JPH07331529A - Polyhexamethylene adipamide fiber and its production - Google Patents

Abstract

PURPOSE:To obtain polyhexamethylene-based fibers, excellent in transparency and stability of physical properties at high temperatures and high humidities with time and suitable for improving functions in the fields of clothes, legs and usual industrial materials. CONSTITUTION:This method for producing polyhexamethylene adipamide fibers is to apply 1600-5000ppm water to a mixed composition comprising 99-75 pts.wt. polyhexamethylene adipamide having an amino end group concentration A mequiv./g and a carboxyl end group concentration B mequiv./g satisfying the relationship A>=1.2XB and 1-25 pts.wt. polyglutarimide having an acid anhydride group of the formula (R1 and R2 are each H or a 1-20C alkyl; R3 is H, an alkyl, a cycloalkyl, allyl, an alkaryl or an aralkyl), then melt discharge the resultant composition at >=270 deg.C, subsequently draw the obtained yarn and provide the nylon 66-based fibers. The fibers have physical properties satisfying the relationships of <=3OC difference in beta dispersion peak temperature of a tandelta-temperature curve before and after treating the fibers at 45 deg.C and RH85% in a tensed state for 7 days, <=0.05 difference in its value tandelta beta before and after the treatment, 0.1 <= (total de)<=30, transmittance % of the raw yarn > -15.6Xlog(total de) + 35.0 and reflectance of the raw yarn %<-58.7 (transmittance of the raw yarn) + 151.4.

Description

Detailed Description of the Invention

[0001]

TECHNICAL FIELD The present invention relates to a mixed fiber of polyhexamethylene adipamide and polyglutarimide and a method for producing the same. More specifically, for clothing applications, which minimizes the deterioration of physical properties over time in high humidity and high temperature atmospheres,
The present invention relates to a polyhexamethylene adipamide and poly ε-caproamide blend fiber suitably used for leg applications and the like.

[0002]

2. Description of the Related Art Polyhexamethylene adipamide (nylon 66) fibers are excellent in strength, toughness, heat resistance, dyeing fastness, color developability, etc., and are therefore fibers for industrial materials, interior bedding, and clothing. Widely used as a leg fiber. However, due to its high crystallinity, it has lower color development and higher rigidity than poly ε-caproamide (nylon 6) fiber, and therefore has a relatively low soft feeling, and as a product, it has resistance to the energy applied. It has the problem of being low.

Further, since it is not amorphous or low in crystallinity, such as acrylic fiber and nylon 6, its use is essentially limited in fields requiring transparency and low transparency. Furthermore, the polyamide-based fiber has a fatal defect that it causes deterioration of physical properties over time under high temperature and high humidity conditions. This is basically due to the structural change (moisture diffusion induced crystallization) and microvoiding due to the action of water, and if there are defects in the raw yarn, the physical properties even at the weaving, knitting, dyeing and setting stages. As a result, the yarn's potential, including transparency, cannot be fully exerted.

In order to improve the transparency of the nylon 66, the single yarn may be made thin, but in terms of structure, an amorphous region may be increased, and in order to improve the defect of physical property change with time, It is necessary to increase the aggregation density of molecular chains in the amorphous region. Therefore, this principle is basically one, and it suffices to inhibit the crystal growth of nylon 66 in the spinning stage and increase the hydrogen bond concentration in the amorphous portion. The methodology is to form a branched structure in a linear chain. The mainstream is introduction and blending with other polymers. In the field of engineering plastics, as a method of introducing a branched structure, strength and impact resistance can be improved by grafting nylon 6 essentially non-crystalline glutarimide polymer with caustic soda intervening during melt mixing. It is known that it can be measured, but there is no report that it is molded in a fiber form, and there are few known examples of grafting or blending the above polymer with nylon 66.

It is presumed that this is because the basic hydrogen bond densities of nylon 6 and nylon 66 are different from each other, so that even nylon 66 cannot be uniformly mixed. Further, it cannot be said that mixing caustic soda at a high temperature as in the case of nylon 6 is a preferable method per se. That is, even if the blend system has some water, the melting point of caustic soda is 318 ° C. or higher, and it is unavoidable that a part of the caustic soda is changed to carbonate during the mixing operation process.

