KR101858550B1 - Manufacturing method of high strength fiber and high strength fiber manufactured thereby - Google Patents

Manufacturing method of high strength fiber and high strength fiber manufactured thereby Download PDF

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KR101858550B1
KR101858550B1 KR1020160028742A KR20160028742A KR101858550B1 KR 101858550 B1 KR101858550 B1 KR 101858550B1 KR 1020160028742 A KR1020160028742 A KR 1020160028742A KR 20160028742 A KR20160028742 A KR 20160028742A KR 101858550 B1 KR101858550 B1 KR 101858550B1
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South Korea
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fiber
heating
nozzle
fibers
spinning
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KR1020160028742A
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Korean (ko)
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KR20170105746A (en
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함완규
남인우
김도군
이주형
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한국생산기술연구원
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    • D—TEXTILES; PAPER
    • D01—NATURAL OR MAN-MADE THREADS OR FIBRES; SPINNING
    • D01D—MECHANICAL METHODS OR APPARATUS IN THE MANUFACTURE OF ARTIFICIAL FILAMENTS, THREADS, FIBRES, BRISTLES OR RIBBONS
    • D01D5/00—Formation of filaments, threads, or the like
    • D01D5/08—Melt spinning methods
    • D01D5/084—Heating filaments, threads or the like, leaving the spinnerettes
    • D—TEXTILES; PAPER
    • D01—NATURAL OR MAN-MADE THREADS OR FIBRES; SPINNING
    • D01D—MECHANICAL METHODS OR APPARATUS IN THE MANUFACTURE OF ARTIFICIAL FILAMENTS, THREADS, FIBRES, BRISTLES OR RIBBONS
    • D01D10/00—Physical treatment of artificial filaments or the like during manufacture, i.e. during a continuous production process before the filaments have been collected
    • D01D10/02—Heat treatment
    • D—TEXTILES; PAPER
    • D01—NATURAL OR MAN-MADE THREADS OR FIBRES; SPINNING
    • D01D—MECHANICAL METHODS OR APPARATUS IN THE MANUFACTURE OF ARTIFICIAL FILAMENTS, THREADS, FIBRES, BRISTLES OR RIBBONS
    • D01D5/00—Formation of filaments, threads, or the like
    • D01D5/08—Melt spinning methods
    • D01D5/088—Cooling filaments, threads or the like, leaving the spinnerettes
    • D—TEXTILES; PAPER
    • D01—NATURAL OR MAN-MADE THREADS OR FIBRES; SPINNING
    • D01D—MECHANICAL METHODS OR APPARATUS IN THE MANUFACTURE OF ARTIFICIAL FILAMENTS, THREADS, FIBRES, BRISTLES OR RIBBONS
    • D01D5/00—Formation of filaments, threads, or the like
    • D01D5/08—Melt spinning methods
    • D01D5/098—Melt spinning methods with simultaneous stretching
    • D—TEXTILES; PAPER
    • D01—NATURAL OR MAN-MADE THREADS OR FIBRES; SPINNING
    • D01D—MECHANICAL METHODS OR APPARATUS IN THE MANUFACTURE OF ARTIFICIAL FILAMENTS, THREADS, FIBRES, BRISTLES OR RIBBONS
    • D01D5/00—Formation of filaments, threads, or the like
    • D01D5/28—Formation of filaments, threads, or the like while mixing different spinning solutions or melts during the spinning operation; Spinnerette packs therefor
    • D01D5/30—Conjugate filaments; Spinnerette packs therefor
    • D—TEXTILES; PAPER
    • D01—NATURAL OR MAN-MADE THREADS OR FIBRES; SPINNING
    • D01D—MECHANICAL METHODS OR APPARATUS IN THE MANUFACTURE OF ARTIFICIAL FILAMENTS, THREADS, FIBRES, BRISTLES OR RIBBONS
    • D01D5/00—Formation of filaments, threads, or the like
    • D01D5/28—Formation of filaments, threads, or the like while mixing different spinning solutions or melts during the spinning operation; Spinnerette packs therefor
    • D01D5/30—Conjugate filaments; Spinnerette packs therefor
    • D01D5/32—Side-by-side structure; Spinnerette packs therefor
    • D—TEXTILES; PAPER
    • D01—NATURAL OR MAN-MADE THREADS OR FIBRES; SPINNING
    • D01D—MECHANICAL METHODS OR APPARATUS IN THE MANUFACTURE OF ARTIFICIAL FILAMENTS, THREADS, FIBRES, BRISTLES OR RIBBONS
    • D01D5/00—Formation of filaments, threads, or the like
    • D01D5/28—Formation of filaments, threads, or the like while mixing different spinning solutions or melts during the spinning operation; Spinnerette packs therefor
    • D01D5/30—Conjugate filaments; Spinnerette packs therefor
    • D01D5/34—Core-skin structure; Spinnerette packs therefor
    • D—TEXTILES; PAPER
    • D01—NATURAL OR MAN-MADE THREADS OR FIBRES; SPINNING
    • D01F—CHEMICAL FEATURES IN THE MANUFACTURE OF ARTIFICIAL FILAMENTS, THREADS, FIBRES, BRISTLES OR RIBBONS; APPARATUS SPECIALLY ADAPTED FOR THE MANUFACTURE OF CARBON FILAMENTS
    • D01F8/00—Conjugated, i.e. bi- or multicomponent, artificial filaments or the like; Manufacture thereof
    • D01F8/04—Conjugated, i.e. bi- or multicomponent, artificial filaments or the like; Manufacture thereof from synthetic polymers
    • D01F8/06—Conjugated, i.e. bi- or multicomponent, artificial filaments or the like; Manufacture thereof from synthetic polymers with at least one polyolefin as constituent
    • D—TEXTILES; PAPER
    • D01—NATURAL OR MAN-MADE THREADS OR FIBRES; SPINNING
    • D01F—CHEMICAL FEATURES IN THE MANUFACTURE OF ARTIFICIAL FILAMENTS, THREADS, FIBRES, BRISTLES OR RIBBONS; APPARATUS SPECIALLY ADAPTED FOR THE MANUFACTURE OF CARBON FILAMENTS
    • D01F8/00—Conjugated, i.e. bi- or multicomponent, artificial filaments or the like; Manufacture thereof
    • D01F8/04—Conjugated, i.e. bi- or multicomponent, artificial filaments or the like; Manufacture thereof from synthetic polymers
    • D01F8/12—Conjugated, i.e. bi- or multicomponent, artificial filaments or the like; Manufacture thereof from synthetic polymers with at least one polyamide as constituent
    • D—TEXTILES; PAPER
    • D01—NATURAL OR MAN-MADE THREADS OR FIBRES; SPINNING
    • D01F—CHEMICAL FEATURES IN THE MANUFACTURE OF ARTIFICIAL FILAMENTS, THREADS, FIBRES, BRISTLES OR RIBBONS; APPARATUS SPECIALLY ADAPTED FOR THE MANUFACTURE OF CARBON FILAMENTS
    • D01F8/00—Conjugated, i.e. bi- or multicomponent, artificial filaments or the like; Manufacture thereof
    • D01F8/04—Conjugated, i.e. bi- or multicomponent, artificial filaments or the like; Manufacture thereof from synthetic polymers
    • D01F8/14—Conjugated, i.e. bi- or multicomponent, artificial filaments or the like; Manufacture thereof from synthetic polymers with at least one polyester as constituent
    • D—TEXTILES; PAPER
    • D10—INDEXING SCHEME ASSOCIATED WITH SUBLASSES OF SECTION D, RELATING TO TEXTILES
    • D10B—INDEXING SCHEME ASSOCIATED WITH SUBLASSES OF SECTION D, RELATING TO TEXTILES
    • D10B2401/00—Physical properties
    • D10B2401/06—Load-responsive characteristics
    • D10B2401/063—Load-responsive characteristics high strength

Abstract

The present invention relates to a process for producing high-strength synthetic fibers and high-strength synthetic fibers produced therefrom.
The present invention optimizes the local heating method when spinning in a melt spinning process, while indirectly heating the high heat transfer uniformly to all the fibers that are radiated directly under the spinneret, and in particular, By optimizing the heat transfer method by double heating the fibers directly under the nozzle, the molecular chain entanglement structure in the melt phase polymer is controlled by the direct local high temperature heating to improve the stretchability and to enhance the stretchability of the spun fibers, And the mechanical properties such as strength and elongation of the obtained fibers are improved. In addition, the manufacturing method of the present invention improves the mechanical properties while utilizing the existing spinning nozzle design and the conventional processes of the melt spinning process and the stretching process, so that high-performance fibers can be mass-produced at low cost.

