” of Mitani Shoji Co., Ltd. for this photographed image, assuming that the domain is a circle as the size of the island domain (non-stained part), the diameter (diameter converted) (2r) converted from the domain area ) As the domain size. The number of domains to be measured was 100 per sample, and the distribution was obtained for 80 domain diameters excluding 10 values with the largest domain diameter and 10 values with the smallest domain diameter.

The blend ratio of component A and component B in the fiber was obtained as a weight ratio by correcting the cross-sectional area ratio obtained from the TEM image (5.93 × 4.65 μm) with the specific gravity of each component. Here, the specific gravity of each component in this example is polylactic acid: 1.24, nylon 6: 1.14, nylon 11: 1.04, nylon 610: 1.08, nylon 6/66 copolymer: 1.14 was used.
TEM apparatus: Hitachi H-7100FA type condition: accelerating voltage 100 kV.

H. Surface morphology of crimped yarn One single fiber constituting the crimped yarn was extracted, and the surface state of the fiber was observed and photographed with an electron microscope ESEM-2700 manufactured by Nikon Instech Co., Ltd. at a magnification of 5,000 times. Using the image analysis software “WinROOF” of Mitani Shoji Co., Ltd., this photographed image was measured for the width (maximum width) of any 10 streak grooves, and the average value was taken as the width of the streak grooves. Further, the length of each streak groove was measured, and the aspect ratio (length of streak groove / width of streak groove) was determined. The number of streak-like grooves was counted by counting the number existing in an arbitrary 10 μm × 10 μm on the fiber surface.

I. Heat loss rate of compatibilizer Using an EXSTAR6000 series TG / DTA6200 manufactured by SII, about 10 mg of a sample (component C) was weighed, and a heat loss curve of 200 ± 0.5 measured at a heating rate of 10 ° C./min. The weight loss rate at the ° C point was determined.

J. et al. Fineness A 100 m crimped yarn was measured in a skein shape with a measuring scale, the weight of the crimped yarn having a length of 100 m was measured, and the weight was multiplied by 100 to obtain the fineness (dtex). The measurement was performed three times, and the average value was defined as the fineness (dtex).

K. Strength and Elongation A sample (crimped yarn) was measured with a Tensilon UCT-100 manufactured by Orientec Co., Ltd. under the constant speed elongation conditions shown in JIS L1013 (Test method for chemical fiber filament yarn, 1998). The holding interval (sample length) was 200 mm. The elongation at break was determined from the elongation at the point showing the maximum strength in the SS curve.

L. Boiling water shrinkage (boiling yield)
A sample (crimped yarn) was immersed in boiling water for 15 minutes, and was determined from the dimensional change before and after immersion according to the following equation.
Boiling water shrinkage (%) = [(L0−L1) / L0] × 100
L0: A skein length measured by scraping a sample and measuring it under an initial load of 0.088 cN / dtex.
L1: A skein length measured under an initial load of 0.088 cN / dtex after treating the skein whose L0 was measured with boiling water in an unloaded state and air-drying.

M.M. Yarn spots U%
A sample (crimped yarn) was measured using a UT4-CX / M manufactured by Zellweger Uster, with a yarn speed of 200 m / min and a measurement time of 1 minute.

N. Crimp elongation after boiling water treatment A crimped yarn that has been unwound from a package (crimped yarn winding drum or bobbin) that has been left in an atmosphere having an ambient temperature of 25 ± 5 ° C and a relative humidity of 60 ± 10% for 20 hours or more. Then, immersing with boiling water for 30 minutes under no load. After the treatment, it is air-dried for 1 day and night (about 24 hours) in the above environment, and this is used as a sample of crimped yarn after the boiling water treatment. An initial load of 1.8 mg / dtex is applied to this sample, and after 30 seconds, marking is performed on a sample length of 50 cm (L1). Next, the sample length (L2) is measured after 30 seconds have elapsed by applying a measurement load of 90 mg / dtex instead of the initial load. And the crimp expansion | extension rate (%) after a boiling water process is calculated | required by the following Formula.
Crimp elongation (%) = [(L2-L1) / L1] × 100.

O. Crimp elongation after treatment with boiling water under restraint load (stretch rate under restraint load)
When treating with boiling water, the crimp elongation rate was determined in the same manner as for M, except that the crimped yarn was treated with a load of 2 mg / dtex suspended, and the value was defined as the elongation rate under constraint load. .

P. Deformation degree A cross section of the sample (crimped yarn) was cut out and obtained from the following equation from the diameter D1 of the circumscribed circle of the single fiber cross section and the diameter D2 of the inscribed circle of the single fiber cross section.
Deformity = D1 / D2.