[0006]

SUMMARY OF THE INVENTION An object of the present invention is to establish a uniform melt mixing method of nylon 66 and polyglutarimide, which has a single yarn denier of 1.8 d or less and has high transparency, high humidity and high humidity. Provided is a blended fiber of nylon 66 and polyglutarimide, which has excellent physical stability over time in a temperature atmosphere, and accordingly, clothing, legs, and general industries that are required to maintain high toughness and have a soft texture. It is to ensure the processing stability while achieving the functional improvement in the material field.

[0007]

Means for Solving the Problems The inventors of the present invention investigated an industrial blending method of nylon 66 and polyglutarimide, and earnestly studied the characteristics of the fiber obtained from the method. The melt-mixing property of the mixed composition of No. 1 is in balance with the flow characteristics and the end group of nylon 66, the crystal growth of Nylon 66 is suppressed in the blended fiber, and the transparency is remarkably excellent. The present inventors have found that the mechanism lies in the formation of microvoids based on water diffusion-induced crystallization, and that the end group balance is also related to the essential cohesiveness of the amorphous region of the melt-extruded fiber.

That is, according to one aspect of the present invention, the relationship between the amino terminal group concentration A (milliequivalent / kg; meq / kg) and the carboxyl terminal group concentration B (meq / kg) is A ≧ 1.2 × B. A blend fiber comprising 99 to 75 parts by weight of hexamethylene adipamide and 1 to 25 parts by weight of polyglutarimide having an acid anhydride group represented by the following general formula (1). (A) Constituent single yarn denier is 1.8 d or less, (b) 45 ° C. and 8% relative humidity under tension.
T of fiber before and after treatment in 5% atmosphere for 7 days
an δ-temperature (T) β dispersion peak temperature T appearing in the curve
The difference between β and its value tan δβ is 3 ° C or less, and 0.0
And less than 05, (c) a raw fiber transmittance and a raw yarn reflectance satisfy the following formulas (2) and (3), a polyhexamethylene adipamide-based fiber,

[0009]

[Chemical 3]

Raw yarn transmittance (%)> − 15.6 × Log (total denier) +35.0 (2) However, 0.1 ≦ (total denier) ≦ 30. Raw yarn reflectance (%) <−58.7 × (raw yarn transmittance (%)) + 151.4 (3), and the other is polyhexamethylene adipamide and the following general formula ( 1. A method for producing a blend fiber with an acid anhydride group-containing polyglutarimide represented by 1), wherein the amino terminal group concentration A of the polyhexamethylene adipamide is A.
The relationship between (milliequivalent / kg; meq / kg) and the concentration B of carboxyl end group B (meq / kg) is A ≧ 1.2 × B, and 99 to 75 parts by weight of the polyhexamethylene adipamide and the polyglutar. Water is added to a mixed composition of 1 to 25 parts by weight of imide at a concentration of 1600 to 5000 ppm, and melt-discharged at 270 ° C. or higher to form a fiber, and the discharged fiber is directly drawn or continuously drawn. And a method for producing a polyhexamethylene adipamide-based fiber, which comprises:

[0011]

[Chemical 4]

That is, the blend fiber of nylon 66 and polyglutarimide of the present invention has an amino terminal group concentration A
(Milliequivalent / kg; meq / kg) and carboxyl end group concentration B (meq / kg) have a relationship of A ≧ 1.2 × B, polyhexamethylene adipamide 99 to 75 parts by weight, and acid anhydride group. Water is added to a mixture of 1 to 25 parts by weight of polyglutarimide at a concentration of 1600 to 5000 ppm, melt-mixed at 270 ° C. or higher, and then discharged, and then the fibers are taken as they are, or the fibers are taken. It is a novel fiber which has a denier of 1.8 d or less and has the following characteristics, which is obtained by subsequent drawing and has the following characteristics, and is highly transparent and has little deterioration in physical properties over time.