Description

TECHNICAL FIELD [0001] The present invention relates to a method for producing a high strength synthetic fiber and a high strength synthetic fiber produced therefrom,

The present invention relates to a method for producing a high strength synthetic fiber and a high strength synthetic fiber produced therefrom. More particularly, the present invention relates to a method for producing a high strength synthetic fiber, The temperature is raised to a temperature higher than the pack body temperature for a short period of time in which no thermal decomposition occurs and locally heated to effectively control the molecular chain entanglement structure in the polymer without lowering the molecular weight to improve the stretchability, Strength synthetic fiber which can improve the mechanical properties such as strength and elongation and improve the mechanical properties while utilizing the existing spinning nozzle design, melt spinning process and stretching process, and can produce high-performance fibers at low cost And a high-strength synthetic fiber produced therefrom .

The maximum known strength of commercially available PET products to date is 1.1 GPa, and compared to the high strength fibers (extreme performance para-aramid (Kevlar) fiber 2.9 GPa) / 3 level, which is 3 to 4%. Accordingly, there is a limit to apply to industrial textile materials which require extreme performance, except for general clothing, living or industrial (tire cord) fiber materials.

As described above, PET and nylon-based fibers, which are non-liquid crystalline thermoplastic fibers, have lower strength than PBO (xylon, Zylon) and para-aramid (Kevlar) fibers, which are liquid crystal polymer , Since the behavior of the structure formation is different when the resin is processed into a fibrous form.

That is, since the liquid crystal polymer (LCP) forms a liquid crystal phase structure in a solution state, if a proper shear stress is applied, a fiber structure having a very high degree of orientation and crystallinity due to a small entropy difference in fiber structure before and after spinning is formed, .

On the other hand, since PET and nylon-based non-liquid crystalline thermoplastic polymers have a complicated structure in which polymer chains are intertwined with amorphous random coils in a molten state, a high shear stress and a subsequent stretching ratio (draft and elongation ratio, etc.) There is a problem that complete orientation crystallization (high strength) is relatively difficult due to the structure entangled with random coils. At this time, there is a large difference between entropy of fiber structure before and after spinning.

On the other hand, if the relatively high strength PET fiber can be developed in spite of the structural disadvantage of the general thermoplastic polymer, since the application market and the ripple effect are very large, Various studies are being carried out to maximize the physical properties and to raise the limit performance.

For example, as a research to produce high strength PET fiber, it is known to use ultra high molecular weight PET resin [Ziabicki, A., "Effect of Molecular Weight on Melt Spinning and Mechanical Properties of High-Performance Poly (ethylene terephthalate) Fibers" Text. Res. J., 1996, 66, 705-712; 2. Uniaxial and Biaxial Extensional Flow ", Macromol., 2001, 34, 6056-6063), solidification of melt spinning Drawn Poly (ethylene terephthalate) ", Polymer, 1990, 31, 58-63], which is a study to maximize orientation by applying bath technology [Ito M., et al., "Effect of Sample Geometry and Drawing Conditions on Mechanical Properties of Drawn Poly Are reported.

However, considering the fact that the above studies are a laboratory scale approach for developing high strength PET fibers, commercialization has not been achieved due to limitations of workability and productivity compared to the effect of improving physical properties.

In recent years, in Japan, research and development have been made on using conventional thermoplastic polymers such as PET and nylon to increase the strength of existing fibers from 1.1GPa to 2GPa within a range that does not increase the manufacturing cost more than twice based on the melt spinning process have.

In addition, melt-structure control technology, molecular weight control technology, stretching / heat treatment technology, and evaluation / analysis technology are applied to the research and development fields that are finally applied to tire cords, which are the most consumed as industrial fibers, .

In particular, unlike a conventional melt-structure control technique that controls the formation behavior of a fiber structure through the molecular orientation and crystallization of a solidified fiber, a molecular entanglement in the melt phase polymer, And the structure control and behavior of non-oriented amorphous fiber are investigated to achieve high strength of PET fiber.

Accordingly, as a means for controlling the molecular structure in the melt spinning process, development of high strength PET fiber has been reported through spinning nozzle design, laser heating, supercritical gas, and coagulation bath.

In particular, the conventional melt spinning process when the nozzle near to provide a high-strength PET fiber by means of a spinning nozzle designed as an example of the method for local heating, Fig. 7 is an embodiment of the local heating by the direct thermal insulation method of the spinning nozzle 8 Sectional view taken along the line III-III in the embodiment of the direct lowering method of the spinning nozzle.

Specifically, in the melt spinning process, the spinning nozzle 100 is fixed to the pack body 200 held from the pack body heater 300 provided with a heat source of 100 to 350 캜, and after the spinning, the multi- C. By passing the high-temperature electric heater through the annealing heater unit 400 of 20 to 200 mm so as to uniformly apply the high-temperature electric heater at a constant distance, heat transfer of high efficiency can be performed at a lower cost.

However, the local heating of the fibers by the annealing heater 400 is not for heating purposes but for maintaining a uniform temperature between the lower holes of the nozzle. In order to minimize the temperature deviation between the holes, And the distance between the fibers and the heater is long and uniform heating is not applied to the fibers.

As another method of locally heating the vicinity of the nozzle in the conventional melt spinning process, the hole diameter of the spinneret is miniaturized and the CO 2 laser is irradiated right under the spinneret, so that the PET fiber strength after stretching is 1.68 GPa (13.7 g / (Masuda, M., "Effect of Controlling Polymer Flow on Mechanical Properties of Poly (ethylene terephthalate) Fibers ", Intern. Polymer Processing, 2010, 25, 159-169].

FIG. 9 shows an embodiment of local heating by laser irradiation directly under a spinning nozzle, and FIG. 10 shows a cutting sectional view taken along the line IV-IV in the above embodiment.

Specifically, after spinning multi-filament 112 to the CO 2 laser irradiation part 410, the bottom of the CO 2 laser with a spinning nozzle 100, the lower the pack body 200, in such a way that direct heating by irradiation from 1 to 3 Mm, and a CO 2 laser is irradiated at a position of 1 to 10 mm immediately after irradiation.

However, the laser heating directly under the spinning nozzle has a feature of heating a specific fiber portion to a high temperature, but there is a limit to be applied to an actual commercialized spinning nozzle having dozens to tens of thousands of holes at the same time.

The present inventors have made efforts to improve the conventional problems of the method of manufacturing high strength synthetic fibers. As a result, the present inventors have found that by optimizing the heat transfer method by heating the fibers in the vicinity of the hole of the spinning nozzle and directly under the spinning nozzle, The temperature was elevated to a temperature higher than the pack body temperature for a short time without pyrolysis and locally heated to effectively control the molecular chain entanglement structure in the polymer without deteriorating the molecular weight to confirm the improvement of the mechanical properties such as the strength and elongation of the synthetic fiber, Thereby completing the invention.

