JP2010150694A - Liquid crystalline polyester fiber and method for producing the same - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide a fiber keeping the excellent dynamic characteristics of a liquid crystalline polyester fiber, while improving abrasion resistance by leaps and bounds, and to provide a method for producing the same. <P>SOLUTION: The liquid crystalline polyester fiber has a half band width of a peak having a maximum at 18 to 22° in an equatorial line direction of not less than 3.5°, and having ≤0.92 a crystal orientation π calculated by using a half band width Δβ in an intensity distribution from 0 to 360° of an azimuth angle direction by centering around the peak in a wide angle X-ray diffraction measurement by using CuKα ray as a radiation source. <P>COPYRIGHT: (C)2010,JPO&INPIT

Description

The present invention relates to a liquid crystalline polyester fiber excellent in strength, elastic modulus and abrasion resistance and a method for producing the same.

  Liquid crystalline polyester fiber is a high-performance fiber with high strength and high elastic modulus derived from the strength of intermolecular interaction of crystal parts exhibiting liquid crystallinity, and it is also chemically stable in various fields. Applications are expanding. In particular, liquid crystalline polyester fibers can be increased in molecular weight by solid-phase polymerization, and for this reason, can be made a material having higher strength and higher elastic modulus.

  As for the use, the use as a mesh constituting fiber for screen printing has been expanded in recent years, and attention is paid to the difficulty of plastic deformation and the good printability due to the high elastic modulus. In recent years, a particularly large opening ratio (opening) and a narrow wire diameter have been desired, and great expectations are placed on liquid crystalline polyester fibers.

  However, since the liquid crystalline polyester fiber has a fiber structure in which molecular chains are highly oriented in the fiber axis direction during spinning, the tensile strength and elastic modulus in the fiber axis direction are very high, while the cohesive force in the cross-sectional direction is high. However, a fiber having a structure in which crystallization has progressed has a problem that wear easily proceeds by rubbing. For example, when the fiber is rubbed against a metal guide or the like existing in the weaving process, this problem easily causes fibrillation and becomes a mesh defect. Moreover, since the fibers are fibrillated even when rubbed during actual use, there is a drawback that the product life is shortened.

  For improving the abrasion resistance of the liquid crystalline polyester fiber, the core component is liquid crystalline polyester, the sheath component is a core-sheath type composite fiber (see Patent Document 1), the island component is liquid crystalline polyester, and the sea component is bent. A sea-island type composite fiber made of a thermoplastic polymer has been proposed (see Patent Document 2). Although these technologies can achieve improved wear resistance by forming a fiber surface with a flexible polymer, the strength of the liquid crystalline polyester is inferior because of the high fraction of components other than the liquid crystalline polyester. In the solid phase polymerization of fibers necessary for the above, there is a problem that the fiber surface with a low melting point is fused and becomes a defect to cause fibrillation. Furthermore, in the core-sheath composite spinning as in Patent Document 1, the discharge amount of each core-sheath is smaller than that of single component spinning, and when the discharge amount is further reduced for fineness, the residence time is increased. There is a problem that the melt viscosity changes due to gelation or thermal decomposition, resulting in thick irregularities and complex abnormalities in the longitudinal direction of the fiber, and the uniformity in the longitudinal direction is impaired. Further, in blend spinning as in Patent Document 2, if the discharge amount is reduced for fineness, the effect of blend unevenness in the longitudinal direction becomes obvious and the uniformity in the longitudinal direction is impaired.

  In addition, a technique has been proposed in which wear resistance is improved by heat-treating a composite fiber composed of a liquid crystalline polyester and a flexible thermoplastic resin at a temperature equal to or higher than the melting point of the flexible thermoplastic resin + 20 ° C. (see Patent Documents 3 and 4). ). However, this technique has a problem that the obtained fiber is inferior in heat resistance because the abrasion resistance is improved by making the flexible thermoplastic resin amorphous. Moreover, since it is a composite spinning, there was also a problem that the uniformity in the longitudinal direction was impaired as described above.

  These problems are caused by the means of combining the liquid crystalline polyester and other components, and from this, a technique capable of achieving high wear resistance with a single component of the liquid crystalline polyester has been desired.

  With regard to improving the wear resistance of single-component yarns, polyamides, polyvinylidene fluoride, and polypropylene monofilaments for fishing lines, fishing nets, mowing machines, etc., apply heat above the melting point to the drawn monofilaments to promote surface orientation relaxation and wear resistance. A method for improving the performance has been proposed (see Patent Documents 5 to 9). However, this technique is a technique that can be achieved because the polymer is a flexible polymer and the time required for orientation relaxation (relaxation time) is short, and when the molecular chain is rigid such as liquid crystalline polyester, the relaxation time becomes long, There was a problem that the inner layer also relaxed and the fibers melted during the time when the surface layer relaxed. Furthermore, as the single fiber fineness decreases, the effect of heat treatment reaches the center of the fiber, and there is a problem that it is difficult to achieve both sufficient strength and wear resistance.

  In addition, there is a technique in which liquid crystalline polyester fibers are heated and cured (solid phase polymerization) at a temperature lower than the melting point, and then stretched by 10% to 400% within a temperature range of 50 ° C. to increase the strength and elastic modulus. It has been proposed (see Patent Document 10). However, this technique aims to further increase the molecular chain orientation by stretching at a temperature that can maintain the crystallinity, and to increase the strength and elastic modulus. The fiber has high crystallinity and high molecular chain orientation. Wear resistance cannot be improved due to the structure. In this technique, the relationship between the stretching temperature and the melting point of the liquid crystalline polyester fiber subjected to stretching is only specified in Examples 3 and 4, but the stretching temperature is lower than the melting point of the liquid crystalline polyester fiber. There is no suggestion about the effect of heating the solid-phase polymerized liquid crystalline polyester fiber to the melting point or higher.