Of the blended fiber obtained in the present invention,
As for the light transmittance and the reflectance of the raw yarn, SZ-Σ90 manufactured by Nippon Denshoku Industries Co., Ltd. was used, and the fiber was uniformly parallel to a metal plate with a thickness of 2 mm having a hole of 5 cm × 3 cm. After winding by traverse control, transmitted light is made incident on this plate in the vertical direction, and the transmittance is measured and defined on the plate by the 0-45 ° method.

The total denier of the polyhexamethylene adipamide fiber of the blended fiber of the present invention is 7 denier, and the light transmittance and the reflectance of the 5 filament fiber are 2 respectively.
More than 1.8% 72. It is 8% or less, and compared with a normal nylon fiber having the same single filament denier and the same filament configuration, the raw fiber light transmittance is 18.0% and the raw fiber light reflectance is 77.7%. It has remarkable transparency.

Also, under tension, 45 ° C., relative humidity 85%
Tan of the fiber before and after treatment for 7 days in the atmosphere
The difference between the β dispersion peak temperature Tβ appearing on the δ-temperature (T) curve and its value tan δβ is 3 ° C. or less, and 0.005 or less, the degree of change is extremely small, and the stability over time is large. The β-dispersion is a moving region of side chains and end groups of the polyamide polymer. It is considered that the end base portion usually becomes a stress concentration point under tension, and if this portion easily moves with respect to an external stimulus, it eventually leads to deterioration of characteristics over time.
Especially, in the conventional spinning method in which spinning and drawing are performed in separate steps,
The structure of the undrawn yarn changes every time it is left unattended, which is a problem in terms of management and has a drawback that the final physical properties vary widely. Therefore, in the blended fiber of the present invention, the difference between the β dispersion peak temperature Tβ before and after the treatment and its value tanδβ is 3
It is essential that the temperature is not higher than 0 ° C and not higher than 0.005.

The nylon 66 raw material polymer which is one member of the polyhexamethylene adipamide fiber of the blended fiber of the present invention is a polycondensate of adipic acid and hexamethylene diamine. For the nylon 66 raw material polymer used in the present invention, commonly used additives, for example, inorganic phosphorus compounds such as phosphoric acid and sodium hypophosphite, organic phosphorus compounds such as phenylphosphonic acid and triphenylphosphite, phosphorus- Nitrogen complex salts, polymerization catalysts such as phosphorus-nitrogen compounds, copper acetate, copper bromide, copper iodide, copper compounds such as 2-mercaptobenzimidazole copper complex salts, 2-mercaptobenzimidazole, tetrakis- [methylene-3- (3,5-di t-
Butyl-4-hydroxyphenyl) -propionate]-
Heat stabilizers such as methane, light stabilizers such as manganese lactate and manganese hypophosphite, matting agents such as titanium dioxide and kaolin,
A lubricating agent such as ethylene bis-stearyl amide, a partial methylol compound, calcium stearate, a plasticizer, and a crystallization inhibitor can be included.

The nylon 66 raw material polymer used in the present invention can satisfy practical mechanical properties if the number average degree of polymerization is 13500 or more. Polyglutarimide, which is another member of the polyhexamethylene adipamide-based fiber of the blended fiber of the present invention, is commercially available and has a glutarimidization ratio of 55.
-80% and a molecular weight of 90,000 to 145,000 are used.

The mixing ratio of both is 99 to 66 of nylon 66.
The amount of polyglutarimide is 1 to 25% by weight with respect to 75% by weight. Since the acid anhydride part in the polyglutarimide reacts with the terminal amino group of nylon 66 and the imide part inhibits the hydrogen bond formation of nylon 66,
If the amount of polyglutarimide is 1 part by weight or more, the crystallization of nylon 66 can be sufficiently inhibited and the stretchability can be improved.
If the amount of polyglutarimide is 25% by weight or more, the thermal characteristics of nylon 66 are impaired, and the heat settling phenomenon seen in, for example, acrylic fibers occurs, which is not preferable.

Nylon 6 is an absolute condition for producing the polyhexamethylene adipamide fiber of the above blended fiber.
6 as the amino terminal group concentration A (milliequivalent / kg; meq
/ Kg) and carboxyl end group concentration B (meq / kg)
Using a chip having a relationship of A ≧ 1.2 × B, water is added to the mixture of both at a concentration of 1600 to 5000 ppm, and melt ejection is performed at 270 ° C. or higher is a technical skeleton. The amino terminal group and carboxyl terminal group concentrations of the polyhexamethylene adipamide chip can be adjusted by the ratio of charged monomers.