Q. Abrasion resistance of crimped yarn Using a Twain abrasion tester manufactured by Ando Iron Works, No. P600 sandpaper was wound around a roller, and the roller was rotated under the following conditions to measure the number of rotations of the roller until the yarn was cut.
Rotating body diameter: 40mm
Yarn contact length: 110 mm
Roller rotation speed: 200rpm
Measurement load: 0.4 cN / dtex

R. The average particle diameter D50 of the crystal nucleating agent and the content of the crystal nucleating agent of 10 μm or more The average particle diameter D50 (μm) of the crystal nucleating agent was measured by a laser diffraction method using SALD-2000J manufactured by Shimadzu Corporation. Moreover, the volume% of the crystal nucleating agent of 10 μm or more was determined from the obtained particle size distribution.

S. Abrasion resistance of carpet (wear loss rate)
After twisting the crimped yarn with two S twists and Z twists, and twisting the twisted yarn into a PP spunbonded nonwoven fabric as the front yarn, a backing material is applied to the back of the base fabric and dried. A tufting carpet was obtained (weighing 1200 g / m ² ).

The tufting carpet was cut into a circular shape having a diameter of 120 mm, and a 6 mm hole was formed in the center to obtain a test piece. After measuring the weight W0 of the test piece, the test piece was attached to a Taber abrasion tester (Rotary Abster) defined in ASTM D 1175 (1994) with the surface facing up, H # 18 abrasion rod, compression load 1 kgf (9.8 N) ), A wear test with a sample holder rotation speed of 70 rpm and a wear count of 5500 was performed, and the sample weight W1 after the wear test was measured. The wear weight loss rate was calculated using these measured values and the following equation.
Wear loss rate (%) = (W0−W1) × 100 / (W2 × A1 / A0)
W0: Weight of circular carpet before measurement (g)
W1: Weight of the circular carpet after measurement (g)
W2: Carpet weight (g / m ² )
A0: Total area of circular carpet (m ² )
A1: Total area (m ² ) of the portion where the wear ring contacts.

T.A. Carpet feel (flexibility) and appearance (glossiness)
A gold-containing dye (Irgaran Red 4GL [manufactured by Ciba-Gaigi)] was treated with 0.6% owf, bath ratio 1:50 (as a carpet), pH = 7, and treated at 98 ° C. for 60 minutes for dyeing. When the dyed carpet was pressed with the palm, the feeling of touch (flexibility) and visual observation under sunlight were confirmed for glossiness and glossy spots.
Double circle, extremely good ○ ・ ・ ・ Excellent △ ・ ・ ・ Same as conventional product × ・ ・ ・ Inferior to conventional product

[Production Example 1] (Production of polylactic acid)
Polymerization of lactide prepared from L-lactic acid having an optical purity of 99.8% in the presence of bis (2-ethylhexanoate) tin catalyst (lactide to catalyst molar ratio = 10000: 1) at 180 ° C. for 240 minutes in a nitrogen atmosphere. And polylactic acid P1 was obtained. The resulting polylactic acid had a weight average molecular weight of 23,000. The amount of lactide remaining was 0.12% by weight.

[Production Example 2] (Production of polylactic acid containing 10% by weight of polycarbodiimide)
After drying P1 and polycarbodiimide “LA-1” manufactured by Nisshinbo Co., Ltd., it was supplied to a twin-screw kneading extruder so that P1: LA-1 = 90: 10 (weight ratio), and the cylinder temperature was 200 ° C. By kneading, polylactic acid P2 containing 10% by weight of LA-1 was obtained. The amount of residual lactide of the obtained polylactic acid was 0.14% by weight.

[Production Example 3] (Production of polylactic acid)
Polymerization of lactide produced from L-lactic acid with an optical purity of 99.8% in the presence of bis (2-ethylhexanoate) tin catalyst (lactide to catalyst molar ratio = 10000: 1) at 180 ° C. for 150 minutes in a nitrogen atmosphere. And polylactic acid P3 was obtained. The weight average molecular weight of the obtained polylactic acid was 150,000. The amount of residual lactide was 0.10% by weight.

