WO2009084390A1 - 耐炎化繊維と炭素繊維の製造方法 - Google Patents
耐炎化繊維と炭素繊維の製造方法 Download PDFInfo
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- WO2009084390A1 WO2009084390A1 PCT/JP2008/072381 JP2008072381W WO2009084390A1 WO 2009084390 A1 WO2009084390 A1 WO 2009084390A1 JP 2008072381 W JP2008072381 W JP 2008072381W WO 2009084390 A1 WO2009084390 A1 WO 2009084390A1
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- D—TEXTILES; PAPER
- D01—NATURAL OR MAN-MADE THREADS OR FIBRES; SPINNING
- D01F—CHEMICAL FEATURES IN THE MANUFACTURE OF ARTIFICIAL FILAMENTS, THREADS, FIBRES, BRISTLES OR RIBBONS; APPARATUS SPECIALLY ADAPTED FOR THE MANUFACTURE OF CARBON FILAMENTS
- D01F9/00—Artificial filaments or the like of other substances; Manufacture thereof; Apparatus specially adapted for the manufacture of carbon filaments
- D01F9/08—Artificial filaments or the like of other substances; Manufacture thereof; Apparatus specially adapted for the manufacture of carbon filaments of inorganic material
- D01F9/12—Carbon filaments; Apparatus specially adapted for the manufacture thereof
- D01F9/14—Carbon filaments; Apparatus specially adapted for the manufacture thereof by decomposition of organic filaments
- D01F9/20—Carbon filaments; Apparatus specially adapted for the manufacture thereof by decomposition of organic filaments from polyaddition, polycondensation or polymerisation products
- D01F9/21—Carbon filaments; Apparatus specially adapted for the manufacture thereof by decomposition of organic filaments from polyaddition, polycondensation or polymerisation products from macromolecular compounds obtained by reactions only involving carbon-to-carbon unsaturated bonds
- D01F9/22—Carbon filaments; Apparatus specially adapted for the manufacture thereof by decomposition of organic filaments from polyaddition, polycondensation or polymerisation products from macromolecular compounds obtained by reactions only involving carbon-to-carbon unsaturated bonds from polyacrylonitriles
- D01F9/225—Carbon filaments; Apparatus specially adapted for the manufacture thereof by decomposition of organic filaments from polyaddition, polycondensation or polymerisation products from macromolecular compounds obtained by reactions only involving carbon-to-carbon unsaturated bonds from polyacrylonitriles from stabilised polyacrylonitriles
Definitions
- the present invention relates to a method for producing high-strength carbon fibers and a method for producing flame-resistant fibers useful as an intermediate raw material.
- composite materials using carbon fibers as reinforcing fibers are light and have excellent mechanical properties such as high strength, and thus have been widely used as structural materials for aircraft and the like.
- These composite materials are molded, for example, from a prepreg, which is an intermediate product in which a reinforcing fiber is impregnated with a matrix resin, through molding and processing steps such as heating and pressing. Therefore, in order to obtain a desired composite material, it is necessary to employ an optimum material or molding / processing means for each.
- the carbon fiber, which is a reinforcing fiber may be required to have higher strength. For example, when it is intended to reduce the weight of a composite material for aircraft, it is necessary to increase the elasticity while maintaining the strength of the carbon fiber. However, the carbon fiber generally becomes brittle as the elastic modulus increases. Increased and decreased elongation, it is difficult to obtain a composite material having high composite performance.
- an oxidation treatment flame resistance treatment
- the method of carbonizing and manufacturing in 300 degreeC or more inert gas atmosphere is known.
- the fiber processing method in the flameproofing process greatly affects the strength development of the carbon fiber, and many studies have been conducted for a long time.
- the fiber density is in the range of 1.30 to 1.42 g / cm 3 produced in the range of ⁇ 10 to + 10% (stretch ratio 0.9 to 1.1) in the flameproofing process.
- High-strength carbon fibers can be obtained by carbonizing the flameproof treated yarn (see Patent Document 6), and an elongation rate of 3% or more (stretching of 1.03 or more) until the fiber density reaches 1.22 g / cm 3.