The relationship between the amino end group concentration A (milliequivalent / kg; meq / kg) and the carboxyl end group concentration B (meq / kg) of nylon 66 specified by the present invention, A ≧ 1.
2xB is important for the melt mixing property with polyglutarimide. Although the molecular chains can naturally be entangled by the mixing operation, as will be described later, water is always present during melt mixing, and the water diffuses in the melt.

Therefore, in the system having a rich amino terminal group as in the present invention, a large number of hydroxide ions are present, and the hydroxide ions cleave the intermolecular hydrogen bond of the existing polymer, but a new hydrogen bond is newly formed. By creating a starting point and increasing the hydrogen bonding probability between the N66 molecule and the imide of polyglutarimide to increase the miscibility between the two, the acid anhydride and nylon 66 in the polyglutarimide under alkaline atmosphere
It also improves the reactivity at high temperature with.

On the other hand, in a carboxyl-rich system, for example, since protons diffuse, only existing hydrogen bond breakage occurs, and the probability of hydrogen bond firmly connecting N66 and polyglutarimide is reduced, resulting in a thermal problem in spinning. During the phase separation operation, the probability of each independently aggregating increases, a strong aggregate structure cannot be obtained as a whole, the reaction between the amino terminal group and the acid anhydride cannot be expected at all, and nylon by grafting is not expected. The crystallization-inhibiting effect of 66 does not occur.

The upper limit of AB (hereinafter referred to as Δa) is not limited, but as Δa increases, the nylon 66 used in the present invention has a relatively high melt viscosity during the melting process even if the degree of polymerization is the same, and the same chip has the same viscosity. Under water conditions, as Δa becomes larger, the relative melt viscosity increase rate at the same degree of polymerization also rises, and there is no choice but to spin at a temperature (300 ° C. or higher) that is much higher than the normal spinning temperature, causing oxidative decomposition of the polymer, etc. Problems and problems of polymer gel formation on the wall surface of the extruder also occur during long-term operation, which impairs spinning stability, and therefore should be selected appropriately.

In order to ensure the mixing uniformity of both, in the present invention, it is necessary to set the water content contained in both polymer chips used in the invention to 1600 to 5000 ppm and perform melt mixing at 270 ° C. or higher. If the spinning temperature does not fall below 270 ° C., sufficiently proper spinning can be performed, and a 1GD wound yarn having a uniform aggregated structure can be produced. This is considered to be an effect of reducing the polydispersity of molecular weight in addition to the plasticizing effect of water. When the water content is 1600 ppm or less, the effect of improving the die swell of both mixed polymer melts melted and discharged is low, the mixing property is low, and there remains a problem in the uniformity of the agglomerated structure of the spun 1GD take-up yarn.

This is because when the terminal group of the nylon 66 polymer used in the present invention is amino-rich as in the present invention as described above, for example, the melt viscosity is higher than that of a carboxyl-rich polymer, One of the reasons is that it is necessary to have a plasticizing effect in the presence of sufficient water. On the contrary, at 5000 ppm or more, a rapid crystallization action of the N66 portion is induced, and even in a polymer blend system in which the N66 portion is uniformly mixed, the nylon 66 portion is rapidly crystallized due to the action of water to cause microphase separation, which is stable. The spinnability cannot be ensured, and when the stretching operation is continued, due to the above micro phase separation, smooth stretching cannot be secured,
As a result, stability over time cannot be guaranteed. The more preferable range of the chip moisture content is 1800 ppm to 3500 in consideration of the fact that the viscosity variation of the discharged polymer melt due to the moisture variation is small and the structural stability of the spun 1GD wound yarn.
It is ppm.