  Furthermore, in order to improve the abrasion resistance of the liquid crystalline polyester fiber, there is a method in which polysiloxane and / or fluorine resin is adhered to the fiber surface and dried at 100 ° C. to 300 ° C. or heated and fired at 350 ° C. or higher. It has been proposed (see Patent Document 11). However, in this technique, a treatment at a high temperature is performed for drying or baking, and this is a treatment for making it difficult to remove the attached polysiloxane and / or fluorine-based resin, and the liquid crystalline polyester to be treated. There is no description of the relationship with the melting point of the fiber, and it is not a technique for improving the wear resistance of the fiber itself by a structural change.

Patent Document 12 or Patent Document 13 discloses a technique for improving the wear resistance of a liquid crystalline polyester fiber by performing a heat treatment at a temperature equal to or higher than the melting point. These techniques can certainly improve the wear resistance of the liquid crystalline polyester fiber, but in the process of cooling the fiber after heat treatment, the cold crystallization proceeds and the wear resistance deteriorates again, There was concern that the process passability and durability were inferior.
JP-A-1-229815 (first page) JP 2003-239137 A (first page) Japanese Unexamined Patent Publication No. 2007-119976 (first page) JP 2007-119977 A (first page) JP-A-60-231815 (first page) JP 61-152810 A (first page) JP 61-170310 A (first page) Japanese Patent Laid-Open No. 5-148707 (first page) JP-A-8-158151 (first page) JP-A-50-43223 (2nd page) Japanese Patent Laid-Open No. 11-269737 (page 3) JP2008-240230 (5th page) JP 2008-240228 A (first page)

  The object of the present invention can be solved by a liquid crystalline polyester fiber having dramatically improved wear resistance without impairing mechanical properties and a method for producing the same.

An object of the present invention is a liquid crystal characterized in that in a wide-angle X-ray diffraction measurement using CuKα rays as a radiation source, the half-value width of a peak having a maximum at 18 to 22 ° in the equator direction is 3.5 ° or more. Is solved by a sexual polyester fiber.

  In addition, the manufacturing method is such that fibers made of liquid crystalline polyester are heat-treated at a temperature of not less than 10 ° C., endothermic peak temperature (Tm) observed in differential scanning calorimetry under conditions of 10 mg and 50 ° C./min. Then, after performing forced cooling with a fluid within 0.05 seconds, it is wound up.

  According to the liquid crystalline polyester fiber and the method for producing the same of the present invention, it is possible to provide a fiber excellent in abrasion resistance while maintaining the excellent mechanical properties of the liquid crystalline polyester.

  Hereinafter, the liquid crystalline polyester fiber of the present invention will be described in detail.

  The liquid crystalline polyester of the present invention is a polyester that can form an anisotropic molten phase (liquid crystalline) upon melting. This characteristic can be confirmed, for example, by placing a sample made of liquid crystalline polyester on a hot stage, heating and heating in a nitrogen atmosphere, and observing the transmitted light of the sample under polarized light.

  The melting point of the liquid crystalline polyester of the present invention is preferably 200 to 380 ° C., more preferably 250 to 350 ° C., and further preferably 280 to 330 ° C. in order to widen the temperature range in which melt spinning is possible. In addition, melting | fusing point (Tm) of liquid crystalline polyester points out the value measured by the method of an Example description.

  Further, the liquid crystalline polyester used in the present invention may contain other polymers, additives, and fillers as long as the properties are not largely changed. Polymers include polyesters, vinyl polymers such as polyolefin and polystyrene, polycarbonate, polyamide, polyimide, polyphenylene sulfide, polyphenylene oxide, polysulfone, aromatic polyketone, aliphatic polyketone, semi-aromatic polyesteramide, polyetheretherketone, fluorine Polymers such as resins may be added, such as polyphenylene sulfide, polyether ether ketone, nylon 6, nylon 66, nylon 46, nylon 6T, nylon 9T, polyethylene terephthalate, polypropylene terephthalate, polybutylene terephthalate, polyethylene naphthalate, polycyclohexane Preferred examples include dimethanol terephthalate and polyester 99M. In addition, when adding these polymers, the melting point is preferably within the melting point of the liquid crystalline polyester ± 30 ° C. so as not to impair the yarn forming property.

  Furthermore, within the range not impairing the effects of the present invention, various metal oxides, kaolin, silica and other inorganic substances, colorants, matting agents, flame retardants, antioxidants, ultraviolet absorbers, infrared absorbers, crystal nucleating agents In addition, various additives such as a fluorescent brightening agent, a terminal group blocking agent, and a compatibilizing agent may be contained in a small amount.

  In the liquid crystalline polyester fiber of the present invention, it is important that the half width calculated from the peak observed at 2θ = 18 to 22 ° in wide-angle X-ray diffraction is 3.5 ° or more. The full width at half maximum is an index representing the disorder of the crystal plane spacing. If the crystal melted by the heat treatment has a disordered structure, the full width at half maximum increases. When the structure has a disordered crystal plane spacing, the fibers have an unclear fibril hierarchical structure, and peeling between the fibrils is suppressed, so that the wear resistance is improved. The wider the half-value width, the more disordered the crystal plane spacing is. Therefore, the intermolecular force uniformity in the fiber cross section is high, and the fibril hierarchical structure is unclear. More preferably, it is most preferably 4.5 ° or more. The upper limit is not particularly limited, but the range of the full width at half maximum that can be achieved by the preferred production method of the present invention is approximately 7 °.