- a high strength carbon fiber can be obtained by performing a flameproofing treatment while substantially suppressing subsequent shrinkage, followed by carbonization (see Patent Document 7), or the fiber density is After performing the flameproofing treatment at an elongation rate of 3% or more (stretching ratio of 1.03 or more) until reaching 1.22 g / cm 3 , further at an elongation ratio of 1% or more (stretching ratio of 1.01 or more).
- the strand strength is 460k by drawing and then carbonizing.
- the f / mm 2 or more carbon fiber is obtained (see Patent Document 8) it has been reported for a long time.
- An object of the present invention is to provide a method for producing a high-strength and high-elasticity carbon fiber that is suitable for a composite material requiring particularly high composite performance.
- the present inventors use a polyacrylic precursor fiber that has been conventionally known as described above.
- the flameproofing process and / or the carbonization (including graphitization) process is improved and the present invention has been achieved from a completely new viewpoint.
- a flame resistant fiber when producing a flame resistant fiber by subjecting a polyacrylic precursor fiber to a flame resistant treatment in an oxidizing atmosphere, (1) as a pretreatment for the flame resistant treatment,
- the degree of cyclization of the precursor fiber (I 1620 / I 2240 ) measured with a Fourier transform infrared spectrophotometer (FT-IR) at a temperature of 220 to 260 ° C. and a load of 0.58 g / tex or less. )
- FT-IR Fourier transform infrared spectrophotometer
- the precursor fiber is initially stretched at a load of 2.7 to 3.5 g / tex and subsequently (3) 200 to 280 ° C., preferably 240 to 250 ° C. in an oxidizing atmosphere.
- the draw ratio is 0.85 to 1.3 times, preferably 0.95.
- the density until the range of 1.3 ⁇ 1.5g / cm 3 a method for producing a flame-resistant fibers, comprising treating flame the precursor fibers.
- Another aspect of the present invention is a method for producing carbon fiber, characterized in that the polyacrylic precursor fiber obtained as described above is subsequently carbonized by a known method.
- the carbonization treatment includes so-called graphitization treatment.
- Still another embodiment of the present invention is a carbon fiber itself obtained by the production method described above and having a tensile strength of 5880 MPa or more and an elastic modulus of 308 GPa or more.
- the fiber when the polyacrylic precursor fiber is subjected to flameproofing treatment, as a pretreatment, the fiber is contracted once to discharge moisture in the fiber and make the structure of the fiber voidless. As a result, it is possible to produce a flameproof fiber with reduced internal defects. And when this is used as an intermediate raw material and carbonized by a conventionally known method, a carbon fiber having high strength and high elasticity can be obtained. If the conditions are appropriately set, a carbon fiber having a tensile strength of 5880 MPa or more and an elastic modulus of 308 GPa or more and an improved elastic modulus while maintaining high strength can be obtained. And since the composite material obtained from such carbon fiber and matrix resin has excellent composite properties, it is possible to obtain a composite material with higher performance than conventional ones. In fields and the like, it can be used as a composite material that is lightweight and suitable for structural materials.
- conventionally known polyacrylic fibers can be used without any limitation as the polyacrylic precursor fibers used in the method for producing flame-resistant fibers or carbon fibers.
- polyacrylic fibers having an orientation degree of 90.5% or less by wide-angle X-ray diffraction (diffraction angle 17 °) are preferable.
- a carbon fiber raw material (precursor fiber) is obtained by spinning a spinning solution obtained by singly or copolymerizing a monomer containing acrylonitrile at 90% by weight or more, preferably 95% by weight or more.
- the spinning method either a wet or dry wet spinning method can be used, but in order to obtain a carbon fiber excellent in adhesion due to an anchor effect with a resin, a wet fiber that has a pleat on the surface is obtained.
- a spinning method is more preferred.
- the fiber obtained by the wet spinning method is then washed with water, dried and drawn to obtain a carbon fiber raw material.
- the monomer to be copolymerized methyl acrylate, itaconic acid, methyl methacrylate, acrylic acid and the like are preferable.
- the polyacrylic precursor fiber thus obtained can be subjected to flameproofing treatment according to the method for producing flameproofed fiber of the present invention to obtain flameproofed fiber.