It is an object of the present invention to provide a method of manufacturing a high strength synthetic fiber by optimizing an instantaneous local heating method of a spinning nozzle upon spinning in a melt spinning process.

Another object of the present invention is to provide a high strength synthetic fiber having improved strength and elongation through the above-described production method.

The thermoplastic polymer is melt-spun through a spinneret containing at least one spinneret to form fibers and the fibers of the melt are passed through a heating zone (40, 80) disposed directly beneath spinning nozzles (10, 50) (41a, 81a) or belt-like type (41b, 41b) in the peripheral portion of the spinning nozzle hole, the heating zone (40, 80) 81b to heat the fibers locally. The present invention also provides a method for producing high-strength synthetic fibers.

Examples of preferred thermoplastic polymers for use in the present invention include polyethylene terephthalate (PET), polybutylene terephthalate (PBT), polytrimethylene terephthalate (PTT), polycyclohexanedimethanol terephthalate (PCT), and A polyester-based polymer selected from the group consisting of polyethylene naphthalate (PEN); Polyamide-based polymers selected from nylon 6, nylon 6,6, nylon 4, and nylon 4,6; Or a polyolefin-based polymer selected from polyethylene or polypropylene; . ≪ / RTI >

In this manufacturing method, the molten-phase fibers pass through the heating bodies (41, 81) maintained at a temperature elevation condition higher than the pack body temperature (20, 60), wherein the temperature of the heating bodies (41, 81) The temperature difference relative to the temperature is provided at 0 to 1,500 ° C or more. Also, the temperature of the pack bodies 20 and 60 is maintained at 50 to 400 캜.

The fibers are passed through a heating body of a hole-type die 41a, 81a having holes formed so as to be spaced from the center of the spinneret hole by 1 to 300 mm or less. At this time, the heating body of the hole-type die 41a, Lt; RTI ID = 0.0 > 360 < / RTI >

When the fibers are formed with a plurality of holes having the same radius from the spinning nozzle center hole, the heating elements of the belt-shaped types 41b and 81b, which are inserted between the neighboring hole- . At this time, the heating elements of the band-type molds 41b and 81b are inserted so that the distance between the hole-holes is 180 degrees within a range of 1 to 300 m from the hole center of the spinning nozzle.

In the heating zone 40 according to the first preferred embodiment of the present invention, the heat insulating material layer 43 and the heating body extend from 1 to 500 mm in length from the heat insulating material layer within 1 to 30 mm on the lower side of the spinning nozzle, And a heating zone of the fiber including an extension length of the heating body. Thus, the thermoplastic polymer in a molten state immediately after spinning is indirectly heated (e.g., radiant).

The heating zone 80 of the second preferred embodiment of the present invention has a nozzle body 52 located at -50 (entering the pack body) to 300 mm (emerging into the pack body) And an extension length of the heating body extending from the lower portion of the nozzle body 52 is 0.1 to 50 mm (b2) (B3), a depth of insertion of the heating body partially inserted into the lower portion of the nozzle body, and an extension length of the heating body extending from the lower portion of the nozzle body.

The melted polymer is first directly heated (for example, conducted) in the vicinity of the hole in the spinning nozzle through the heating zone 80 of the second embodiment, and then, by the elongated formed heating body, (For example, radiation) of the thermoplastic polymer in a molten state discharged before the solidification step.

In the second embodiment, when the vicinity of the hole is directly or indirectly heated to the lower portion of the spinning nozzle, the deterioration of the molten polymer in the holes 11 and 51 of the spinning nozzles 10 and 50 (Protruding into the body of the pack) to 300 mm (protruding into the body of the pack) relative to the bottom of the pack body.

At this time, the residence time of the polyester-based polymer passing through the hole in the spinning nozzle is 3 seconds or less, the flow rate is at least 0.01 cc / min or more, the shear rate of the hole wall surface in the spinning nozzle is 500 to 500,000 / sec Optimize.

The holes 11 and 51 of the spinning nozzles 10 and 50 have a diameter D of 0.01 to 5 mm, a length L and a diameter D of 1 or more and a pitch of 1 mm or more, Or a modified cross section.

The spinning nozzle used in the above-described method of producing high-strength synthetic fibers is single; Or a combination nozzle made of one selected from the group consisting of a cisco, a side-by-side, and a sea-island type.

Further, the present invention provides a high strength synthetic fiber having improved mechanical properties of strength and elongation.

Specifically, in the method for producing a synthetic fiber according to the present invention, the thermoplastic polymer is heated and heated to a temperature higher than the pack body temperature by instantaneous local high temperature heating directly under the nozzle during melt spinning, and then cooled and stretched, Strength PET fiber, high-strength nylon fiber, and high-strength PP fiber, which maintains the inherent viscosity of the polymer without causing thermal decomposition problems, and has improved strength and elongation.

The method of producing high-strength synthetic fibers according to the present invention is an optimization of the heating method under the direct injection nozzle when spinning in the melt spinning process. The thermoplastic polymer in the molten phase prior to solidification, The temperature of the molten glass fiber is heated to a temperature higher than the pack body temperature for a short period of time in which thermal decomposition does not occur and locally heated to effectively control the molecular chain entanglement structure in the polymer without lowering the molecular weight Improvement in mechanical properties such as strength and elongation can be confirmed by improving the extensibility.

Accordingly, the method of producing high-strength synthetic fibers according to the present invention can improve the mechanical properties while utilizing the existing processes of the melt spinning process and the stretching process, thereby lowering the initial investment cost, and enabling high-performance production of fibers with high production cost and low cost.

Accordingly, the present invention can be applied to a variety of materials such as tire cords, transportation interior materials for automobiles, trains, airplanes, ships, civil engineering and building materials, electronic materials, ropes and nets, In addition to being useful for military use, lightweight sportswear and clothes such as work clothes, uniforms, furniture and interiors, sporting goods, and life-saving roads are also available, thus securing a wide range of markets.

In addition, the present invention can be applied not only to PET filament, short fiber, and nonwoven fabric, but also to a manufacturing field of film, sheet, molding, container and the like using the same.

1 is an enlarged view of a spinning nozzle provided with a heating zone according to a first embodiment of the present invention,
Fig. 2 is a sectional view taken along the line I-I in Fig. 1,
3 (a) and 3 (b) are sectional views taken along a line I-I in Fig. 1 showing a modification of the first embodiment,
4 is an enlarged view of a spinning nozzle provided with a heating zone according to a second embodiment of the present invention.
5 is a sectional view taken along a line II-II in Fig. 4,
6 (a) and 6 (b) are sectional views taken along a line II-II in Fig. 4 showing a modification of the second embodiment,
FIG. 7 is a cross-sectional view of a radiation part of a spinning device provided with a conventional spinning nozzle,
8 is a sectional view taken along the line III-III in Fig. 7,
9 is a cross-sectional view of a radiation part of a spinning device provided with another conventional spinning nozzle,
10 is a sectional view taken along the line IV-IV in Fig.

Hereinafter, the present invention will be described in detail.

The present invention relates to a method for producing a thermoplastic polymer by melt spinning a thermoplastic polymer through a spinneret including at least one spinneret to form a fiber,

The fibers are allowed to pass through heating zones (40, 80) arranged just under the spinning nozzles (10, 50)

The heat-treated fiber is cooled,

The cooled fibers are wound after being stretched, and the heating zone (40, 80) locally heats the fibers by a heating body formed of a hole type die (41a, 81a) or band type die (41b, 81b) Strength synthetic fibers. In the production method of the present invention, the raw polymer may be employed without limitation among general-purpose thermoplastic polymers, and it is more preferable to use polyethylene terephthalate (PET), polybutylene terephthalate (PBT), polytrimethylene terephthalate (PTT) A polyester-based polymer selected from the group consisting of polycyclohexane dimethanol terephthalate (PCT) and polyethylene naphthalate (PEN); Polyamide-based polymers selected from nylon 6, nylon 6,6, nylon 4, and nylon 4,6; Or a polyolefin-based polymer selected from polyethylene or polypropylene; Is used.