  Further, the liquid crystalline polyester fiber of the present invention has a half-width of a peak observed when scanning in the azimuth direction (β scan) with reference to a peak position observed at 2θ = 18-22 ° in wide-angle X-ray diffraction. The value of the degree of crystal orientation π calculated from Δβ according to the following formula is preferably 0.92 or less. The lower the degree of crystal orientation, the less the crystal part in the fiber is oriented, and the higher the correlation with the orientation of the fibrils, the better the index of wear resistance. For this reason, the lower the degree of crystal orientation, the better. However, if it is too low, the mechanical properties in the fiber axis direction may be lowered. Therefore, π is preferably 0.92 or less and 0.10 or more, more preferably 0.90 or less and 0.15 or more, and most preferably 0.85 or less and 0.20 or more.

π = (180−Δβ) / 180
The liquid crystalline polyester fiber of the present invention preferably has an endothermic peak area ΔHm of 3.0 J / g or less in a differential scanning calorimeter measured under conditions of a sample amount of 10 mg and 50 ° C. to 20 ° C./min. The area of the endothermic peak indicates the amount of crystals reflecting the history of heat and stress received by the liquid crystalline polyester fiber in the manufacturing process. As the amount of crystals increases, the tendency of the fibril hierarchical structure to be clear is observed, and the abrasion resistance of the fibers decreases. The cause of this is not clear, but the fiber with high crystallinity has a large difference between the crystalline part with high order and the low amorphous part. For this reason, it is considered that the separation proceeds selectively from a portion having a low intermolecular force. Thus, since the wear resistance of the liquid crystalline polyester fiber tends to improve as the amount of crystals decreases, it is more preferably 2.0 J / g or less, and the change is substantially below the measurement limit of the apparatus. Most preferably not observed.

  The liquid crystalline polyester fiber of the present invention preferably has a tensile strength of 12.0 cN / dTex or more. The higher the strength of the fiber, the more the fiber can be prevented from breaking during the process or in use. For this reason, the higher the tensile strength, the better. Among them, 13.0 cN / dTex or more is more preferable, and 14.0 cN / dTex or more is most preferable. The upper limit of the tensile strength is not particularly limited for the reasons described above, but if the structure is such that the crystal plane spacing in the fiber is sufficiently disturbed by forced cooling after heat treatment that is preferably performed in the present invention, the wear resistance is reduced. While improving, the tensile strength decreases. For this reason, the tensile strength is at most about 20.0 cN / dTex.

  Further, the elastic modulus of the liquid crystalline polyester fiber of the present invention is preferably 600 cN / dTex or more because the fiber does not undergo plastic deformation in actual use, and in particular, deformation due to repeated use in a screen printing mesh is less likely to occur. In particular, the elastic modulus is preferably as high as possible for maintaining printing accuracy by using the screen printing machine, and is more preferably 650 cN / dTex or more, and most preferably 700 cN / dTex or more. The upper limit of the elastic modulus is not particularly limited, but the elastic modulus that can be reached by the liquid crystalline polyester fiber of the present invention is about 1000 cN / dTex. The elastic modulus in the present invention refers to the initial tensile resistance described in JIS L1013: 1999.

  The liquid crystalline polyester fiber of the present invention preferably has an abrasion resistance M, which is an index of strength against rubbing with a metal material, of 50 seconds or more, more preferably 60 seconds or more, still more preferably 70 seconds or more, and 80 Particularly preferred is seconds or more. The abrasion resistance M referred to in the present invention refers to a value measured by the method described in the examples. Abrasion resistance M of 50 seconds or more can suppress fibrillation due to rubbing with wrinkles in the high-order processing process of liquid crystalline polyester fiber, particularly in the weaving process, and can greatly improve process passability. Since the accumulation of fibrils on the surface is reduced, the cleaning and replacement cycle can be extended.

  The liquid crystalline polyester fiber of the present invention can have a wide number of filaments. There is no particular upper limit on the number of filaments, but in order to make the aperture ratio uniform when a mesh fabric for screen printing is used, the number of filaments is preferably 50 or less, and more preferably 10 or less. A monofilament having a filament number of 1 is particularly suitable because the aperture ratio can be made extremely uniform.

  The liquid crystalline polyester fiber of the present invention has high strength, high elastic modulus, and high heat resistance, and has improved wear resistance. It is a general industrial material, civil engineering / building material, sports application, protection. Widely used in the fields of clothing, rubber reinforcing materials, electrical materials (especially as tension members), acoustic materials, and general clothing. Effective applications include screen kites, filters, ropes, nets, fish nets, computer ribbons, printed circuit board bases, paper canvases, air bags, airships, dome bases, rider suits, fishing lines, various lines (Yachts, paragliders, balloons, kites), blind cords, support cords for screen doors, various cords for automobiles and aircraft, power transmission cords for electrical products and robots, etc. Among them, monofilaments to be used are mentioned, and among them, there is a strong demand for high strength, high elastic modulus and fineness, and it is most suitable for filters that require abrasion resistance for improving weaving properties and fabric quality, and monofilaments for screen wrinkles.