- the flame-resistant fiber can be carbonized (including so-called graphitization treatment if necessary) to obtain a high-strength, high-elasticity carbon fiber.
- the usual flameproofing treatment for the polyacrylic precursor fiber is performed in an oxidizing atmosphere such as heated air within a temperature range of 200 to 280 ° C., preferably 240 to 250 ° C. At this time, the precursor fiber is generally stretched or shrunk in a range of a stretch ratio of 0.85 to 1.3 times. However, in order to obtain a high-strength and high-elasticity carbon fiber, 0.95 times More preferably. With this flameproofing treatment, a flameproof fiber having a fiber density of 1.3 to 1.5 g / cm 3 is obtained, but the tension applied to the yarn at the time of flameproofing is not particularly limited.
- the polyacrylic precursor fiber shrinks as the processing temperature increases unless it is stretched. Therefore, the stretching ratio can be adjusted by adjusting the stretching stress and performing a stretching treatment.
- a draw ratio of 1.0 indicates that a drawing stress is applied to the fiber, but shrinkage and drawing are balanced and the length before drawing and after drawing are the same.
- pre-treatment is first performed in the flameproofing treatment. That is, first, as a pretreatment of (1) flameproofing treatment, the precursor fiber is subjected to a temperature of 220 to 260 ° C., preferably 230 to 245 ° C., and a load of 0.58 g / tex or less, preferably 0.55 g.
- the cyclization degree (I 1620 / I 2240 ) of the precursor fiber measured by a Fourier transform infrared spectrophotometer (FT-IR) is not more than 7%, preferably not more than 6.6%. Shrink under conditions.
- the weight does not sag and is within the above range.
- the degree of cyclization of the precursor fiber (I 1620 / I 2240 ) measured with a Fourier transform infrared spectrophotometer (FT-IR) is a value used as an indicator of the flameproofing reaction, This shows the degree of reaction in which the nitrile group appearing in I 2240 opens as the flame resistance progresses and reacts with the naphthyridine ring appearing in I 1620 .
- the precursor fiber pretreated as described above is then subjected to (2) an oxidizing atmosphere of 230 to 260 ° C., preferably 240 to 250 ° C., and the degree of cyclization of the precursor fiber is 27 % And the density does not exceed 1.2 g / cm 3 , the precursor fiber is initially loaded with a load of 2.7 to 3.5 g / tex, preferably 2.8 to 3.0 g / tex. Stretch. At this time, if the load is outside this range, the filament may be cut in the process, which is not preferable because the process becomes unstable and the productivity deteriorates.
- the precursor fiber pretreated in the step (1) is initially stretched under the above conditions in the step (2). Subsequently, the precursor fiber is subjected to normal flameproofing treatment. That is, (3) in an oxidizing atmosphere at 200 to 280 ° C., preferably 240 to 250 ° C., a draw ratio of 0.85 to 1.3 times, preferably 0.95 times or more, and a density of 1.3 The precursor fiber is flameproofed to obtain flameproofed fiber until it is in the range of ⁇ 1.5 g / cm 3 .
- the flameproofing treatment of the polyacrylic precursor fiber is usually performed in an atmosphere gas circulation type heating furnace while the precursor fiber passes through the supply roller and the take-off roller a plurality of times while being stretched or contracted by applying a predetermined load. Is done by letting And since a polyacrylic precursor fiber is normally processed in a precursor fiber bundle (strand) state, it is preferable for the stability of a process that a strand is in the state converged as much as possible. In particular, in the case of a thick strand having 20,000 or more filaments, it is preferable to maintain the convergence of the strand by applying an appropriate oil agent.
- Densification of the precursor fiber in the step (1) in the present invention is essential for the flame resistance treatment of the polyacrylic precursor fiber containing moisture.
- the fiber which has not started the flameproofing reaction has a sparse structure, and when heated, moisture in the fiber evaporates and is discharged out of the fiber.
- the flameproofing treatment occurs from the fiber surface, if the flameproofing reaction starts before the moisture in the fiber is completely removed, the surface structure formed by the flameproofing reaction inhibits the discharge of moisture. This insufficiently discharged water vapor forms voids in the fiber, resulting in a structural defect, resulting in a problem that the strength of the resulting flame resistant fiber is reduced.