In the embodiments of the present invention, polyethylene terephthalate (PET), nylon 6 and polypropylene are described as preferred examples, but the present invention is not limited thereto.

The fiber F is passed through the heating zones 40 and 80 disposed directly under the spinning nozzles 10 and 50 so that thermal contact (transfer) does not occur directly to the spinning nozzle holes, And passes through nozzle-heating mantle 41, 81 formed of type 41a, 81a or band-type 41b, 81b.

1 is an enlarged view of a spinning nozzle provided with a heating zone according to a first embodiment of the present invention. Fig. 2 is a sectional view taken along a line I-I in Fig. 1, Is provided in the pack body 20 of the spinning device and a pack body heater 30 is provided on the outer side of the pack body 20. The spinning nozzle 10 includes a nozzle body 12 having a plurality of spinning holes 11 for melt spinning a thermoplastic resin to form fibers F and a spinning nozzle And heating means for heating the post-spinning fiber (F).

The nozzle body 12 sprays a thermoplastic resin in a molten state through the spinneret 11 to form fibers F. The spinning fibers F are subjected to heat treatment through heating means, The thermoplastic polymer fibers are produced by cooling the fibers F and drawing the cooled fibers F by an in-line stretching machine and then winding.

The heating means directly under the spinning nozzle 10 comprises a heating body 41 having a hole-type heating hole 41a of the same structure and number as those of the spinning hole 11 of the nozzle body 12 And the post-spinning fibers F pass through the heating holes 41a so as not to directly contact (for example, heat conduction) with the heating holes 41a when passing through the heating holes 41a.

To this end, the distance a1 from the inner circumferential surface of the heating hole 41a to the center of the fiber F is preferably set within a range of 1 to 300 mm, more preferably within a range of 1 to 100 mm. The heating hole 41a of the heating hole 41a can maintain a uniform temperature at the same distance in the 360 degree direction from the center of the heating hole 41a.

As a modified example of the heating hole 41a, in the case of the spinning nozzle in which the spinning holes 11 are arranged concentrically, as shown in FIG . 3A , a plurality of spinning holes Type heating holes 41b are formed in a circular shape so that the fibers F radiated from the heating elements 11 are allowed to pass together or the heating holes 41b are formed such that the radiation holes 11 are aligned in a line In the case of the arranged spinning nozzle, it can be formed into a strip-shaped heating hole 41b that is linearly formed so that the fibers F radiated from the plurality of spinning holes 11 arranged in a row can pass therethrough. According to the form in which the radiation hole 11 is arranged in the nozzle body 12, it is possible to design various types of band-type heating holes such as arc-shaped and mountain-type, or to combine various types of heating holes have.

Like the heating hole 41a of the hole type, the distance a1 from the inner circumferential surface to the center of the fiber F is within 1 to 300 mm, more preferably within the range of 1 to 100 mm Lt; / RTI >

1, it is preferable that the nozzle body 12 and the heating body 41 are not heat transferred to each other. For this purpose, a heat insulating material layer 43 is provided between the nozzle body 12 and the heating body 41, Respectively.

The temperature of the nozzle body 12 is equal to the temperature of the pack body heater 30. [ The heat insulating material layer 43 functions to block the heat transfer so that the high temperature temperature provided by the heating body 41 located under the nozzle body 12 is not transmitted to the nozzle body 12, The problem that the raw material composed of the polyester-based polymer resin deteriorates in the nozzle body 12 to deteriorate the physical properties can be prevented. At this time, the material for the heat insulating material layer 43 may be a known heat insulating material that realizes a heat insulating effect, and preferably uses an inorganic high temperature thermal insulating material including glass and a ceramic compound.

The thickness a2 of the heat insulating layer 43 is set such that the distance between the nozzle body 12 and the heating body 41 is in the range of 1 to 30 mm. For example, when the thickness a2 is more than 30 mm, the fibers F formed after spinning from the nozzle body 12 are cooled before being heat-treated by the heating body 41, I do not.

The extension a3 of the heating body 41 is set to 1 to 500 mm from the bonding surface with the heat insulating material layer 43 and the thickness a2 of the heat insulating material layer 43 and the extension length of the heating body 41 (a3) to form a heating zone (40).

That is, the heating zone 40 of the first embodiment has a thickness a2 of the heat insulating material layer 43 set within 1 to 30 mm on the undersurface of the nozzle body 12 and a thickness a2 of 1 to 500 mm from the heat insulating material layer 43 The fiber F is heated indirectly (for example, radiation) while passing through the heating body 41 formed by the extension length a3.

At this time, by setting the distance a4 from the portion directly under the nozzle body 12 to the lower end surface of the pack body 20 within the range of 1 to 30 mm, the entire heat insulating material layer 43 and the heating body 41 ) Is located in the pack body (20). Thereby, indirectly (for example, radiation) heating is performed on all the fibers F immediately after radiation, so that productivity can be improved.

The heating zone 40 including the heating body 41 and the heat insulating layer 43 shown in the first embodiment designed as described above can be immediately applied without directly changing the design of the spinneret 10 to be commercialized, Lowering the cost, and increasing the productivity of the fiber at low cost.

In the heating zone 40 of the first embodiment, the entire fiber F discharged after the spinning is instantaneously heated at a uniform distance and at a high temperature by the heating body 41, whereby the molecular chain entanglement structure in the molten polymer It is possible to prevent the deterioration of the physical properties due to the deterioration of the molten polymer by preventing the high temperature heat from being transmitted to the radiation hole 11 of the nozzle body 12 by the heat insulating layer 43. [ Therefore, when the fibers (F) are formed by applying the heating zone (40) of the first embodiment described above, conventional thermoplastic resins can be applied without limitation, and more preferably, they are particularly advantageous for application of a polymer resin which is weak to heat.

Fig. 4 is an enlarged view of a spinning nozzle provided with a heating zone according to a second preferred embodiment of the present invention, Fig. 5 is a sectional view taken along line II-II in Fig. 4, 50 are installed in the pack body 60 of the spinning device and a pack body heater 70 is provided on the outside of the pack body 60.

The spinning nozzle 50 includes a nozzle body 52 having a plurality of spinning holes 51 for melt spinning a thermoplastic resin to form fibers F and a spinning nozzle And heating means for heating the post-spinning fiber (F).

The heating means in the second embodiment is a hole type heating hole 81a having the same structure and number as the radiation hole 51 of the nozzle body 52, Shaped heating hole 81b as shown in Fig. 1 and the post-spinning fiber F is made to pass through the heating hole 81a or 81b and the heating hole 81a Or 81b (for example, thermal conduction).

Since the heating holes 81a and 81b are the same as the heating holes 41a and 41b described in the first embodiment, a detailed description thereof will be omitted.

4, the heating means according to the second embodiment has a length b1 of -50 (inside the pack) to 300 (outside the pack) from the bottom of the pack body 60 without a heat insulating layer directly under the nozzle body 52, (b2) of 0 to 50 mm and an extended length b3 from the lower bottom surface of the nozzle body 52. The nozzle body 52 has a nozzle body 52, And a heating body 81 extending from the lower body of the nozzle body 52. The heating body 81 is inserted into the nozzle body 52. The heating body 81 is inserted into the nozzle body 52, A heating zone 80 is formed including the extension length b3 of the heating body 81. [

4, a clearance b4 of 0 to 10 mm is formed between the upper surface of the heating body 81 inserted into the nozzle body 52 and the lower surface of the nozzle body 52 facing the upper surface of the heating body 81 The heating body 81 and the surface of the nozzle body 52 come into direct contact with each other (clearance: 0 mm) and heated by direct or indirect (e.g., conduction or radiation) with a gap b4 of 10 mm maximum, The melted thermoplastic resin is first directly heated (for example, conducted) in the vicinity of the radiation hole 51.