  The polymerization method of the liquid crystalline polyester used in the present invention can be produced according to a known production method, for example, hydroxycarboxylic acid such as p-hydroxybenzoic acid and aromatic dihydroxy compound such as 4,4′-dihydroxybiphenyl and hydroquinone and terephthalic acid. It is preferable to produce a liquid crystalline polyester by a deacetic acid polycondensation reaction after reacting an aromatic dicarboxylic acid such as isophthalic acid with acetic anhydride to acylate the phenolic hydroxyl group.

  At this time, the total amount of aromatic dihydroxy compounds such as 4,4'-dihydroxybiphenyl and hydroquinone and the total amount of aromatic dicarboxylic acids such as terephthalic acid and isophthalic acid are preferably equimolar. The amount of acetic anhydride used is such that the total of the phenolic hydroxyl groups of p-hydroxybenzoic acid, 4,4′-dihydroxybiphenyl and hydroquinone is preferably 1.20 equivalents or less, and preferably 1.10 equivalents or less. More preferably, the lower limit is preferably 1.00 equivalent or more.

  When the obtained polymer is discharged onto a strand and pelletized using a rotary cutter, it is a preferable embodiment because handling in a drying process, a transport process, and an extrusion process becomes easy.

  The obtained liquid crystalline polyester pellets are vacuum dried at a temperature not exceeding the crystallization temperature to remove moisture to 500 ppm or less, and then subjected to melt spinning. Here, the crystallization temperature is a temperature of an exothermic peak observed in a temperature rising process when differential scanning calorimetry is performed under the conditions of a sample amount of 10 mg and 50 ° C. to 20 ° C./min.

  The melt spinning temperature is preferably set to a melting point of the liquid crystalline polyester + 10 ° C. or higher, and the resin is spun while securing the fluidity of the resin, and then cooled and supplied with oil.

  Thereafter, the liquid crystalline polyester fiber is preferably subjected to solid phase polymerization for the purpose of enhancing the mechanical properties of the fiber. The temperature of the solid-phase polymerization starts from room temperature, and when the temperature is gradually increased to a temperature of melting point (Tm) −10 ° C. or lower observed in the fiber after the solid-phase polymerization, the mechanical properties of the fiber are changed. This is a preferable mode because it can be sufficiently increased and fusion can be prevented.

  The solid phase polymerization time is preferably longer for the purpose of improving the mechanical properties of the fiber, but on the other hand, shorter time is preferable for productivity, and if it is in the range of 10 to 50 hours, sufficient mechanical properties are obtained. Can be increased.

  In the method for producing a liquid crystalline polyester fiber of the present invention, the endothermic peak temperature (Tm) + 10 ° C. observed in the differential scanning calorimetry of the fiber comprising the liquid crystalline polyester under the conditions of a sample amount of 10 mg and 50 ° C. to 20 ° C./min. It is important to heat-treat at the above temperature. In addition, Tm said here points out the value calculated | required by the measuring method of an Example description. Although Tm is the melting point of the fiber, the wear resistance is greatly improved by subjecting the liquid crystalline polyester fiber to a heat treatment at a high temperature of the melting point + 10 ° C. or higher, and the effect becomes remarkable when the single fiber fineness is small. In the case of a general crystalline polymer (for example, polyethylene terephthalate), when the heat treatment is carried out beyond the temperature at which crystal melting occurs, the disordered molecular chains move apart and flow. Can not keep the fiber form.

  However, in the case of the liquid crystalline polyester suitably used in the present invention, the liquid crystal state maintains molecular orientation even at a temperature higher than the crystal melting temperature, so that it does not become a complete disordered state, and heat treatment at such a high temperature is possible. It is. The higher the heat treatment temperature, the higher the thermal efficiency, so that the heater length can be shortened and the production cost can be kept low.

  On the other hand, the upper limit of the heat treatment temperature is not particularly limited, but the fiber surface may be oxidatively decomposed, and if the temperature is too high, the heater may be soiled or broken. In addition, a large amount of energy is required to maintain it at high temperatures, and the upper limit is set to about 500 ° C in order to improve productivity from the viewpoint of energy saving because the fibers are too soft and process stability is impaired. It is preferable to do. From these viewpoints, the range of the heat treatment temperature is preferably Tm + 50 ° C. or more and 500 ° C. or less, more preferably Tm + 80 ° C. or more and 500 ° C. or less, and most preferably Tm + 100 ° C. or more and 500 ° C. or less.

  The heat treatment is performed while continuously running the fibers for the purpose of performing the treatment uniformly and preventing fusion between the fibers.

  At this time, non-contact heat treatment is preferably performed in order to prevent generation of fibrils and perform uniform treatment. Heating means include atmospheric heating, radiant heating using laser and infrared rays, etc. Heating by slit heater using block or plate heater has both effects of atmospheric heating and radiant heating, and processing stability It is preferable because it increases.

  If the treatment time is too short, crystal melting does not proceed sufficiently and the fibril hierarchical structure is not obscured and improvement in wear resistance is not achieved. Therefore, the treatment time is set to be 0.01 seconds or longer. If the treatment time is long, the orientation of the molecular chain is too relaxed and the strength and elastic modulus are lowered, so 5.0 seconds or less is preferable, and 2.0 seconds or less is more preferable.

  Since the higher the processing speed, the higher the productivity, the processing speed is 10 m / min or more. The treatment speed is appropriately changed depending on the heater length and the heating method, but it is preferable to set the heat treatment time so as not to exceed a desired range.