- the Fourier transform infrared spectrophotometer before the flameproofing treatment, the Fourier transform infrared spectrophotometer is subjected to certain conditions, that is, the precursor fiber, the temperature is in the range of 220 to 260 ° C., the load is 0.58 g / tex or less.
- the degree of cyclization of the precursor fiber I 1620 / I 2240
- the precursor fiber is densified to some extent, and the moisture in the fiber is sufficiently It eliminates the generation of voids that can be structural defects inside the fiber.
- the precursor fiber when the precursor fiber is densified, its molecular structure becomes loose. After that, if the flameproofing treatment is performed under normal conditions, a high-strength, high-elasticity carbon fiber that can be finally satisfied cannot be obtained. There was another problem. Therefore, in the present invention, in the initial stage of the flameproofing treatment process, the cyclization degree of the precursor fiber does not exceed 27% and the density is 1.2 g / cm 3 in an oxidizing atmosphere of 230 to 260 ° C. There is a contrivance that the precursor fiber is initially stretched at a load of 2.7 to 3.5 g / tex within a range not exceeding. It has been found that this problem can be solved by such means.
- the flameproofing treatment within the range of normal conditions is performed until the density is in the range of 1.3 to 1.5 g / cm 3 .
- the method of the present invention as described above is particularly advantageously applied in terms of production cost and quality when the number of filaments is 20,000 or more and the degree of orientation measured by wide-angle X-ray diffraction is 90% or less.
- This is a case of a polyacrylic carbon fiber precursor fiber bundle containing 20 to 50% by weight of water per unit weight.
- the flame-resistant fiber obtained by flame-proofing under the above conditions is obtained by carbonizing this flame-resistant fiber because the processability is good and the productivity is high, and the degree of orientation is structurally improved by stretching.
- the strength of the carbon fiber is high.
- the flameproofing treatment is performed in a flameproofing furnace in an oxidizing atmosphere including the initial stretching step.
- a heating furnace different from the flameproofing furnace before applying the oil agent it is convenient to perform the pretreatment process of the flameproofing treatment in a heating furnace different from the flameproofing furnace before applying the oil agent.
- the pretreatment process and the flameproofing process of the flameproofing process can be continuously performed in the same heating furnace (flameproofing furnace).
- a carbon fiber when a carbon fiber is produced by subjecting a polyacrylic precursor fiber to a flameproofing treatment in an oxidizing atmosphere and then a carbonization treatment in an inert atmosphere, (1) flameproofing.
- the precursor fiber is measured with a Fourier transform infrared spectrophotometer (FT-IR) at a temperature in the range of 220 to 260 ° C. and a load of 0.58 g / tex or less.
- FT-IR Fourier transform infrared spectrophotometer
- the body fibers were shrunk under conditions where the degree of cyclization (I 1620 / I 2240 ) did not exceed 7%, and then (2) in an oxidizing atmosphere of 230 to 260 ° C., the degree of cyclization of the precursor fibers was 27 %, And the density of the precursor fiber does not exceed 1.2 g / cm 3.
- the precursor fiber is initially stretched at a load of 2.7 to 3.5 g / tex, and subsequently (3) in an oxidizing atmosphere. 200 to 280 ° C., preferably 240 to 250 In draw ratio from 0.85 to 1.3 times, preferably in the range of more than 0.95 times the density until the range of 1.3 ⁇ 1.5g / cm 3, oxidization processing the precursor fibers And then carbonizing the carbon fiber.
- the conditions and means for flameproofing the polyacrylic precursor fiber in an oxidizing atmosphere are as described above for the method for producing flameproof fiber.
- the flame-resistant fiber is then carbonized to obtain the carbon fiber of the present invention.
- carbonization treatment as described below is usually performed, and the carbonization treatment in the present invention also means such treatment.