Example 1
Polylactic acid P1 (melting point: 177 ° C.) as component A and nylon 6 (melting point: 225 ° C.) having a relative viscosity of sulfuric acid of 2.15 as component B were dried to give a moisture content of component A of 50 to 100 ppm and a moisture content of component B, respectively. It is adjusted to 100 to 300 ppm, chip blended at a blend ratio (weight ratio) P1 / nylon 6 = 30/70, charged into a spinning hopper 1 of a spinning device equipped with a twin screw kneader shown in FIG. 4, and twin screw extrusion kneading. The melted polymer was measured and discharged in the spinning block 3, and the molten polymer was guided to the built-in spinning pack 4 and spun from the spinneret 5. The die used was a Y-shaped hole described below. At this time, the annular chimney 6 (cooling length: 30 cm) was installed so that the upper end of the blow hole was 3 cm below the cap surface, the yarn 7 was cooled and solidified, and two stages of oil supply were performed by the oil supply device 8 and the oil supply device 9. Further, after taking the temperature of the first heating roll 11 (hereinafter referred to as 1FR) at 60 ° C. at a spinning speed of 700 m / min, the temperature of the second heating roll 12 (hereinafter referred to as 1DR) is set to 120 ° C. and 1890 m / min. The first stage stretching (stretching ratio: 2.7 times) is performed in minutes, and the temperature of the third heating roll 13 (hereinafter referred to as 2DR) is set to 157 ° C., and the second stage stretching (at 2590 m / min) ( Stretching ratio: 1.37)), and continuously crimped by heating and air pressure with an air stuffer device at a nozzle temperature of 220 ° C. to form a three-dimensional crimp, which is drawn against a cooling drum. After being taken up, it was taken up at a take-up tension of 120 g (0.08 cN / dtex) and a take-up speed of 2200 m / min (15% lower than 2DR speed). The obtained polylactic acid crimped yarn was 1500 dtex and 96 filaments. The melt spinning conditions are as follows. In addition, the discharge linear velocity in a nozzle | cap | die hole on the following conditions is 0.184 m / sec. The breaking elongation of the drawn yarn sampled at the 2DR outlet was 35%.
-Twin screw extruder temperature: 225 ° C
-Shearing speed during kneading: about 2000 sec ^-1
-Spinning temperature: 240 ° C
-Filter layer: 46 #, filled with white Morundum sand-Filter: 20 μm non-woven filter (Dynalloy)
・ Base: slit width 0.14mm, slit length 0.7mm, hole depth 0.6mm
・ Discharge rate: 330 g / min (1 pack 1 yarn, 96 filaments)
Cooling: Cooling air temperature 19 ° C., wind speed 0.55 m / sec. Oil: Adhering 10% of oil mixed with polyether oil 15 and low-viscosity mineral oil 85 to the yarn (1.5% pure oil) % Owf).

  Although about 100 kg of crimped yarn was sampled, yarn breakage, single yarn flow, etc. did not occur in all steps of spinning, drawing, and bulky processing, and the yarn was extremely stable.

  When the cross section of the obtained fiber was observed with a TEM, it was found to have a uniformly dispersed sea-island structure, and the island domain size was 0.03 to 0.3 μm in terms of diameter. Moreover, when the section of the yarn cross section was alkali etched to dissolve and remove polylactic acid, the island component was missing, and it was confirmed that polylactic acid formed the island component. 2 are formed on the fiber surface, and the average width of the streak grooves is 0.26 μm and the aspect ratio (length of streak grooves / width of streak grooves) is 20. Met. The resulting fiber has a tensile strength of 2.8 cN / dtex, residual elongation: 48%, boiling water shrinkage: 2.8%, yarn spot U%: 0.8%, crimp elongation: 12%, Deformation degree: 2.5, showing good fiber properties. Further, melting points by DSC were around 175 ° C. (polylactic acid) and around 225 ° C. (nylon 6), and melting peaks attributable to the respective components were observed. Moreover, the carboxyl group terminal density | concentration of the polylactic acid extracted from this fiber was 18 equivalent / ton. Furthermore, the number of yarn cutting rotations by the wear test was 101 times, indicating good wear resistance. Furthermore, when the carpet was made using the crimped yarn and evaluated, the weight loss rate was 25.5%, and the carpet exhibited good wear resistance. In addition, it was a carpet with a soft, moderate waist, and a moist silky luster.

(Example 2)
An air stuffer crimped yarn was obtained in the same manner as in Example 1 except that the blend ratio of P1 / component B was 10/90. As in Example 1, the yarn forming property of Example 2 was extremely stable. When the TEM observation of the cross section of the obtained fiber was performed, the island structure was uniformly dispersed, and the island domain size was 0.01 to 0.15 μm in terms of the diameter, and the dispersion of island components was greater than in Example 1. The diameter was small. Further, when the section of the yarn cross section was alkali etched to dissolve and remove the polylactic acid, the island component was missing, and it was confirmed that the polylactic acid formed the island component.