  Furthermore, it is important that the subsequently heat-treated fiber is wound after forced cooling using a fluid within 0.05 seconds. By freezing the structure by forcibly cooling the crystal of the liquid crystalline polyester in an advanced state, it is possible to widen the crystal plane spacing, obscure the fibril hierarchical structure, and dramatically improve the abrasion resistance of the fiber. . Fibers with reduced crystallinity are generally considered to have inferior mechanical properties (strength, elastic modulus), but liquid crystalline polyester has a very high molecular weight, so even if the crystal order is lost, liquid crystalline The molecular orientation is hardly relaxed in order to maintain the mechanical properties, while maintaining the mechanical properties, eliminating the structural difference between the crystal and the amorphous in the cross section, that is, by making the fibril hierarchical structure indistinct, the wear resistance is dramatically improved. Can be improved.

  However, when cooling after heat treatment is performed in an air atmosphere that does not actively flow at room temperature, the fibers are gradually cooled, so that crystallization proceeds again in the process (cold crystallization), and the fibril hierarchical structure Becomes clear again and wear resistance deteriorates. Therefore, in order to obtain a fiber structure that is not crystallized, it is important to freeze the structure by rapidly and forcibly cooling the fiber in the molten state (liquid crystal state).

  Forced cooling as used herein refers to lowering the temperature faster than cooling in an atmosphere in which room temperature air is not actively stirred by forcibly contacting or spraying the fluid after heat treatment. .

  The method of forced cooling is not particularly limited, but since liquid crystalline polyester fibers are vulnerable to abrasion, a method of imparting or contacting a liquid or gas to the fibers can keep the abrasion resistance of the fibers low, reducing the abrasion of the fibers. This is a preferred mode for suppressing.

  Since the temperature of the fluid is intended to effectively lower the temperature of the traveling fiber to the cold crystallization temperature (Tc) or less, it is important that the temperature is lower than the cold crystallization temperature. It is preferable to perform cooling at the following temperature.

  An apparatus for performing forced cooling is not particularly limited, but when the length of the fluid discharge port in the fiber running direction is 10 mm or less, the fluid can be contacted or sprayed in a limited range, and the process design can be performed. It is easy to obtain the effect of forced cooling.

  As an application method, any method such as a direct contact method using a nozzle or a spraying method can be adopted. Particularly, when the fluid is a liquid, a method of applying and contacting the liquid using an oil supply nozzle is preferable. It is also preferable to use a rectangular nozzle in order to perform forced cooling simultaneously on a large number of weights.

  The fluid used for forced cooling is preferably a gas because extra substances hardly adhere to the fibers. Although the kind of gas is not specifically limited, Air and nitrogen gas are used suitably. Nitrogen gas is preferred because it can prevent oxidative degradation of the fiber surface during forced cooling. On the other hand, it is preferable to use air as the gas because it is possible to perform forced cooling stably at low cost and there is no fear of suffocation. As the gas, it is more preferable to select air because it is cheap and safe to work.

  The gas flow rate is preferably 500 times or more the volume per unit time of the fiber traveling in the heat treatment heater. In general, the specific heat of a gas is smaller than that of a liquid or solid, so that the effect of forced cooling can be exhibited by sufficiently increasing the flow rate. Moreover, since the flow rate also leads to an increase in production cost, the smaller the flow rate, the more inexpensive the fiber can be produced, which is preferable. Therefore, the gas flow rate is preferably 500 times or more and 10,000 times or less, and more preferably 1000 times or more and 5000 times or less.

  It is preferable to select a liquid as the fluid used for forced cooling because the specific heat is large with respect to the gas and cooling can be effectively performed with a small amount. Although the kind of liquid is not specifically limited, Water, silicone oil, etc. can be used. Among these, water is preferable because it has a high specific heat, is inexpensive, and can be stably supplied.

  It is also preferable that the oil contains an oil component as long as the effects of the invention are not impaired. As oils, known ones can be used, but mineral oils, smoothing agents such as esters, polyethers, silicones, emulsifiers such as ether compounds, anionic, cationic and nonionic antistatic agents, synthetic ester waxes, etc. The oil agent which mix | blended components, such as water resistance improver, can be illustrated.

  If the oil component is contained in an amount of 50% by weight or less based on water, both the effect of forced cooling and the effect of oil agent application can be obtained. If the oil component is an emulsion, a uniform film is formed on the fiber. It is easy and particularly suitable.

  In addition, when the fiber is dried using air, nitrogen, or the like after the liquid is applied, it is preferable because the oil agent can uniformly adhere to the fiber in the subsequent oil supply step. As a specific example, the efficiency of the additional oil before winding can be improved by drying and removing the liquid adhering to the fiber using an air nozzle or the like.

  The flow rate of the liquid supplied in the present invention is preferably 0.5 times or more with respect to the volume per unit time of the traveling fiber. The liquid applied at a flow rate of 0.5 times or more can effectively forcibly cool the fibers. On the other hand, the flow rate is preferably small from the viewpoint of productivity and from the viewpoint of process passage. The range in which these are compatible is more preferably from 0.5 times to 10 times, and most preferably from 0.7 times to 5 times.

  It is a desirable embodiment to replenish the process oil after the forced cooling of the present invention. In the heat treatment, as described above, it is not preferable that the oil content is too much. Therefore, the fiber to be subjected to the heat treatment is attached with an oil content of the minimum required amount, and after the heat treatment, the process passability after the next step, and further the loom In order to improve productivity, it is preferable to attach an oil for improving the weaving property. It is also a preferred aspect that this process oil replenishment is performed simultaneously with the forced cooling of the present invention.