- the flame resistant fiber is subjected to a primary stretching treatment and a secondary stretching treatment in an inert atmosphere within a temperature range of 300 to 900 ° C., preferably 300 to 550 ° C. That is, first, a primary stretching process is performed at a stretching ratio of 1.03 to 1.07, and then a secondary stretching process is performed at a stretching ratio of 0.9 to 1.01 to obtain a fiber density of 1.4 to 1.7 g / cm. 3 of the first carbonized fiber is obtained.
- the density of the fiber reaches 1.5 g / cm 3 in the range from the point when the elastic modulus of the flameproof fiber decreases to the minimum value until it increases to 9.8 GPa.
- the stretching process is preferably performed at a stretching ratio of 0.9 to 1.01 within a range in which the density of the fiber after the primary stretching process continues to increase during the secondary stretching process.
- the crystals are densified without growing, the formation of voids can be suppressed, and finally high-strength carbon fibers having high density can be obtained.
- the first carbonization treatment step can be carried out continuously or separately in one furnace or two or more furnaces.
- the first carbonization treatment fiber is divided into a primary treatment and a secondary treatment in an inert atmosphere within a temperature range of 800 to 2100 ° C., preferably 1000 to 1450 ° C.
- a second carbonized fiber In the primary treatment, it is preferable to stretch the fiber in a range where the density of the first carbonized fiber continues to increase during the primary treatment, and in a range where the nitrogen content of the fiber is 10% by mass or more.
- the secondary treatment it is preferable to stretch the fiber in a range where the density of the primary treated fiber does not change or decreases.
- the elongation of the second carbonized fiber is 2.0% or more, more preferably 2.2% or more.
- the diameter of the second carbonized fiber is preferably 5 to 6.5 ⁇ m.
- these baking processes can be processed continuously with a single facility or with several facilities, and are not particularly limited.
- the second carbonization-treated fiber is further carbonized or graphitized at 1500 to 2100 ° C., preferably 1550 to 1900 ° C.
- the third carbonized fiber is subsequently subjected to a surface treatment.
- a gas phase or a liquid phase treatment can be used, but surface treatment by electrolytic treatment is preferable from the viewpoint of easy process control and productivity.
- the electrolyte solution used for an electrolytic treatment is not specifically limited,
- the aqueous solution of the conventionally well-known inorganic acid, organic acid, alkali, or those salts can be used. Specific examples include nitric acid, ammonium nitrate, sulfuric acid, ammonium sulfate, sodium hydroxide, and the like.
- the surface-treated fiber is subsequently subjected to sizing treatment.
- the sizing method can be carried out by a conventionally known method, and the sizing agent is preferably used after changing its composition as appropriate according to the application, and after uniformly adhering.
- the carbon fiber of the present invention having a tensile strength of 5880 MPa or more and an elastic modulus of 308 GPa or more is obtained.
- the degree of cyclization (I 1620 / I 2240 ) is measured by KBr method using Magna-IR ⁇ 550 manufactured by Thermo Fisher Scientific, and the peak intensity of nitrile group appearing in I 2240 and appearing in I 1620 It calculated
- the density was measured by deaeration treatment in acetone by a liquid replacement method (JIS R7601).
- the resin-impregnated strand strength and elastic modulus of carbon fiber were measured by the method defined in JIS R7601.
- the carbon fiber sizing agent was removed by Soxhlet treatment with acetone for 3 hours, and then the fiber was air-dried.
- Examples 1 to 3 Comparative Examples 1 to 9
- a copolymer spinning stock solution of 95% by weight of acrylonitrile / 4% by weight of methyl acrylate / 1% by weight of itaconic acid is wet-spun by a conventional method so that the total draw ratio becomes 14 times after washing, oiling and drying. Steam drawing was performed to obtain a precursor fiber having a filament number of 24,000 having a fineness of 1733 tex. The precursor fiber thus obtained was processed in the production process described later to obtain a flame resistant fiber of the present invention.
- Step (1) As a pretreatment for the flameproofing treatment, the precursor fiber is changed in a pretreatment furnace at a temperature in the range of 230 to 245 ° C. under a stretching condition as shown in Table 1, Pretreatment was performed.
- the degree of cyclization (I 1620 / I 2240 ) of the precursor fiber measured with a Fourier transform infrared spectrophotometer (FT-IR) was as shown in Table 1.