Of course, as can be easily understood by those skilled in the art, the essential solution to the problem of stability of polyamide-based fibers over time is basically the uniformity of the fiber structure at the stage of the raw yarn, that is, in the amorphous region. It depends on the cohesiveness of the molecular chains. In this respect, it is adopted as a normal spinning technique to reduce the structurally strained portion (such as a spherulite portion) and facilitate the molecular chain orientation to densify the aggregated structure. For example, when raising the temperature of the discharged polymer melt, lowering the temperature of the cold air given to the polymer melt, increasing the velocity of the cold air, giving the given cold air uniformly from the circumferential direction, or giving the cold air from one direction, the polymer melt We have responded by optimizing the spinneret arrangement that discharges, and lowering the single yarn denier.
This is because the take-up roll temperature, which is currently used industrially, is the glass transition point of the polymer (65-75 for polyamide).
It is an appropriate method in the so-called cold stretching method, in which the temperature is set at (° C).

In the above method, the fraction of the molecular chains accommodated in the amorphous portion is necessarily increased due to the decrease of spherulites.
However, at present, it is far from obtaining a uniform aggregation structure for uniformly stretching the molecular chains existing in the amorphous region by these methods alone. In particular, it is effective to raise the polymer melt temperature, but it causes a problem of polymer decomposition.

On the other hand, various methods have been proposed for realizing the absolute increase of the amorphous fraction in which the packing density of the molecular chains is as uniform as possible, which is referred to as increasing the toughness of the polyamide fiber. Judging from patents and academic papers, the technologies proposed other than the ones mentioned above are 1) increase the degree of polymerization of the polymer, 2) draw in a zone (non-contact type) at high temperature, and 3) reduce the spinning speed. Later, there are methods such as multi-stage drawing, 4) using a non-aqueous oil agent, and 5) positively steaming the discharged and cooled solidified yarn at about 140 ° C. to promote crystallization.

Item 5) contradicts the improvement in durability and fatigue resistance after the raw yarn is made into the final product. Although 2) depends on the degree of drawing, it realizes an absolute increase in the uniform density of the packing density of the molecular chains, and since the thread does not contact the medium such as rolls, it has a macro structure. Although defects (fluffs) are less likely to occur, they are extremely disadvantageous in terms of productivity, manufacturing equipment, and cost. In the case of 3), not only is it disadvantageous in terms of equipment and productivity, but it is more likely to come into contact with a medium such as a roll and structural defects due to friction are likely to occur. 4) has a problem in terms of work environment and proportional manufacturing cost.

Of course, although these methods are important technical areas, nylon 66 / having a constituent single yarn of 1.8d or less is used.
Nylon 6 blend fiber is not sufficient to solve the deterioration of physical properties over time due to the structural change due to the action of water, and the effect is very small without the method of the present invention.

[0031]

EXAMPLES Examples will be described below, but the invention is not limited thereto. The structure and characteristic evaluation method of the present invention will be described below. 1. Raw yarn light transmissivity Fiber is traversed in a uniform and parallel manner at a speed of 8.5 cm / min while rotating a metal plate with a thickness of 5 cm x 3 cm and a thickness of 2 mm at the number of rotations represented by formula (3). Thus, after two reciprocal windings, SZ-Σ90 manufactured by Nippon Denshoku Industries Co., Ltd. was used, and transmitted light was made incident on this plate in the vertical direction, and the transmittance was measured as an L * value.

Plate rotation speed (rpm) = 13744.5 / (total denier) --- (3) 2. Raw yarn light reflectivity A plate type sample similar to the above 1 was prepared using the same measuring group as the raw yarn transmittance, and 0-45 was applied to the same plate.
Measured by the ° method. 3. tan δ-T analysis Using a viscoelasticity measuring device (manufactured by Orientec: Rheovibron DDV-01FP type), temperature rising rate: 3 ° C./min, measurement frequency: 110 Hz, initial load: 0.15 g / d, vibration amplitude: The measurement is performed at 16.0 μm and sample length: 2 cm. 4. Fiber physical properties Using a Toyo Baldwin Tensilon RTA-100 type machine, fiber yarn length 20 cm, crosshead speed 2
It was measured at 00 mm / min. Note that toughness is strength ×
It shall be expressed in terms of elongation. 5. Moisture Concentration of Mixed Composition Using an electric titration type moisture measuring device (Mitsubishi CA-05 type) and a moisture vaporizing device (VA-05 type), a vaporization temperature of 208 ° C.,
N2 carrier gas flow rate 300ml / min, ENDS
ENS: 0.5 μg / sec, delay time: 5 minutes, background: a value measured on a chip with a sample weight of about 1 g under conditions of 0.05 or less. 6. Amino group end concentration 6 g of the polymer is accurately weighed to the third decimal place and dissolved in 50 cc of 90% phenol aqueous solution. After complete dissolution, the solution temperature is stabilized at 25 ° C. and titrated to pH 3 with a 0.05N hydrochloric acid aqueous solution. The drop of 0.05N hydrochloric acid aqueous solution at this time was recorded, and the polymer 1K was calculated by the following calculation formula.
The amino group terminal concentration per gram (milliequivalent / Kg is calculated).