Therefore, the heating zone 80 is formed by the thermoplastic resin melted in the vicinity of the radiation hole 51 in the nozzle body 52 before spinning with the insertion length b2 of the heating body 81 inserted into the lower part of the spinning nozzle 52 (For example, conduction or radiation) by the gap b4 and then by the extension length b3 of the heating body 81 extending from 0.1 to 500 mm in length, (For example, radiation) of the fibers F discharged before the solidification, which are discharged from the pre-solidification state.

The heating zone 80 according to the second embodiment of the present invention directly transfers the high temperature heat to the vicinity of the radiation hole 51 of the nozzle body 52 due to the structural change of the lower end in the nozzle body 52 which is actually commercialized, (F) is indirectly heated by a heating body (81) formed directly under the heating body (52), thereby controlling the molecular entanglement structure in the polymer by the instantaneous high temperature heating The thermoplastic polymer fibers obtained by the present invention are improved in the stretchability and the cooling rate is delayed, whereby the spinning speed and the stretching speed can be increased to improve the productivity.

Thus, the second embodiment can change the structure of the lower part of the nozzle body 52, which is actually commercialized, and can immediately apply it, so that the initial investment cost can be lowered and the productivity of the synthetic fiber can be improved at low cost.

In order to achieve the same object in the heating means of the first embodiment and the second embodiment described above, the residence time, flow rate, and flow rate of the molten polymer passing through each of the radiation holes 11, 51 of the nozzle bodies 12, Optimization of shear rate is required.

Thus, the residence time of the molten polymer per hole is preferably 3 seconds or less, and the flow rate is at least 0.01 cc / min or more. At this time, in the case of the polyester-based polymer, if the residence time exceeds 3 seconds, the molten polymer is exposed to excessive heat for a long time to cause deterioration, and when the flow rate is less than 0.01 cc / min, excessive heat is also exposed to the molten polymer And deterioration problems are undesirable.

The shear rate of the wall surface of the spinner holes 11 and 51 in the nozzle bodies 12 and 52 of the first and second embodiments is preferably 500 to 500,000 / sec and the shear rate is preferably 500 / sec , The molecular orientation and structure control effect of the molten polymer due to low shear stress is reduced. When the molecular weight exceeds 500,000 / sec, melt fracture due to the viscoelastic characteristics of the molten polymer occurs, resulting in nonuniformity of the cross- do.

That is, the heating holes 41a, 41b, 81a and 81b of the heating bodies 41 and 81, which are features of the present invention, are designed to have the same structure and number as the radiation holes 11 and 51 of the nozzle bodies 12 and 52 , And the fibers F discharged after the radiation are locally heated while passing through the heating bodies 41 and 81 as they are. In particular, the hole-type heating holes 41a and 81a maintain the structure of the emission holes 11 and 51 of the nozzle bodies 12 and 52, The temperature is maintained at the same distance in the 360 degree direction from the centers of the emission holes 11 and 51 of the nozzle bodies 12 and 52 by being formed within the range of 1 to 300 mm from the center of the nozzle bodies 11 and 51 6).

The band-shaped heating holes 41b and 81b have a linear structure facing 180 degrees with respect to the emission holes 11 and 51 of the nozzle bodies 12 and 52, And is symmetrical within 300 m (see Figs. 4 and 7).

At this time, the heating holes 41a, 41b, 81a and 81b are designed by an indirect heating method in which the fibers F that are passed through after radiation do not directly touch the heat. The size of the heating holes 41a, 41b, 81a, It is highly likely that the heating bodies 41 and 81 come into contact with the fibers F when the distance from the centers of the radiation holes 11 and 51 of the bodies 12 and 52 is less than 1 mm, (F) are generated, and the fiber quality and workability are deteriorated. Also, the fiber (F) may be deteriorated due to excessive heat exposure. If it exceeds 300 mm, sufficient heat transfer to the fiber (F) It is difficult to control the molecular chain entanglement structure in the scarf fiber polymer and the effect of improving the physical properties is lowered.

As shown in FIGS. 2 and 5, the hole diameter (D) is 0.01 to 5 mm and the hole length (L) / hole diameter (D) The diameter D is 1 or more, and the number of holes 11, 51 in the nozzle body is 1 or more.

The pitch between the radiating holes 11 and 51 is not less than 1 mm and the radiating holes 11 and 51 have circular shapes in the embodiments of the present invention. -, O, etc.) can also be applied. Further, two or more kinds of composite spinning such as a sheath-core type, a side-by-side type, and a sea-island type may be possible through the spinneret including the spinning nozzles 10 and 50.

The heating holes 41a and 81a of the heating bodies 41 and 81 of the heating bodies 41 and 81 of the present invention are identical in number to the radiation holes 11 and 51 of the nozzle bodies 12 and 52, A square, a donut, and the like.

The heating elements 41 and 81 can be applied to a conventional electric heating wire. Examples of the heating elements 41 and 81 include a Cu-based and an Al-based cast heater, an electromagnetic induction induction heater, a sheath heater, a flange heater, cartridge heater, a coil heater, a near-infrared heater, a carbon heater, a ceramic heater, a PTC heater, a quartz tube heater, a halogen heater, a nichrome wire heater and the like.

In the first and second preferred embodiments of the spinning nozzle for producing a high-strength thermoplastic fiber according to the present invention, the heating bodies 41 and 81 are arranged such that the temperature difference between the pack bodies 20 and 60 is 0 to 1,500 ° C., At least equal to or higher than the temperature.

The nozzle bodies 12 and 52 are fixed to the pack bodies 20 and 60 maintained at 50 to 400 DEG C from the heat sources of the pack body heaters 30 and 70, Is equal to or higher than the temperature of the heater (30, 70). If the temperature of the pack bodies 20 and 60 is less than 50 캜, most of the resin can not be melted and becomes hard to spin. When the temperature is higher than 400 캜, the physical properties of the fiber are lowered due to rapid thermal decomposition of the resin. I do not.

At this time, the temperature of the pack body heaters 30 and 70 can be controlled by an electric heater or a heat medium.

Thereafter, the molten polyester-based polymer forms the fibers discharged through the spinneret including the spinneret. Particularly, PET, nylon and PP fibers are described as the most preferable examples in the embodiments of the present invention, but the present invention is not limited to these materials. In addition, the present invention can be applied to the field of fibers such as long fibers, short fibers, and nonwoven fabrics of the above materials, and can also be applied to the fields of production of films, sheets, molds, containers and the like.

The spinning nozzles 10 and 50 of the first and second embodiments can be applied to a melt spinning process in which one or more thermoplastic polymers are used as a raw material. Specifically, the monofilament can be applied to a monofilament alone or a composite spinning process, and a monofilament having a fiber diameter of 0.01 to 3 mm can be provided by performing the spinning at a spinning speed of 0.1 to 200 m / min.

The local heating method directly above the spinning nozzle is characterized by low speed spinning (UDY, 100-2000 m / min), medium spinning (POY, 2000-4000 m / min), high speed spinning (HOY, 4000 m / (filamentous) single or multiple spinning process of 100 d / f or less by using spinning and in-line drawing process (SDY).

In addition, it can be applied to a staple fiber (single fiber) single or multiple spinning process, and can be performed at a spinning speed of 100 to 3000 m / min to provide fibers having a fiber diameter of 100 d / f or less, / min and a fiber diameter of 100 d / f or less (Spun-bond and melt blown) alone or in combination. But it can also be applied to polymer resin molding and extrusion processes.