  Further, the degree of irregularity of the obtained fiber was 2.4, and the fiber physical properties were also good. Further, melting points by DSC were around 175 ° C. (polylactic acid) and around 225 ° C. (nylon 6), and melting peaks attributable to the respective components were observed. The obtained multifilament had a yarn cutting rotational speed of 185 times according to the abrasion test, which was superior to Example 1.

  Further, when a carpet was prepared using the crimped yarn and evaluated, a product having excellent wear resistance and a soft feeling as compared with Example 1 was obtained. However, the gloss was slightly duller than Example 1.

(Example 3)
An air stuffer crimped yarn was obtained in the same manner as in Example 1 except that the blend ratio of P1 / component B was 40/60. As in Example 1, the yarn forming property of Example 3 was extremely stable. When the TEM observation of the cross section of the obtained fiber was performed, it had a uniformly dispersed sea-island structure, and the island domain size was 0.03 to 0.8 μm in terms of diameter, which is a more dispersed island component than in Example 1. The diameter was large. When the carpet was prepared using the crimped yarn and evaluated, Example 1 was superior in abrasion resistance, but both the tactile sensation and the appearance were superior to the conventional products.

( Comparative Example 6 )
An air stuffer crimped yarn was obtained in the same manner as in Example 1 except that the blend ratio of P1 / component B was 5/95. As in Example 1, the yarn forming property of Comparative Example 6 was extremely stable. When the TEM observation of the cross section of the obtained fiber was performed, it has a uniformly dispersed sea island structure, and the island domain size is 0.01 to 0.1 μm in terms of diameter, and the dispersion diameter of the island component is extremely small. There were few islands. Further, almost no streak-like grooves were formed on the fiber surface of the crimped yarn. When a carpet was prepared using the crimped yarn and evaluated, it was found to have a high flexibility and excellent tactile sensation as in Example 1, but the glossiness was equivalent to the conventional product.

(Example 5)
An air stuffer crimped yarn was obtained in the same manner as in Example 1 except that nylon 6 (melting point: 225 ° C.) having a relative viscosity of 2.05 was used as component B and the blend ratio of P1 / component B was 47/53. It was. In Example 5, the bulge of the discharge flow was slightly large due to the ballast effect directly under the base. Further, when 100 kg of crimped yarn was sampled, the yarn breakage occurred twice, which was slightly inferior to the yarn in Example 1. When the TEM observation of the cross section of the obtained fiber was performed, it was found that the island structure was uniformly dispersed, the island domain size was 0.03 to 0.8 μm in terms of diameter, and the dispersion diameter of the island component was Example 1. In contrast, it was slightly larger. When a carpet was prepared using the crimped yarn and evaluated, the abrasion resistance of Example 1 was superior. Further, the touch was somewhat rough and hard, but had a moist silky luster.

(Comparative Example 1)
An air stuffer crimped yarn was obtained in the same manner as in Example 1 except that only component A (polylactic acid P1) was used. The yarn forming property of Comparative Example 1 was stable as in Example 1. The crimped yarn obtained had a yarn cutting rotational speed of 9 by the wear test and was extremely inferior in wear resistance. Moreover, when the carpet was made using the crimped yarn and evaluated, the wear loss rate was 89%, which was a level that considerably limited the application.

(Example 6)
An air stuffer crimped yarn was obtained in the same manner as in Example 1 except that polylactic acid P3 (melting point: 178 ° C.) was used as component A and the spinning conditions were changed as follows.
・ Shear rate of biaxial kneader: about 280 sec ⁻¹
・ Filtration layer configuration: φ1mm glass bead filling ・ Filtration filter: 200 # wire mesh filter

  In Example 6, the thinning point just below the base was not stable, and the discharge flow was somewhat unstable. Further, when 100 kg of crimped yarn was sampled, the yarn breakage occurred three times, which was slightly inferior to the yarn in Example 1. When the TEM observation of the cross section of the obtained fiber was carried out, the island domain size was 0.3 to 2.5 μm in terms of diameter, and the dispersion diameter of the island component was large, and the distribution was It was wide. Further, it was found that Worcester spots U% indicating thread spots were as high as 2.1%, and that there were thick spots in the longitudinal direction of the threads. As a result of producing and evaluating a carpet using the crimped yarn, the wear loss rate was about twice that of Example 1. Further, the tactile sensation was partially rough and the glossiness was at the same level as the conventional product.