Amino group terminal concentration = A × F × 50 / B A: 0.05 N-hydrochloric acid aqueous solution (ml) required for titration F: 0.05 N-hydrochloric acid aqueous solution factor B: Polymer weight (g) 7. Carboxyl group end concentration: 6 g of the polymer is accurately weighed to the third decimal place and dissolved in 50 cc of benzyl alcohol at 170 ° C.
After complete solution, 1 liter of benzyl alcohol, 5 g of phenolphthalein, 0.5 g of copper acetate, 12 g of titanium dioxide
Add 0.3 ml of the indicator prepared from. afterwards,
At the time when the 0,1N-NaO ethylene glycol solution was dropped, the liquid color became pink. 0,1N-Na at this time
The amount of OH ethylene glycol solution dropped is recorded, and the carboxyl group terminal concentration (milliequivalent / Kg) per 1 Kg of the polymer is calculated by the following formula.

Carboxyl group end concentration = A × F × 100 / BA A: 0,1N-NaOH ethylene glycol solution required for titration (ml) F: 0.05N-hydrochloric acid aqueous solution factor B: polymer weight (g)

[0035]

[Example 1, Comparative Example 1, 2] Amino end group concentration 7
6.5 (meq / kg), carboxyl end group concentration 4
6.0 (meq / kg) polyhexamethylene adipamide and Roam and Haas polyglutarimide EX
L4140 [Mn: 90,000, imidization ratio: 56.1
%,] As a chip and mixed at a ratio of 95: 5, water is added to this mixed composition at a concentration of 2000 ± 100 ppm, melt-discharged at a spinning temperature of 280 ° C., and the collected fiber is continuously drawn. Then, a fiber of 7 denier and 5 filaments was obtained.

Further, as Comparative Example 1, the above Example 1 is used.
Roam and Haas with polyhexamethylene adipamide having similar amino end group and carboxyl end group concentrations
Polyglutarimide EXL4140 [Mn: 9
0000, imidization ratio: 56.1%,] was mixed as a chip at a ratio of 95: 5, and 1000 was added to this mixture.
Water is added at a concentration of ± 100 ppm, and the spinning temperature is 280.
The fibers were melt-discharged at 0 ° C., and the fibers collected were continuously drawn to obtain fibers of 7 denier and 5 filaments.

As Comparative Example 2, the above Example 1
Only polyhexamethylene adipamide having the same amino terminal group concentration and carboxyl terminal group concentration as in Example 1 was spun under the same conditions as in Example 1 above. This fiber was treated in a pan shape in an environment of 45 ° C. and 85% RH for 7 days, and the physical properties of the fiber before and after aging were measured.
The sample of No. 1 was not only confirmed to have extremely good stability over time as shown in Table 1, but also had a high physical property retention rate (strength, elongation) after time, and the transparency of the obtained fiber was remarkably high. Has improved.

[0038]

Example 2 Amino end group concentration 76.5 (meq /
kg), carboxyl end group concentration 46.0 (meq /
kg) polyhexamethylene adipamide and Roam and H
aas polyglutarimide EXL4151 [M
n: 145000, imidization ratio: 76.6%] as a chip, and mixed at a ratio of 95: 5, and water is added to this mixture at a concentration of 2000 ± 100 ppm and melted at a spinning temperature of 280 ° C. The discharged and collected fibers were continuously stretched to obtain fibers of 7 denier and 5 filaments.