In the above-mentioned melt spinning process of the present invention, the method of manufacturing high strength synthetic fibers optimized for the heating method under the spinning nozzle directly in spinning uses the existing spinning nozzle design and the conventional processes such as melt spinning process and drawing process, It is possible to lower the initial investment cost, and to produce high-performance fibers at a high production cost and at a low cost.

Accordingly, the present invention relates to a method for producing a thermoplastic resin composition, which comprises using a thermoplastic polymer as a raw material and heating a molten phase fiber through a heating zone disposed immediately below a spinning nozzle during melt spinning, the temperature being raised to a temperature higher than a pack body temperature for a short time, It is possible to provide a high strength synthetic fiber which maintains the inherent viscosity without deteriorating the molecular weight in spite of the high temperature heating and has improved strength and elongation.

Accordingly, the present invention can produce a high strength PET fiber having a strength of 11 g / d or more.

In particular, the present invention relates to a process for producing a polyethylene terephthalate (PET) polymer having an intrinsic viscosity (IV) of 0.5 to 3.0, more preferably 0.5 to 1.5, cooling being obtained, it provides a high-strength PET fiber elongation meet the above intensity calculated by the equation (1) to at least 5%, yet the physical properties in Table 1 and Table 2.

Equation 1

Tensile strength (g / d) = 15.873 x Intrinsic viscosity of PET fiber (I V) - 3.841

The intrinsic viscosity (IV) of the PET fiber was determined by adding 0.1 g of a sample to a reagent (90) containing phenol and 1,1,2,2-tetrachloroethane in a weight ratio of 6: 4 at a concentration of 0.4 g / 100 ml Dissolve in a Ubbelohde viscometer for 90 minutes, hold it in a thermostat for 30 minutes, and measure the number of drops of the solution using a viscometer and an aspirator. The number of drops of the solvent was also calculated by the formula of the R.V. value and I.V. value (Bill Meyer approximation formula) obtained by the method described below.

R.V. = Sample falling water / solvent falling water water

I.V. = (R.V.-1) / 4C + 3ln (R.V.) / 4C (C: concentration (g / 100ml)

The polyester fiber group having various intrinsic viscosities (IV) can be obtained by the local high-temperature heating method directly under the nozzle in the melt spinning of the present invention. The polyester fiber group having relatively high intrinsic viscosity (IV) It is possible to provide high strength polyester fibers having physical properties.

Also, the present invention can produce high-strength nylon fiber which is produced through the above-mentioned production method and has a strength of 10.5 g / d or more.

In particular, the present invention relates to a nylon polymer having a relative viscosity (Rv) of from 2.0 to 5.0, more preferably from 2.5 to 3.5, which is heated, radiated, stretched and cooled after heating by a local high- the elongation is provided to at least 5%, yet high-strength nylon to meet the strength properties than that calculated by the expression (2) fibers [Table 3].

Equation 2

Tensile strength (g / d) = relative viscosity (Rv) of 8.6 x Nylon fiber - 14.44

The relative viscosity (RV) of the Nylon fiber was measured by dissolving 0.1 g of the sample in 96% sulfuric acid for 90 minutes so that the concentration became 0.4 g / 100 ml, transferred to a Ubbelohde viscometer, and maintained in a thermostat for 30 minutes , And the falling seconds of the solution were determined using a viscometer and an aspirator. The number of drops of the solvent was also determined by the same method, and then calculated by the following formula of the RV value.

R.V. = Samples falling in water / solvent drops in seconds

Accordingly, the polyamide fiber group having various relative viscosities (Rv) can be obtained by the local high-temperature heating method directly under the nozzle in the melt spinning of the present invention, and the relative viscosity (Rv) High-strength polyamide-based fibers having high physical properties can be provided.

Further, the present invention can produce high-strength PP fibers which are produced by the above-mentioned production method and have a strength of 10.0 g / d or more.

Particularly, the present invention is characterized in that a polypropylene (PP) polymer having a melt viscosity (MFI) of 3 to 200, preferably 10 to 35 is heated, radiated, stretched and cooled by heating by an instant local heating method directly under a nozzle during melt spinning, that provides a high-strength PP fiber that meets the above strength is calculated by the following equation (3) at least 5%, yet the physical properties [Table 4].

Equation 3

The tensile strength (g / d) = -0.225 × the melt viscosity (MFI) of the PP fiber + 12.925

The PP resin and the melt flow index (MFI) were measured according to the ASTM D1238 (MFI 230/2) method. Specifically, the PP resin was melted at 230 ° C for about 6 minutes, The weight (g / 10 min) of the resin discharged for 10 minutes under a pressure of 2.16 kg is measured.

Accordingly, the polyolefin-based fiber group having various melt viscosities (MFI) can be obtained by the local high-temperature heating method directly under the nozzle during melt spinning of the present invention, and the relatively high Strength high-strength polyolefin-based fibers.

The present invention provides high-strength synthetic fibers from the above-mentioned manufacturing methods, thereby providing cost-competitive properties due to mass production and low cost, and control of various fiber properties, thereby providing tire cord, interior materials for transportation such as automobiles, trains, , Electronic materials, ropes and nets, as well as lightweight sportswear, work clothes, uniforms, furniture, interior and sporting goods, and life-saving roads, .

Hereinafter, the present invention will be described in more detail with reference to Examples.

The present invention is intended to more specifically illustrate the present invention, and the scope of the present invention is not limited to these embodiments.

< Example  1> Production of high-strength PET fiber by the heating method of the first embodiment

A polyethylene terephthalate (PET) resin (intrinsic viscosity of 1.20 dl / g) was extruded into a melt extruder and introduced into a spinning nozzle at a temperature of 300 ° C. At this time, unburned and partially stretched PET fibers were produced by spinning from a pack-body heater heat source in a packed state held at the same temperature as the spinning nozzle. At this time, the heat insulating material layer 43 and the heaters having the same hole structure and the same number as the spinneret were arranged at the positions directly below the spinneret from the lower end of the nozzle to have a length of 5 mm and 10 mm, respectively, (40). The heat insulating material layer 43 and the heating body 41 made of a heater are formed in a plurality of holes having a radius larger than 10 mm at the center of each hole of the spinning nozzle so that the fibers discharged from the spinning- It is designed so that heat can be transmitted without directly contacting the heating body 41 made of the heater 43 and the heater.

(1) Radiation condition

- Resin used: PET (I.V. 1.20)

- Radiation temperature (Nozzle temperature): 300 ℃

- Spray nozzle hole diameter: Φ 0.5

- Discharge volume per spinner nozzle hole: 3.3 g / min

- Local heating heater temperature directly below the nozzle: Nozzle temperature + 100 ℃ or higher

- Radiation speed: 0.5 to 2 k / min

< Example  2> Production of high-strength PET fiber by the heating method of the second embodiment

A polyethylene terephthalate (PET) resin (intrinsic viscosity of 1.20 dl / g) was extruded into a melt extruder and introduced into a spinning nozzle at a temperature of 297 ° C. At this time, unburned and partially stretched PET fibers were produced by spinning from a pack-body heater heat source in a packed state held at the same temperature as the spinning nozzle. The lower part of the spinning nozzle was protruded 2 mm from the lower part of the pack body and the heating body 81 made of the heater having the same hole structure and number as the spinning nozzle was disposed within a distance of 5 mm from the lower end of the nozzle without heat insulating material, And the heating zone 80 of the direct / indirect heating type of the fibers immediately after discharge was formed. The heating body 81 made of the heater has a plurality of holes each having a radius larger than 10 mm at the center of each hole of the spinning nozzle so that the fibers discharged from the discharge port of each spinning nozzle can be heat- And was directly heat-transferred within 5 mm of the lower end of the spinning nozzle. At this time, the spinning conditions were the same as in Example 1, and the results are shown in Table 1 .