(Comparative Example 2)
An air stuffer crimped yarn was obtained in the same manner as in Example 1 except that polylactic acid P1 (melting point: 178 ° C.) was used as component A and nylon 6 (melting point: 225 ° C.) having a relative viscosity of sulfuric acid of 2.90 was used as component B. . In Comparative Example 2, a very large bulge was generated due to the ballast effect directly under the base, and therefore, a pulsation phenomenon in which the thinning point fluctuated up and down occurred, which was an unstable state. Further, when 100 kg of crimped yarn was sampled, yarn breakage frequently occurred at 17 times, and the yarn forming property was considerably poor. Moreover, when the TEM observation of the cross section of the obtained fiber was performed, although the sea island structure was taken, the island component was dyed. Therefore, when polylactic acid was eluted by alkaline etching, only the island component remained as an ultrafine thread, indicating that polylactic acid formed a sea component. The crimped yarn had a low strength of 1.1 cN / dtex, and the yarn unevenness U% was 4.5%, which was extremely bad. When the carpet was made using the crimped yarn and evaluated, the wear loss rate was 87%, which was the same level as that of polylactic acid alone (Comparative Example 1), and the application was considerably limited.

(Example 7)
An air stuffer crimped yarn was obtained in the same manner as in Example 1 except that nylon 11 having an intrinsic viscosity of 1.45 was used as Component B. As in Example 1, the yarn forming property of Example 7 was extremely stable. When the TEM observation of the cross section of the obtained fiber was performed, it had a uniformly dispersed sea-island structure, and the island domain size was 0.05 to 0.5 μm in terms of diameter. Further, when the section of the yarn cross section was alkali etched to dissolve and remove the polylactic acid, the island component was missing, and it was confirmed that the polylactic acid formed the island component.

  Furthermore, when the carpet was made using the crimped yarn and evaluated, the bulkiness was higher than that of Example 1, the quality was high, and the wear resistance was excellent. Further, both the tactile sensation and the appearance were extremely excellent as in Example 1.

(Example 8)
An air stuffer crimped yarn was obtained in the same manner as in Example 1 except that nylon 610 (melting point: 225 ° C.) having a relative viscosity of sulfuric acid of 2.15 was used as Component B. As in Example 1, the yarn forming property of Example 8 was extremely stable. When the cross section of the obtained fiber was observed with a TEM, it was found to have a uniformly dispersed sea-island structure, and the island domain size was 0.03 to 0.3 μm in terms of diameter. Further, when the section of the yarn cross section was alkali etched to dissolve and remove the polylactic acid, the island component was missing, and it was confirmed that the polylactic acid formed the island component. Further, when a carpet was prepared using the crimped yarn and evaluated, the feel and appearance were excellent as in Example 1.

Example 9
As component B, N6 / N66 copolymer nylon (melting point 198 ° C.) polymerized at a weight ratio of ε-caprolactam / hexamethylenediammonium adipate (66 salt) = 85/15 was used in the same manner as in Example 1. Air stuffer crimped yarn was obtained. As in Example 1, the yarn forming property of Example 9 was extremely stable. When the cross section of the obtained fiber was observed with a TEM, it was found to have a uniformly dispersed sea-island structure, and the island domain size was 0.03 to 0.26 μm in terms of diameter. Further, when the section of the yarn cross section was alkali etched to dissolve and remove the polylactic acid, the island component was missing, and it was confirmed that the polylactic acid formed the island component. Furthermore, when the carpet was prepared using the crimped yarn and evaluated, the bulkiness was higher than that of Example 1. Further, both the tactile sensation and the appearance were extremely excellent as in Example 1.

(Example 10)
Polylactic acid P2 containing a compatibilizing agent (component C) (polycarbodiimide “LA-1”: 10 wt%) was used, and the blend ratio was P1 / component B / P2 = 20/70/10 (component A and component B) The air stuffer crimped yarn was used in the same manner as in Example 1 except that the concentration of component C with respect to the total amount was 1.0 wt%. As in Example 1, the yarn forming property of Example 10 was extremely stable. When the cross section of the obtained fiber was observed with a TEM, it was found to have a uniformly dispersed sea-island structure, and the island domain size was 0.03 to 0.3 μm in terms of diameter. Furthermore, when the carpet was made using the crimped yarn and evaluated, it was superior in abrasion resistance as compared with Example 1 and was extremely excellent in both touch and appearance as in Example 1.

(Comparative Example 3)
An air stuffer crimped yarn was obtained in the same manner as in Example 1 except that melt spinning was performed at a spinning temperature of 270 ° C. (Tmb + 45 ° C.). The melt viscosity of component A at the spinning temperature was 35 Pa · s, and the melt viscosity of component B was 28 Pa · s (ηb / ηa = 0.8). In Comparative Example 3, swelling occurred due to the ballast effect directly below the base, and the discharge flow was somewhat unstable. In addition, when 100 kg of crimped yarn was sampled, yarn breakage occurred five times, which was slightly inferior to the yarns of Example 1. When the TEM observation of the cross section of the obtained fiber was performed, a portion where the sea-island structure was partially reversed and a portion having a co-continuous structure formed by connecting islands coexisted. In addition, the strength was 1.4 cN / dtex, which was about a half of that in Example 1, and the Worcester spot U% indicating the thread spot was as high as 2.2%. When the carpet was made using the crimped yarn and evaluated, the wear loss rate was extremely poor at 76.5%, and the glossiness was inferior to that of the conventional product.