  EXAMPLES Hereinafter, although an Example demonstrates this invention in detail, this invention is not limited at all by this. The various characteristics of the present invention were evaluated by the following methods.

(1) Single fiber fineness and fineness variation rate 10 m of fiber is taken with a measuring machine, the weight (g) is multiplied by 1000, 10 measurements are performed per sample, and the average value is the fineness (dtex) It was. The quotient obtained by dividing this by the number of filaments was defined as the single fiber fineness (dtex). The fineness variation rate was calculated by the following equation using the larger value of the absolute values of the differences between the maximum and minimum values from the average value of 10 finenesses.

Fineness fluctuation rate (%) = ((| maximum value or minimum value−average value | / average value) × 100)
(2) Strength, elongation, elastic modulus and strength variation rate According to the method described in JIS L1013: 1999, one sample using Tensilon UCT-100 manufactured by Orientec under the conditions of a sample length of 100 mm and a tensile speed of 50 mm / min. The measurement was performed 10 times per average, and the average value was defined as strength (cN), strength (cN / dtex), elongation (%), and elastic modulus (cN / dtex). The strength fluctuation rate was calculated by the following formula using the larger one of the absolute values of the differences between the maximum and minimum values from the average value of 10 strengths.

Strong fluctuation rate (%) = ((| maximum or minimum value−average value | / average value) × 100)
(3) Tm, peak half-width at Tm, ΔHm
Differential scanning calorimetry is performed with a DSC2920 manufactured by TA instruments, and the endothermic peak temperature observed when the sample amount is 10 mg and the temperature is measured under a temperature rising condition of 50 ° C. to 20 ° C./min is Tm (° C.). The half width (° C.) and the heat of fusion (ΔHm) (J / g) were measured.

(4) Wide-angle X-ray diffraction peak half-width (WAXD half-width)
A sample was cut into a length of 4 cm, and 20 mg of the sample was weighed to obtain a measurement sample. A 4036A2 type manufactured by Rigaku Corporation was used as the X-ray generator, a CuKα ray using a Ni filter as the X-ray source, and an output of 40 kV and 20 mA were used. As the goniometer, model 2155D manufactured by Rigaku Corporation was used, slit 2 mmφ-1 ° -1 °, and the detector was a scintillation counter. RAD-C type manufactured by Rigaku Corporation was used for the counting recording device. Scanned by the transmission method in 0.05 second increments from 5 to 60 ° in the equator line direction with an integration time of 2 seconds, and half of the obtained profile has a maximum in the range of 18 to 22 °. The width of the peak in intensity was taken as the half width.

(5) Wide-angle X-ray diffraction crystal orientation degree The angle in the equator line direction at the maximum value of the peak obtained in (4) is fixed, and the azimuth angle (circumferential direction) is 0.5 ° step, integrated time 2 From the profile obtained by scanning the range of 90 to 270 ° per second with the transmission method, the peak width at half the maximum value was taken as Δβ. The crystal orientation degree π was calculated from the obtained Δβ using the following formula.
π = (180−Δβ) / 180
(6) Wear resistance M
A fiber rod loaded with a load of 2.5 g / dtex is hung vertically, and a hard chrome satin-finished metal rod guide (bar guide manufactured by Yuasa Yindo Kogyo Co., Ltd.) with a diameter of 3.8 mm is perpendicular to the fiber. Pressing at a contact angle of 2.7 °, rubbing the fiber in the fiber axis direction at a stroke length of 30 mm and a stroke speed of 600 times / minute, and taking the time to confirm the occurrence of white powder or fibrils on the rod guide or on the fiber surface The average value of five times excluding the maximum value and the minimum value among the seven times of measurement was obtained and defined as wear resistance.

(7) Weaving properties (number of stops), fabric quality (number of fibrils)
Using a 13 dtex polyester monofilament for the warp with a rapier loom, weaving the weft as a liquid crystalline polyester fiber obtained in the examples of the present invention with a weaving density of both wefts and wefts of 100 / inch (2.54 cm). Went. At this time, weaving property was evaluated from the number of times of stoppage due to fibril deposition on the yarn feeder in a trial weaving having a width of 180 cm and a length of 10 m. . Further, the quality of the fabric was evaluated from the number of fibrils mixed in the fabric, and 2 or less per 10 m length was judged as good (◯) and 3 or more as bad (x).

Reference example 1
In a 5 L reaction vessel equipped with a stirring blade and a distillation tube, 860 parts by weight of p-hydroxybenzoic acid, 320 parts by weight of 4,4′-dihydroxybiphenyl, 91 parts by weight of hydroquinone, 296 parts by weight of terephthalic acid, 157 parts by weight of isophthalic acid Then, 1433 parts by weight of acetic anhydride (1.08 equivalent of the total phenolic hydroxyl groups) was added, and the temperature was raised from room temperature to 145 ° C. over 30 minutes with stirring in a nitrogen gas atmosphere, followed by reaction at 145 ° C. for 2 hours. Then, it heated up to 330 degreeC in 4 hours.

  The polymerization temperature was maintained at 330 ° C., the pressure was reduced to 133 Pa in 1.5 hours, and the reaction was continued for another 20 minutes. When the torque reached 15 kgcm, the polycondensation was completed. Next, the inside of the reaction vessel was pressurized to 0.1 MPa, the polymer was discharged to a strand through a die having one circular discharge port having a diameter of 10 mm, and pelletized by a cutter.