Figure 112016023187675-pat00001

As a result of the above Table 1, the polyethylene terephthalate (PET) resin of Examples 1 and 2 produced through local high-temperature heating directly under the nozzle had no intrinsic viscosity change of the fiber during the spinning process, .

In addition, the PET resin of Examples 1 and 2 described above has confirmed that the fiber properties of the strength and elongation are higher than those of the fibers obtained from the conventional method in which the fiber properties of the fibers are performed without heating at local high temperature directly under the nozzle. Thus, it was confirmed that the physical properties were improved by molecular chain entanglement control by local high temperature heating directly under the nozzle.

Particularly, in the case of the second embodiment in terms of improvement of the fiber properties of the strength and elongation, the case of locally heating the molten resin directly or indirectly is preferable. It was also confirmed that the strength could be further improved when heated to a higher temperature in the future.

< Example  3 to 4> Production of high strength PET fiber by the heating method of the second embodiment

Example 2 and Comparative Example 2 were repeated except that the intrinsic viscosity of the PET resin was changed and the following low-speed spinning and off-line stretching were carried out as shown in Table 2 , High strength PET fibers were produced in the same manner.

(1) Radiation condition

- Resin used: PET (I.V. 0.65 and 1.20)

- Radiation temperature (nozzle temperature): 280-300 ℃

- Spray nozzle hole diameter: Φ 0.5

- Discharge volume per spinner nozzle hole: 3.3 g / min

- Local heating heater temperature directly below the nozzle: Nozzle temperature + 100 ℃ or higher

- Radiation speed: 1k / min

(2) Offline stretching condition

- undrawn yarn: PET as-spun fibers obtained from the above spinning conditions

- 1st godet roll speed (temperature): 10m / min (85 ° C)

- Stages of stretching: more than 3 stages

- Sampling was carried out at the maximum draw ratio that can be continuously drawn without being cut (open and constant temperature 130 to 180 ° C)

Figure 112016023187675-pat00002

As can be seen in Table 2 above, the PET resins with intrinsic viscosity of 0.65 and 1.2 were prepared in the same manner, except that the PET resin of Examples 3 to 4, prepared via local hot heating immediately below the nozzle, The fibers of Comparative Examples 2 to 3, which were performed, showed no change in intrinsic viscosity during the spinning process. This suggests that the pyrolysis problem did not occur due to local high temperature heating immediately after the nozzle.

As a result of the fiber properties of the strength and elongation, the fiber properties of the unstretched yarn (as-spun yarn) and the drawn yarn prepared in Examples 3 to 4 were compared in the same manner Compared with 2 to 3 fibers. From these results, it was confirmed that the physical properties of the low molecular weight and high molecular weight PET resin were improved by molecular entanglement control by local high temperature heating directly under the nozzle.

In particular, in the drawn yarns of Examples 3 to 4, the strength of the low molecular weight and high molecular weight PET fibers was improved by 10% or more at the same elongation as compared with Comparative Examples 2 to 3.

< Example  5 to 6> Production of high-strength nylon fiber by the heating method of the second embodiment

Nylon 6 resin (Rv 3.4) having relative viscosities of 2.6 and 3.4 was melt-extruded in an extruder and flowed into a spinning nozzle at a temperature of 270 ° C. In the second embodiment of the present invention, Low speed spinning and off - line stretching were performed to fabricate Nylon 6 fibers. However, Comparative Examples 4 to 5 were carried out in the same manner, except that the nozzle was not subjected to the local high-temperature heating method. The results are shown in Table 3 .

(1) Radiation condition

- Resin used: Nylon 6 (Rv 2.6 and 3.4)

- Radiation temperature (Nozzle temperature): 250 ~ 270 ℃

- Spray nozzle hole diameter: Φ 0.5

- Discharge volume per spinner nozzle hole: 3.3 g / min

- Local heating heater temperature directly below the nozzle: Nozzle temperature + 100 ℃ or higher

- Radiation speed: 1k / min

(2) Offline stretching condition

- Undrawn yarn: Nylon 6 as-spun fibers obtained from the above spinning conditions

- 1st godet roll speed (temperature): 10m / min (85 ° C)

- Stages of stretching: more than 3 stages

- Continuous continuous stretching without cutting The stretching sample is sampled at the maximum stretching ratio (open and constant temperature 130 ~ 180 ℃)

Figure 112016023187675-pat00003

From the results in the above Table 3, except that the fibers of Examples 5 to 6 prepared by instantaneous local heating directly under the nozzle using a Nylon 6 resin having a relative viscosity (Rv) of 2.6 and 3.4 were carried out without local high temperature heating directly under the nozzle The fibers of Comparative Examples 4 to 5, which were performed in the same manner, were observed uniformly with no relative viscosity difference during the spinning process. This suggests that the pyrolysis problem did not occur due to local high temperature heating immediately after the nozzle.

As a result of the fiber properties of the strength and elongation, the unstretched yarn (as-spun yarn) and stretch yarn of Examples 5 to 6 obtained by locally high-temperature heating directly under the nozzle using a Nylon 6 resin having a relative viscosity (Rv) of 2.6 and 3.4, The properties were higher than those of Comparative Examples 4 and 5. From these results, it was confirmed that the properties of the low molecular weight and high molecular weight nylon resin were improved by molecular entanglement control by local high temperature heating directly under the nozzle.

In particular, in the stretched yarns of Examples 5 to 6, the strength of the low molecular weight and high molecular weight Nylon 6 fibers was improved by 10% or more at the same elongation as in Comparative Examples 4 to 5.

< Example  7 to 8> Production of high-strength PP fiber by the heating method of the second embodiment

The PP resin having melt viscosity (MFI) of 33 and 12 was put into an extruder and melt-extruded and flowed into a spinning nozzle at a temperature of 270 DEG C. In the second embodiment of the present invention, Followed by stretching to prepare PP fibers. However, Comparative Examples 6 to 7 were carried out in the same manner, except that the nozzle was not subjected to the local high-temperature heating method. The results are shown in Table 4.

(1) Radiation condition

- Resins used: PP (MFI (190/5) 33 and 12)

- Radiation temperature (nozzle temperature): 210 to 270 ° C

- Spray nozzle hole diameter: Φ 0.5

- Discharge volume per spinner nozzle hole: 3.3 g / min

- Local heating heater temperature directly below the nozzle: Nozzle temperature + 100 ℃ or higher

- Radiation speed: 1k / min

(2) Offline stretching condition

- Undrawn yarn: PP fibers obtained under the above spinning conditions

- 1st godet roll speed (temperature): 10 m / min (85)

- Stages of stretching: more than 3 stages

- Sampling was carried out at the maximum draw ratio that can be continuously drawn without being cut (open and constant temperature 130 to 180 ° C)

Figure 112016023187675-pat00004

From the results in Table 4, except that the PP resins of MFIs 33 and 12 were used without local high temperature heating directly under the fibers and nozzles of Examples 7 to 8, which were prepared by local high temperature heating immediately below the nozzle, The fibers of Comparative Examples 6 to 7, which were carried out in the same manner, had no change in intrinsic viscosity during the spinning process. This suggests that the pyrolysis problem did not occur due to local high temperature heating immediately after the nozzle.

As a result of the fiber properties of the strength and elongation, the fiber properties of the unstretched yarn (as-spun yarn) and the drawn yarn of Examples 7 to 8 obtained by locally high-temperature heating directly under the nozzle using a PP resin having a melt viscosity (MFI) Was higher than that of Comparative Examples 6 to 7 fibers. From these results, it was confirmed that the physical properties of the low molecular weight and high molecular weight PP resins were improved by molecular entanglement control by local high temperature heating directly under the nozzle.