(Comparative Example 4)
The yarn was produced in the same manner as in Example 3 except that the base was changed to a Y hole having a slit width of 0.43 mm, a slit length of 2.15 mm, and a hole depth of 0.6 mm. Swelling directly under the base did not occur, but the thinning was not stable and the yarn could not be produced. In addition, the discharge linear velocity in the nozzle hole of the comparative example 4 is 0.0195 m / sec.

(Comparative Example 5)
The yarn was produced in the same manner as in Example 3 except that the base was changed to a Y hole having a slit width of 0.09 mm, a slit length of 0.45 mm, and a hole depth of 0.6 mm. In Comparative Example 5, a very large bulge was generated due to the ballast effect directly under the base, and as a result, a pulsation phenomenon in which the thinning point fluctuated up and down occurred, and the yarn could not be produced.

(Example 11)
An air stuffer crimped yarn was obtained in the same manner as in Example 1 except that the cooling air speed at the annular chimney was 0.1 m / sec. In Example 11, swelling occurred due to the ballast effect directly under the base, and a slight pulsation phenomenon occurred. Therefore, the yarn breakage occurred twice with 100 kg sampling. The crimped yarn thus obtained had a strength of 1.3 cN / dtex, which was about half that of Example 1, and had a high Worcester spot U% showing a thread spot of 3.3%. When the carpet was made using the crimped yarn and evaluated, the wear loss rate was slightly poor at 46.8%, and the touch feeling was somewhat coarse, but the silky gloss The appearance was good.

(Example 12)
The second stage stretching (stretching ratio: 1.15 times) was performed at a 2DR speed of 2173 m / min with a discharge rate of 277 g / min, and the winding speed was 1847 m / min (15% lower than the 2DR speed). Except for the above, an air stuffer crimped yarn was obtained in the same manner as in Example 1. The breaking elongation of the drawn yarn sampled at the 2DR outlet was 76%. The obtained crimped yarn had a strength of 1.8 cN / dtex and a strength of about 64% as compared with Example 1, and the Worcester spot U% indicating the yarn spot was 1.6%, which was slightly high. When the carpet was made using the crimped yarn and evaluated, the abrasion loss rate was 41.1%, which was a little bad, but it was at a level that could be used if the application was limited.

( Comparative Example 7 )
An air stuffer crimped yarn was obtained in the same manner as in Example 1 except that the setting temperature at 2DR was 130 ° C. As in Example 1, the yarn forming property of Comparative Example 7 was extremely stable. When the TEM observation of the cross section of the obtained fiber was performed, it had a uniformly dispersed sea island structure, and the island domain size was 0.03 to 0.3 μm in terms of diameter, which was the same level as in Example 1. However, almost no streak-like grooves were formed on the fiber surface of the crimped yarn. Also, the crimp elongation rate was less than half that of Example 1. When a carpet was prepared using the crimped yarn and evaluated, the gloss was equivalent to that of the conventional product, although the feel was superior to that of the conventional product.

( Comparative Example 8 )
An air stuffer crimped yarn was obtained in the same manner as in Example 1 except that the setting temperature at 2DR was 110 ° C. The yarn forming property of Comparative Example 8 was stable as in Example 1. The obtained fiber had a crimp elongation ratio of 2.5% and was not so crimped. Moreover, the boiling water shrinkage rate was as high as 11.1%, and Example 1 was superior in dimensional stability. When the carpet was made using the crimped yarn and evaluated, both the tactile sensation and glossiness were equivalent to those of the conventional product.

(Example 15)
An air stuffer crimped yarn was obtained in the same manner as in Example 13 except that the base was changed to a round hole having a diameter of 0.62 mm and a hole depth of 1.0 mm. As in Example 1, the yarn forming property of Example 15 was extremely stable. The cross-section of the obtained fiber is almost a perfect circle (degree of irregularity 1.0). When the TEM observation of the cross-section is performed, it has a uniformly dispersed sea-island structure, and the island domain size is 0 in terms of diameter. 0.03 to 0.3 μm, which is the same level as in Example 1. When a carpet was prepared using the crimped yarn and evaluated, the gloss feeling of Example 1 was superior to that of Example 1, although the texture was excellent as in Example 1.