- Step (2) The precursor fiber pretreated as described above was used as shown in Table 1 until the specific gravity reached 1.20 using a hot-air circulating flameproofing furnace set at 240 to 250 ° C. Initial stretching was performed by changing the load under stretching conditions. The degree of cyclization of the obtained fiber was as shown in Table 1.
- Step (3) The initially drawn precursor fiber was subsequently drawn in the same flameproofing furnace in an oxidizing atmosphere set at 240 to 250 ° C., as shown in Table 1, with a draw ratio of 1.0 to The flameproofing treatment was performed until the density was in the range of 1.3 to 1.5 g / cm 3 within a range of 1.01 times.
- the various flameproof fibers obtained above were first carbonized in a nitrogen atmosphere at a furnace temperature distribution of 300 to 580 ° C. and a draw ratio of 1.01 times, and then within a temperature range of 1000 to 1450 ° C. A second carbonization was performed. Further, the obtained second carbonized fiber is subjected to third carbonization within a temperature range of 1400 to 1850 ° C., and after surface treatment and sizing treatment, carbon having physical property values (strand performance) shown in Table 2 is obtained. Fiber was obtained.
- Comparative Examples 7 and 8 do not satisfy the condition that initial stretching is performed at a load of 2.7 to 3.5 g / tex in the step (2).
- Comparative Example 9 does not satisfy both the condition that the initial stretching is performed at a load of 2.7 to 3.5 g / tex in the step (2) and the condition that the density does not exceed 1.2 g / cm 3 .
- a high-strength and high-elasticity carbon fiber having a tensile strength of 5880 MPa or more and an elastic modulus of 308 GPa or more can be obtained.
- Such high-strength and high-elasticity carbon fibers are suitable for producing a composite material having high composite performance required for aircraft and the like.
- the flame-resistant fiber of the present invention is useful as an intermediate raw material for producing the high-strength and high-elasticity carbon fiber as described above.
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Abstract
Description