Particularly, in the case of the drawn yarns of Examples 7 to 8, the strength of the low molecular weight and high molecular weight PP fibers was improved by 10% or more at the same elongation as in Comparative Examples 6 to 7.

As described above, the manufacturing method of the present invention is an optimization of the heating method when the spinneret is directly spun when spinning in a melt spinning process, and the melted filament is doubly heated By optimizing the heat transfer method, the molecular chain entanglement structure of the molten phase polymer is controlled by instantaneous high temperature heating to improve the extensibility of the fibers, thereby improving the strength and elongation.

The method for producing high-strength synthetic fibers of the present invention can improve the physical properties while utilizing existing processes such as melt spinning process and stretching process, thereby lowering the initial investment cost and enabling production of high-performance fibers at a high production cost and low cost.

Accordingly, by providing a high-strength synthetic fiber group including PET, Nylon and PP fibers among the thermoplastic polymers, it is possible to provide various kinds of synthetic fibers such as tire cord, transportation interior material for automobiles, trains, airplanes, ships, civil engineering and building materials, And it is also useful for lightweight sportswear and clothes such as work clothes, uniforms, furniture and interior, sporting goods, and life-use roads, and it is possible to secure a wide market.

In particular, by providing high-strength PET fibers, it can be applied to textile fields such as PET long fibers, short fibers, and nonwoven fabrics, and can be utilized in the field of production of films, sheets, molds, containers and the like.

While the present invention has been particularly shown and described with reference to exemplary embodiments thereof, it is evident that many alternatives, modifications and variations will be apparent to those skilled in the art.

10, 50: spinning nozzle 11, 51:
12, 52: nozzle body 20, 60: pack body
30,70: Pack-Body Heater
40, 80: heating zone 41, 81:
41a, 41b, 81a, 81b: heating hole 43: heat insulating material layer
F: Fiber

Claims (15)

The thermoplastic polymer is melt-spun through a spinneret containing at least one spinneret to form a fiber, and the fiber is passed through a heating zone disposed on the lower surface of the spinneret during the spinning process, Cooling the treated fibers, winding the cooled fibers after stretching,
A heating zone disposed directly below the spinning nozzle,
Shaped or band-like type in which a heating hole having the same structure and number as the radiation holes of the nozzle body is formed and the distance a1 from the inner circumferential surface of the heating hole to the center of the fiber F is within 1 to 300 mm The molten-phase fibers are passed through the heating body formed around the hole,
The heating body is extended to the lower bottom surface of the nozzle body and the temperature difference between the pack body temperature maintained at a temperature of 50 to 400 ° C is maintained at 1 to 1,500 ° C so that the fiber temperature is locally heated to a higher temperature than the pack body temperature By weight based on the total weight of the synthetic fibers. The method of claim 1, wherein the thermoplastic polymer is at least one selected from the group consisting of polyethylene terephthalate (PET), polybutylene terephthalate (PBT), polytrimethylene terephthalate (PTT), polycyclohexanedimethanol terephthalate (PCT), and polyethylene naphthalate PEN); &lt; / RTI &gt; Polyamide-based polymers selected from nylon 6, nylon 6,6, nylon 4, and nylon 4,6; Or a polyolefin-based polymer selected from polyethylene or polypropylene; , Wherein the high-strength synthetic fiber is produced by a method comprising the steps of: delete delete delete The method of claim 1, wherein when the spinning fibers are formed in a concentric shape and the spinning nozzle has a plurality of holes in the same radius from the center of the spinning nozzle, Is passed through the heating body formed of the heating holes (41b, 81b) of the high-strength synthetic fiber. The heat insulating material layer (43) according to claim 1, wherein the heating zone (40) extends from 1 mm to 500 mm from the heat insulating material layer and the heat insulating material layer (43) Wherein a heating zone of the fiber is formed including an extension length of the heating body. The method according to claim 1, wherein the heating zone (80) comprises a lower portion of a nozzle body (52) located at -50 (entering the pack body) to 300 mm And the extension length of the heating body extending from the lower portion of the nozzle body 52 is 0.1 to 500 mm, and a part of the heating body is inserted in the lower part of the nozzle body Wherein a heating zone of the fiber is formed including an insertion depth of the inserted heating body and an extension length of the heating body extending from a lower portion of the nozzle body. The method according to claim 1, characterized in that the residence time of the molten thermoplastic polymer passing through the holes (11, 51) in the spinning nozzle (10, 50) is 3 seconds or less and the flow rate is at least 0.01 cc / min Method of manufacturing high strength synthetic fibers. The method according to claim 1, wherein a shear rate of the wall surface of the holes (11, 51) in the spinning nozzle (10, 50) is 500 to 500,000 / sec. 2. A method according to claim 1, characterized in that the structure of the holes (11, 51) of the spinning nozzle (10, 50)
Diameter (D) of 0.01 to 5 mm,
Length (L) / Diameter (D) 1 or more,
A pitch of 1 mm or more and
Wherein the cross-section is a circular or irregular cross-section. The method of claim 1, wherein the spinning nozzle (10, 50) is single; Wherein the composite nozzle is made of one selected from the group consisting of a cis-sponge, a side-by-side, and a sea-island type. The polypropylene fiber according to claim 1, wherein the synthetic fiber is a fiber obtained from a polyethylene terephthalate (PET) polymer having an intrinsic viscosity (IV) of 0.5 to 3.0, and has an elongation of 5% or more and a strength Wherein the high strength PET fiber is a high strength PET fiber.
Equation 1
Tensile strength (g / d) = 15.873 x Intrinsic viscosity of PET fiber (IV) - 3.841 The high-strength nylon fiber according to claim 1, wherein the synthetic fiber is a fiber obtained from a nylon polymer having a relative viscosity (Rv) of from 2.0 to 5.0, and has a elongation of 5% or more and a strength Wherein the fiber is a fiber.
Equation 2
Tensile strength (g / d) = relative viscosity (Rv) of 8.6 x Nylon fiber - 14.44 The synthetic fiber according to claim 1, wherein the synthetic fiber is a fiber obtained from a polypropylene (PP) polymer having a melt viscosity (MFI) of 3 to 200, an elongation of 5% Strength PP fiber satisfying the strength calculated by the following formula (3).
Equation 3
The tensile strength (g / d) = -0.225 × the melt viscosity (MFI) of the PP fiber + 12.925
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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR20200066188A (en) 2018-11-30 2020-06-09 한국생산기술연구원 Manufacturing method of melt-spinning type nonwoven web and nonwoven web products manufactured thereby

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WO2020111910A1 (en) * 2018-11-30 2020-06-04 한국생산기술연구원 Method for manufacturing melt-spun nonwoven fabric and microfiber nonwoven web manufactured therefrom
KR20240035665A (en) * 2022-09-08 2024-03-18 한국생산기술연구원 Manufacturing method of high strength sheath-core fiber and high strength sheath-core fiber manufactured by using the same

Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2010037676A (en) 2008-08-04 2010-02-18 Teijin Fibers Ltd Melt-spinning device
JP2012158851A (en) 2011-02-01 2012-08-23 Kb Seiren Ltd Method for manufacturing aromatic polyester fiber
KR101632636B1 (en) * 2015-03-09 2016-06-23 한국생산기술연구원 Manufacturing method of high strength polyester fiber

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2010037676A (en) 2008-08-04 2010-02-18 Teijin Fibers Ltd Melt-spinning device
JP2012158851A (en) 2011-02-01 2012-08-23 Kb Seiren Ltd Method for manufacturing aromatic polyester fiber
KR101632636B1 (en) * 2015-03-09 2016-06-23 한국생산기술연구원 Manufacturing method of high strength polyester fiber

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR20200066188A (en) 2018-11-30 2020-06-09 한국생산기술연구원 Manufacturing method of melt-spinning type nonwoven web and nonwoven web products manufactured thereby

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