This fiber is formed into a bun shape at 45 ° C. × 85.
When the fiber properties were measured before and after the treatment for 7 days in a% RH environment, the sample of Example 1 was confirmed to have extremely good stability over time, as shown in Table 1, and the obtained fiber was transparent. As shown in Table 1, the sex has also improved markedly.

[0040]

Comparative Example 3 Amino end group concentration 46.7 (meq /
kg), carboxyl end group concentration 80.5 (meq /
kg) polyhexamethylene adipamide and Roam and H
aas polyglutarimide EXL4140 [M
n: 90000, imidization ratio: 56.1%,] as a chip and mixed at a ratio of 95: 5, and to this mixture,
Moisture was applied at a concentration of 1000 ± 100 ppm, melt-discharged at a spinning temperature of 280 ° C., and the collected fiber was continuously drawn to obtain a fiber of 7 denier and 5 filaments.

This fiber is formed into a bun shape at 45 ° C. × 85.
When the fiber properties were measured before and after the treatment for 7 days in a% RH environment, the sample of Example 3 was
Compared with No. 2, as shown in Table 1, not only the stability over time and the transparency are lowered, but also the spinning stability is low, yarn breakage occurs, and the mechanical properties of the obtained fiber are also low. I wasn't satisfied.

As described above, the polyhexamethylene adipamide fiber of the present invention has improved transparency, toughness and dyeability, has a relatively soft feeling, and eliminates the drawbacks of the aliphatic polyamide fiber. it can.

[0043]

[Table 1]

[0044]

EFFECTS OF THE INVENTION The polyhexamethylene adipamide fiber of the present invention is highly transparent, has excellent stability over time in physical properties under high humidity and high temperature atmosphere, and requires maintenance of high toughness and soft texture. In addition to achieving improved functionality in the fields of garments, legs and general industrial materials, the processing stability is guaranteed.

Further, the manufacturing method of the present invention uses nylon 66
Established a uniform melt mixing method of polyglutarimide with
It is possible to provide a polyhexamethylene adipamide-based fiber, which is a blend fiber of nylon 66 and polyglutarimide having a single yarn denier of 1.8 d or less.

Claims (2)

[Claims] 1. An amino terminal group concentration A (milliequivalent / kg;
meq / kg) and carboxyl end group concentration B (meq / kg)
a mixture of 99 to 75 parts by weight of polyhexamethylene adipamide having a relationship of A ≧ 1.2 × B and 1 to 25 parts by weight of polyglutarimide having an acid anhydride group represented by the following general formula (1). A blend fiber composed of a composition, wherein the fiber has (a) constituent single yarn denier of 1.8 d or less,
(B) 7 in an atmosphere of 45 ° C and 85% relative humidity under tension
The β-dispersion peak temperature Tβ appearing in the tan δ-temperature (T) curve of the fiber after the day treatment and before and after the treatment, and its value t
When the difference in an δβ is 3 ° C or less and 0.005 or less,
(C) The raw yarn transmittance and the raw yarn reflectance are expressed by the following equation (2).
A polyhexamethylene adipamide-based fiber characterized by satisfying (3). [Chemical 1] Raw yarn transmittance (%)>-15.6 × Log (total denier) +35.0 (2) However, 0.1 ≦ (total denier) ≦ 30. Raw yarn reflectance (%) <-58.7 x (raw yarn transmittance (%)) +151.4 (3) 2. A method for producing a blended fiber of polyhexamethylene adipamide and polyglutarimide having an acid anhydride group represented by the following general formula (1), which comprises: Amino end group concentration A (milliequivalent / kg; meq / kg) and carboxyl end group concentration B
The relationship of (meq / kg) is A ≧ 1.2 × B, and 1600 to 5000 ppm with respect to a mixed composition of 99 to 75 parts by weight of the polyhexamethylene adipamide and 1 to 25 parts by weight of the polyglutarimide. A polyhexamethylene adipamide-based fiber, characterized in that the fiber is melt-discharged at a temperature of 270 ° C. or higher to form a fiber, and the discharged fiber is directly drawn or the drawn fiber is subsequently drawn. Manufacturing method. [Chemical 2]