第一炭素化処理工程においては、耐炎化繊維を、不活性雰囲気中で、300~900℃、好ましくは300~550℃の温度範囲内で、一次延伸処理と二次延伸処理を行う。即ち、先ず、1.03~1.07の延伸倍率で一次延伸処理し、次いで0.9~1.01の延伸倍率で二次延伸処理して、繊維密度1.4~1.7g/cm3の第一炭素化処理繊維を得る。第一炭素化処理工程において、一次延伸処理では、耐炎化繊維の弾性率が極小値まで低下した時点から9.8GPaに増加するまでの範囲、同繊維の密度が1.5g/cm3に達するまでの範囲で、1.03~1.07の延伸倍率で延伸処理を行うのが好ましい。二次延伸処理においては、一次延伸処理後の繊維の密度が二次延伸処理中に上昇し続ける範囲で、0.9~1.01倍の延伸倍率で延伸処理を行うのが好ましい。かかる条件を採用すると、結晶が成長することなく、緻密化され、ボイドの生成も抑制でき、最終的に高い緻密性を有した高強度炭素繊維を得ることができる。上記第一炭素化処理工程は、一つの炉若しくは二つ以上の炉で、連続的若しくは別々に処理することができる。
第二炭素化処理工程においては、上記第一炭素化処理繊維を、不活性雰囲気中で、800~2100℃、好ましくは1000~1450℃の温度範囲内で、一次処理と二次処理とに分けて延伸処理して、第二炭素化処理繊維を得る。一次処理では、第一炭素化処理繊維の密度が一次処理中上昇し続ける範囲、同繊維の窒素含有量が10質量%以上の範囲で、同繊維を延伸処理するのが好ましい。二次処理においては、一次処理繊維の密度が変化しない又は低下する範囲で、同繊維を延伸処理するのが好ましい。第二炭素化処理繊維の伸度は2.0%以上、より好ましくは2.2%以上である。また、第二炭素化処理繊維の直径は、5~6.5μmであるのが好ましい。また、これら焼成工程は、単一設備で連続して処理することも、数個の設備で連続して処理することも可能であり、特に限定されるものではない。
第三炭素化処理工程においては、上記第二炭素化処理繊維を1500~2100℃、好ましくは、1550~1900℃で更に炭素化又は黒鉛化処理する。
上記第三炭素化処理繊維は、引き続いて表面処理を施こされる。表面処理には気相、液相処理も用いることができるが、工程管理の簡便さと生産性を高める点から、電解処理による表面処理が好ましい。また電解処理に使用される電解液は、特に限定されるものではなく、従来の公知の無機酸、有機酸、アルカリ又はそれらの塩の水溶液を使用することができる。具体的には、例えば、硝酸、硝酸アンモニウム、硫酸、硫酸アンモニウム、水酸化ナトリウム等が挙げられる。
上記表面処理繊維は、引き続いてサイジング処理を施こされる。サイジング方法は、従来の公知の方法で行うことができ、サイジング剤は、用途に即して適宜組成を変更して使用し、均一付着させた後に、乾燥することが好ましい。
アクリロニトリル95重量%/アクリル酸メチル4重量%/イタコン酸1重量%よりなる共重合体紡糸原液を、常法により湿式紡糸し、水洗・オイリング・乾燥後、トータル延伸倍率が14倍になるようにスチーム延伸を行い、1733texの繊度を有するフィラメント数24,000の前駆体繊維を得た。かくして得られた前駆体繊維を後述する製造工程で処理し、本発明の耐炎化繊維を得た。
Claims (5)
- ポリアクリル系前駆体繊維を酸化性雰囲気中で耐炎化処理して耐炎化繊維を製造するに際し、(1)耐炎化処理の前処理として、該前駆体繊維を、温度が220~260℃の範囲で荷重が0.58g/tex以下で、フーリエ変換赤外分光光度計(FT-IR)で測定される該前駆体繊維の環化度(I1620/I2240)が7%を越えない条件で収縮させ、その後、(2)230~260℃の酸化性雰囲気中で、該前駆体繊維の環化度が27%を越えず且つ密度が1.2g/cm3を超えない範囲で、該前駆体繊維を、荷重が2.7~3.5g/texで初期延伸し、引き続いて(3)酸化性雰囲気中で200~280℃で、延伸倍率0.85~1.3倍の範囲で、密度が1.3~1.5g/cm3の範囲になるまで、該前駆体繊維を耐炎化処理することを特徴とする耐炎化繊維の製造方法。
- ポリアクリル系前駆体繊維が、フィラメント数が20,000本以上で、広角X線回折で測定される配向度が90%以下であり、且つ、単位重量当たり20~50重量%の水分を含むポリアクリル系炭素繊維前駆体繊維束であることを特徴とする請求項1記載の耐炎化繊維の製造方法。
- ポリアクリル系前駆体繊維を酸化性雰囲気中で耐炎化処理し、その後、不活性雰囲気中で炭素化処理することによって炭素繊維を製造するに際し、(1)耐炎化処理の前処理として、該前駆体繊維を、温度が220~260℃の範囲で荷重が0.58g/tex以下で、フーリエ変換赤外分光光度計(FT-IR)で測定される該前駆体繊維の環化度(I1620/I2240)が7%を越えない条件で収縮させ、その後、(2)230~260℃の酸化性雰囲気中で、該前駆体繊維の環化度が27%を越えず且つ密度が1.2g/cm3を超えない範囲で、該前駆体繊維を、荷重が2.7~3.5g/texで初期延伸し、引き続いて(3)酸化性雰囲気中で200~280℃で、延伸倍率0.85~1.3倍の範囲で、密度が1.3~1.5g/cm3の範囲になるまで、該前駆体繊維を耐炎化処理し、その後、炭素化処理することを特徴とする炭素繊維の製造方法。
- ポリアクリル系前駆体繊維が、フィラメント数が20,000本以上で、広角X線回折で測定される配向度が90%以下であり、且つ、単位重量当たり20~50重量%の水分を含むポリアクリル系炭素繊維前駆体繊維束であることを特徴とする請求項3記載の炭素繊維の製造方法。
- 請求項3又は4記載の製造方法で得られた、引張り強度が5880MPa以上で、弾性率が308GPa以上の炭素繊維。
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