  The obtained liquid crystalline polyester had a melting point of 320 ° C., a molecular weight of 89,000, and a melt viscosity of 15 Pa · s at a shear rate of 100 sec-1.

Example 1
Using the liquid crystalline polyester of Reference Example 1, after vacuum drying at 160 ° C. for 12 hours, it was melt extruded with a φ15 mm single screw extruder (heater temperature 290 to 340 ° C.) manufactured by Osaka Seiki Machine Co., Ltd. The polymer was supplied to the spin pack while weighing. The spinning temperature from the extruder to the spinning pack at this time was 345 ° C. In the spinning pack, a polymer is filtered using a metal nonwoven fabric filter (WLF-10 manufactured by Watanabe Yoshikazu Co., Ltd.), and the discharge amount is 3.0 g from a die having five holes having a hole diameter of 0.13 mm and a land length of 0.26 mm.
The polymer was discharged at a rate of 0.6 g / min (0.6 g / min per single hole).

  The discharged polymer is allowed to pass through a 40 mm heat-retaining region, and then cooled and solidified from the outside of the yarn with an annular cooling air. Thereafter, an oil containing polydimethylsiloxane as a main component is applied, and all the 5 filaments are 1200 m / min. I took it to 1 godet roll. The spinning draft at this time is 32. After passing this through the second godet roll at the same speed, four of the five filaments are sucked with a suction gun, and the remaining one is passed through a dancer arm with a pirn winder (no contact roll contacting the winding package). Used to wind up in the shape of a pan. During the winding time of about 100 minutes, yarn breakage did not occur and the yarn making property was good. The oil adhesion amount was 1.0% by weight.

A winding machine (ET-68S controlled winding by Kozu Seisakusho Co., Ltd.) that unwinds fibers from the spun fiber package in the longitudinal direction (perpendicular to the fiber circulation direction) and keeps the speed constant without using a speed control roller. Machine). As the core material for rewinding, a stainless steel perforated bobbin wound with Kevlar felt (weight per unit: 280 g / m ² , thickness 1.5 mm), the tension at the time of rewinding was 0.05 cN / dtex, and the winding amount was It was 20,000 m. Further, the package form is a taper end winding with a taper angle of 20 °, and the traverse width is always swung by remodeling the taper width adjusting mechanism. The winding density of the package wound up in this way was 0.08 g / cm ³ .

  This was heated in a closed oven from room temperature to 240 ° C. in about 30 minutes, held at 240 ° C. for 3 hours, then heated to 295 ° C. at 4 ° C./hour, and further at 295 ° C. for 15 hours. Solid state polymerization was carried out under the conditions maintained. The atmosphere was supplied with dehumidified nitrogen at a flow rate of 25 NL / min, and exhausted from the exhaust port so that the interior was not pressurized.

  The solid phase polymerization package thus obtained is attached to a feeding device that can be rotated by an inverter motor, and a winder (ET type manufactured by Kozu Seisakusho Co., Ltd.) is fed while feeding the fibers in the transverse direction (fiber circumferential direction) at a yarn feeding speed of about 100 m / min. Winding up with a fast winder). Table 2 shows the physical properties of the obtained liquid crystalline polyester fiber. In addition, when Δn of this liquid crystalline polyester fiber was measured by the compensator method, it was 0.345 and had a high orientation. The physical properties of the fiber were a fineness of 5.0 dTex, a fineness fluctuation rate of 4.0%, a strength of 26.4 cN / dTex, a strength fluctuation rate of 5.0%, an elongation of 2.5%, and an elastic modulus of 1010 cN / dTex. It was. The heat of fusion ΔHm was measured and found to be 8.6 J / g.

  Using a slit heater with a slit width of 5.6 mm and a length of 1000 mm while unwinding this fiber in the longitudinal direction (perpendicular to the fiber circulation direction), the fiber was run without contacting the heater and at 485 ° C. After a heat treatment, a fiber emulsion containing a water emulsion containing 1% by weight of an oil component mainly composed of a fatty acid ester is fed from a ceramic oiling guide having a nozzle diameter of 1 mmφ at a position 10 mm from the heater outlet at a flow rate of 0.1 cc / min. The solution was supplied and contacted from the lower side and forcedly cooled. Then, after passing through a take-up roller, it was taken up with a take-up machine (ET-type controlled take-up machine manufactured by Kozu Seisakusho).

  Table 1 shows main production conditions and physical property values of the obtained fiber. The resulting fiber showed good mechanical properties. Δn was 0.345, which was the same value as before heat treatment. Further, from the analysis results in wide-angle X-ray diffraction, the half-value width is 5.1 °, the crystal plane spacing is very disordered, and the crystal orientation degree π is 0.82, which is sufficient for crystal Since the structure was disordered, the wear resistance was excellent. In addition, as a result of the weaving test, it was found that there was no stopping and no fibrils and excellent processability.

Examples 2-4
Liquid crystalline polyester fibers were obtained in the same manner as in Example 1 except that the forced cooling position was changed as shown in Table 1 and the time until forced cooling was changed. The physical property values of the obtained fibers are also shown in Table 1. The crystal plane spacing was sufficiently disordered, the crystal orientation was low, liquid crystalline polyester fibers excellent in abrasion resistance were obtained, and weaving could be performed without any problems.