(Example 16)
An air stuffer crimped yarn was obtained in the same manner as in Example 1 except that the air jet stuffer device was heated and compressed with a nozzle temperature of 150 ° C. The crimped yarn had a low crimp elongation ratio of 2.7% and did not exhibit much crimp. When the carpet was prepared using the crimped yarn and evaluated, the gloss was excellent, but the touch was slightly coarse.

(Example 17)
1% by weight of talc “SG-2000” (average particle diameter D50: 0.98 μm, particles of 10 μm or more: 0% by volume) manufactured by Nippon Talc Co., Ltd. with respect to polylactic acid P1 (component A) Air stuffer crimped yarn was obtained in the same manner as in Example 1 except that 0.3% by weight (dry blending). As in Example 1, the yarn forming property of Example 17 was extremely stable. Further, the crimped yarn exhibited an elongation rate under a restraining load of about 1.4 times that of Example 1, and had high crimp fastness.

(Example 18)
1% by weight (fiber) of melamine cyanurate “MC-600” (average particle diameter 1.6 μm, particles 10 μm or more: 0% by volume) manufactured by Nissan Chemical Industries, Ltd. with respect to polylactic acid P1 (component A) Air stuffer crimped yarn was obtained in the same manner as in Example 1 except that 0.3% by weight of the whole was dry blended. As in Example 1, the yarn forming property of Example 18 was extremely stable. Further, the crimped yarn showed an elongation rate of about 1.8 times that of Example 1 and a very high crimp fastness.

(Example 19)
Air staff as in Example 1 except that 0.03 wt% of copper iodide and potassium iodide (0.021 wt% of the whole fiber) were dry blended with nylon 6 (component B), respectively. A key yarn was obtained.
Further, the crimped yarn obtained in Example 1 and the crimped yarn of Example 19 were cut off and used under the following conditions using a UV auto fade meter (type: U48AU) manufactured by Suga Test Instruments Co., Ltd. A light resistance test was conducted, and the strength retention was determined from the strength before and after the light resistance test. As a result, the strength retention of the crimped yarn of Example 1 was 5%, whereas the strength retention of the crimped yarn of Example 19 was 91%, which was a very excellent light fastness. .

<UV treatment conditions>
UV irradiation time: 100 hrs
Black panel temperature: 83 ° C
Temperature inside the can: 64 ± 3 ° C
Humidity: relative humidity 50 ± 5% relative to the temperature in the can
Strength retention (%) = strength after UV treatment (cN / dtex) / strength before UV treatment (cN / dtex) × 100

It is a TEM photograph for demonstrating the sea island structure of the polymer alloy fiber of this invention. It is a SEM photograph of the fiber surface layer of the crimped yarn (Example 1) of this invention. It is the schematic for demonstrating the aspect-ratio of the streak-like groove | channel formed in the fiber surface layer of a crimped yarn. FIG. 2 is a schematic view of a direct spinning / drawing / crimping apparatus preferably used for producing the crimped yarn of the present invention. In the manufacturing method of this invention, it is the schematic for demonstrating the hole depth of a nozzle | cap | die. In the manufacturing method of this invention, it is the schematic for demonstrating a cooling start point.

Explanation of symbols

1: Spinning hopper 2: Twin screw extrusion kneader 3: Spinning block 4: Spinning pack 5: Spinneret 6: Circular chimney (yarn cooling device)
7: Yarn 8: Refueling device 1
9: Refueling device 2
10: Stretch roll 11: First heating roll (1FR)
12: Second heating roll (1DR)
13: Third heating roll (2DR)
14: Air jet stuffer device 15: Cooling roll 16: Tension measuring detector 17: Take-up roll 18: Winding machine 19: Cooling air blowing surface

Claims (18)