Comparative Example 1
A liquid crystalline polyester fiber was obtained in the same manner as in Example 1 except that the forced cooling position was 200 mm and the time to forced cooling was 0.06 seconds. The physical property values of the obtained fiber are shown in Table 1. Since the disorder of the crystal plane spacing of the fiber was small and the degree of crystal orientation was high, the wear resistance was poor, and the number of stops in the weaving test was large. It was something that was occasionally seen.

Examples 5 and 6
Liquid crystalline polyester fibers were obtained in the same manner as in Example 1 except that the amount of fluid discharged was changed and the flow rate was changed in proportion to the volume per unit time of the fibers. The obtained fiber had good abrasion resistance and mechanical properties, and showed good processability in the weaving test.

Example 7
A liquid crystalline polyester fiber was obtained in the same manner as in Example 1 except that the heat treatment temperature was 440 ° C. The obtained fiber had good abrasion resistance and mechanical properties, and the weaving test showed a process-passing property with no problem.

Comparative Example 2
A liquid crystalline polyester fiber was obtained in the same manner as in Example 1 except that the heat treatment temperature was 300 ° C. Although the mechanical properties of the obtained fiber were good, the disorder of the crystal plane spacing was small, the wear resistance was poor, and the process passability in the weaving test was poor.

Examples 8 and 9
Liquid crystalline polyester fibers were obtained in the same manner as in Example 1 except that air and nitrogen were used for forced cooling, an air nozzle having a diameter of 6 mmφ was used as the nozzle, and the discharge rate was 120 cc / min. The obtained fiber had good mechanical properties and excellent wear resistance, and showed excellent process passability in the weaving test.

Examples 10-12
Liquid crystalline polyester fibers were obtained in the same manner as in Example 12 except that air was used as the fluid and the amount of fluid discharged was changed to the conditions shown in Table 5. The obtained fiber showed good mechanical properties and abrasion resistance, and also showed good processability in the weaving test.

Example 13
Liquid crystalline polyester fibers were obtained in the same manner as in Example 8 except that air was used as the fluid and the heat treatment temperature was changed to 440 ° C. The obtained fiber had good mechanical properties, fiber structure, and abrasion resistance, and exhibited a process passability that was not a problem in the weaving test.

Comparative Example 3
Liquid crystalline polyester fibers were obtained in the same manner as in Example 8 except that air was used as the fluid and the heat treatment temperature was changed to 300 ° C. The obtained fiber showed good mechanical properties, but the crystal plane spacing was not sufficiently disturbed, the wear resistance was poor, and the processability in the weaving test was also poor.

Examples 14-16
Liquid crystalline polyester fibers were obtained in the same manner as in Example 8 except that the positions until forced cooling were changed to the conditions shown in Table 7. The obtained fiber showed good mechanical properties, fiber structure and abrasion resistance, and also showed good processability in the weaving test.

Comparative Example 4
A liquid crystalline polyester fiber was obtained in the same manner as in Example 8 except that the forced cooling position was 200 mm and the time until forced cooling was 0.06 seconds. Although the obtained fiber showed good mechanical properties, the disorder of the crystal plane spacing was insufficient, the abrasion resistance was inferior, and the processability was poor in the weaving test.

Comparative Example 5
Liquid crystalline polyester fibers were obtained in the same manner as in Example 1, except that forced cooling was not performed, the heat treatment temperature was 520 ° C., the heater length was 500 mm, the treatment speed was 500 m / min, and the heat treatment time was 0.06 seconds. The temperature in the heat treatment process was too high, and the yarn fluctuated in the heater, and stable sampling could not be performed. Although the obtained small sample showed excellent abrasion resistance, a sample sufficient for weaving evaluation could not be obtained.

  The liquid crystalline polyester fiber of the present invention can greatly improve the wear resistance, which has been a conventional drawback, while maintaining the properties such as high mechanical strength and elastic modulus of the liquid crystalline polyester. It is possible to improve the process passability in the manufacturing process and supply a product with less wear deterioration in actual use.

Claims (6)

A liquid crystalline polyester fiber characterized in that, in wide-angle X-ray diffraction measurement using CuKα rays as a radiation source, the half-value width of a peak having a maximum at 18 to 22 ° in the equator direction is 3.5 ° or more. 2. The liquid crystalline polyester according to claim 1, wherein the endothermic peak area ΔHm observed in the differential scanning calorimetry under the conditions of a sample amount of 10 mg and 50 ° C. to 20 ° C./min is 3.0 J / g or less. fiber. The fiber made of liquid crystalline polyester was heat-treated at a temperature of endothermic peak temperature (Tm) + 10 ° C. or more observed in differential scanning calorimetry under the conditions of a sample amount of 10 mg and 50 ° C. to 20 ° C./min, and then 0.05 seconds A method for producing a liquid crystalline polyester fiber, which is wound after forced cooling is performed using a fluid. 4. The liquid crystalline polyester according to claim 3, wherein the heat treatment time is 0.01 seconds or more and 5.0 seconds or less, and the temperature of the fluid used for forced cooling is 100 ° C. or more lower than the cold crystallization temperature of the fibers. A method for producing fibers. The method for producing a liquid crystalline polyester fiber according to claim 3 or 4, wherein the fluid used for forced cooling is a gas and the flow rate thereof is 500 times or more the volume per unit time of the fiber. The method for producing a liquid crystalline polyester fiber according to claim 3 or 4, wherein the fluid used for forced cooling is a liquid, and the flow rate thereof is 0.5 times or more the volume per unit time of the fiber.