An air stuffer crimped yarn composed of a polymer alloy synthetic fiber containing an aliphatic polyester resin (A) and a thermoplastic polyamide resin (B), wherein the aliphatic polyester resin (A) is an island And the thermoplastic polyamide resin (B) has a sea-island structure in which a sea component is formed, and a streak groove extending in the fiber axis direction is formed on the fiber surface, and the width of the streak groove A crimped yarn having a diameter of 0.01 to 1 μm . The crimped yarn according to claim 1, wherein the island component has a domain size of 0.001 to 2 µm. The crimped yarn according to claim 1 or 2, wherein the aliphatic polyester resin (A) is a crystalline resin and has a melting point of 150 to 230 ° C. The crimped yarn according to any one of claims 1 to 3, wherein the thermoplastic polyamide resin (B) is a crystalline resin and has a melting point of 150 to 250 ° C. The crimped yarn according to any one of claims 1 to 4, wherein a blend ratio (weight ratio) of the aliphatic polyester resin (A) and the thermoplastic polyamide resin (B) is 5/95 to 55/45. A polymer alloy comprising an aliphatic polyester resin (A) and a thermoplastic polyamide resin (B) is further added with a compound (C) containing two or more active hydrogen reactive groups in one molecule. The crimped yarn according to any one of claims 1 to 5, which is obtained in the above manner. The crimped yarn according to claim 6, wherein the active hydrogen reactive group is at least one reactive group selected from the group consisting of a glycidyl group, an oxazoline group, a carbodiimide group, and an acid anhydride group. Two or more activities in one molecule relative to the total amount of the aliphatic polyester resin (A), the thermoplastic polyamide resin (B), and the compound (C) containing two or more active hydrogen reactive groups in one molecule The crimped yarn according to claim 6 or 7, wherein the content of the compound (C) containing a hydrogen reactive group is 0.005 to 5% by weight. The crimped yarn according to any one of claims 1 to 8, wherein an aspect ratio of the streak groove (long axis length of streak groove / width of streak groove) is 10 to 500. The crimped yarn according to any one of claims 1 to 9 , wherein the crimped yarn satisfies the following physical properties.
Strength: 1 cN / dtex or more Crimp elongation after boiling water treatment: 3-30%
Deformity (D1 / D2): 1.2-7 The aliphatic polyester resin (A) contains 0.01 to 2% by weight of at least one crystal nucleating agent selected from talc, sorbitol derivatives, phosphate metal salts, basic inorganic aluminum compounds, and melamine compound salts. The crimped yarn according to any one of claims 1 to 10 . A fiber structure comprising at least a part of the crimped yarn according to any one of claims 1 to 11 . The fiber structure according to claim 12 , wherein the fiber structure is a carpet for automobile interior. When kneading the aliphatic polyester resin (A) and the thermoplastic polyamide resin (B) at a blend ratio (weight ratio) of 5/95 to 55/45, the melt viscosity ratio (ηb / ηa) is 0.1 to 2 After the pelletization or the continuous melt spinning, the spinning temperature is set to Tmb + 3 ° C. to Tmb + 40 ° C. with respect to the melting point Tmb of the thermoplastic polyamide resin (B). A multifilament is formed at a discharge linear velocity of 0.02 to 0.4 m / sec, and is substantially orthogonal to the multifilament, with 0.01 to 0.15 m vertically below the base surface as a cooling start point. Cooling with a gas having a wind speed of 0.3 to 1 m / second and a wind temperature of 15 to 25 ° C., covering the multifilament with a spinning finish, and heating with a heating roll of 50 to 130 ° C. The multifilament is stretched in 1 to 3 stages so that the breaking elongation is 15 to 65%, and the final roll temperature after stretching is Tma-30 to Tma + 30 ° C. with respect to the melting point Tma of the aliphatic polyester resin (A). Is set to heat and then supplied to the air jet stuffer device, and the nozzle temperature of the device is 5 to 100 ° C. higher than the final roll temperature after drawing to perform a crimping process to form a three-dimensional crimped yarn. A method for producing a crimped yarn, which is taken up against a cooling drum and wound at a speed 10 to 30% lower than the final roll after drawing.
(Where ηa: melt viscosity of the aliphatic polyester resin (A), ηb: melt viscosity of the thermoplastic polyamide resin (B)) To the aliphatic polyester resin (A) and / or thermoplastic polyamide resin (B), a compound (C) containing two or more active hydrogen reactive groups in one molecule is added as a compatibilizing agent and melt-kneaded. The method for producing a crimped yarn according to claim 14 . Compound (C) containing two or more active hydrogen reactive groups in one molecule is converted into aliphatic polyester resin (A), thermoplastic polyamide resin (B), and two or more active hydrogen reactions in one molecule. The manufacturing method of the crimped yarn of Claim 15 which adds 0.005 to 5 weight% of the total amount of the compound (C) addition amount containing a sex group. At least one crystal nucleating agent selected from talc, a sorbitol derivative, a phosphate ester metal salt, a basic inorganic aluminum compound, and a melamine compound salt is added to the aliphatic polyester resin (A) and / or the thermoplastic polyamide resin (B). The method for producing a crimped yarn according to any one of claims 12 to 16 , which is added and melt-kneaded. 0.01 to 2% by weight of at least one crystal nucleating agent selected from talc, sorbitol derivative, phosphate metal salt, basic inorganic aluminum compound and melamine compound salt is added to aliphatic polyester resin (A). The method for producing a crimped yarn according to claim 17 .

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