JPH0413450B2 - - Google Patents
Info
- Publication number
- JPH0413450B2 JPH0413450B2 JP61012848A JP1284886A JPH0413450B2 JP H0413450 B2 JPH0413450 B2 JP H0413450B2 JP 61012848 A JP61012848 A JP 61012848A JP 1284886 A JP1284886 A JP 1284886A JP H0413450 B2 JPH0413450 B2 JP H0413450B2
- Authority
- JP
- Japan
- Prior art keywords
- pitch
- shear stress
- cross
- spinning
- sectional
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired - Lifetime
Links
- 229920000049 Carbon (fiber) Polymers 0.000 claims description 41
- 239000004917 carbon fiber Substances 0.000 claims description 41
- VNWKTOKETHGBQD-UHFFFAOYSA-N methane Chemical compound C VNWKTOKETHGBQD-UHFFFAOYSA-N 0.000 claims description 19
- 239000000463 material Substances 0.000 claims description 12
- 238000004519 manufacturing process Methods 0.000 claims description 6
- 238000000034 method Methods 0.000 claims description 4
- 239000011295 pitch Substances 0.000 description 53
- 238000009987 spinning Methods 0.000 description 27
- 239000000835 fiber Substances 0.000 description 17
- 230000007547 defect Effects 0.000 description 16
- 238000006068 polycondensation reaction Methods 0.000 description 10
- 230000000052 comparative effect Effects 0.000 description 9
- 238000003763 carbonization Methods 0.000 description 6
- 230000000694 effects Effects 0.000 description 5
- 238000001878 scanning electron micrograph Methods 0.000 description 5
- MWPLVEDNUUSJAV-UHFFFAOYSA-N anthracene Chemical compound C1=CC=CC2=CC3=CC=CC=C3C=C21 MWPLVEDNUUSJAV-UHFFFAOYSA-N 0.000 description 4
- 239000011294 coal tar pitch Substances 0.000 description 4
- 238000010438 heat treatment Methods 0.000 description 4
- 239000002994 raw material Substances 0.000 description 4
- 241000234282 Allium Species 0.000 description 3
- 235000002732 Allium cepa var. cepa Nutrition 0.000 description 3
- UHOVQNZJYSORNB-UHFFFAOYSA-N Benzene Chemical compound C1=CC=CC=C1 UHOVQNZJYSORNB-UHFFFAOYSA-N 0.000 description 3
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 3
- 238000010586 diagram Methods 0.000 description 3
- 238000005516 engineering process Methods 0.000 description 3
- 230000000704 physical effect Effects 0.000 description 3
- SMWDFEZZVXVKRB-UHFFFAOYSA-N Quinoline Chemical compound N1=CC=CC2=CC=CC=C21 SMWDFEZZVXVKRB-UHFFFAOYSA-N 0.000 description 2
- 239000011300 coal pitch Substances 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 239000007789 gas Substances 0.000 description 2
- 229910002804 graphite Inorganic materials 0.000 description 2
- 239000010439 graphite Substances 0.000 description 2
- 239000011261 inert gas Substances 0.000 description 2
- 230000001788 irregular Effects 0.000 description 2
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 1
- 238000004220 aggregation Methods 0.000 description 1
- 230000002776 aggregation Effects 0.000 description 1
- 125000003118 aryl group Chemical group 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 150000001721 carbon Chemical class 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 239000000805 composite resin Substances 0.000 description 1
- 230000002542 deteriorative effect Effects 0.000 description 1
- 229910001873 dinitrogen Inorganic materials 0.000 description 1
- 239000000945 filler Substances 0.000 description 1
- 238000005087 graphitization Methods 0.000 description 1
- 238000002074 melt spinning Methods 0.000 description 1
- 239000011259 mixed solution Substances 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 150000002894 organic compounds Chemical class 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 239000011301 petroleum pitch Substances 0.000 description 1
- 229920002239 polyacrylonitrile Polymers 0.000 description 1
- 239000002243 precursor Substances 0.000 description 1
- 238000000197 pyrolysis Methods 0.000 description 1
- 230000035484 reaction time Effects 0.000 description 1
- 229920005989 resin Polymers 0.000 description 1
- 239000011347 resin Substances 0.000 description 1
- 238000010008 shearing Methods 0.000 description 1
- 239000002904 solvent Substances 0.000 description 1
- 238000003756 stirring Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 229920002994 synthetic fiber Polymers 0.000 description 1
- 239000012209 synthetic fiber Substances 0.000 description 1
Classifications
-
- 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
- D01F9/145—Carbon filaments; Apparatus specially adapted for the manufacture thereof by decomposition of organic filaments from pitch or distillation residues
Landscapes
- Chemical & Material Sciences (AREA)
- Chemical Kinetics & Catalysis (AREA)
- General Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Textile Engineering (AREA)
- Inorganic Fibers (AREA)
- Spinning Methods And Devices For Manufacturing Artificial Fibers (AREA)
Description
産業上の利用分野
本発明は、ピツチ系炭素繊維の製造方法に関す
る。
従来技術及びその問題点
ピツチ系材料を原料とする炭素繊維は、ポリア
クリロニトリル等の有機合成繊維をプリカーサー
とする炭素繊維に比して、主に製造コストが低
い、高弾性率の製品が得られやすい等の理由によ
り、より安価で高性能の素材となり得るものと期
待されている。しかしながら、市販されているピ
ツチ系炭素繊維は、引張り強度が200Kg/mm2程度
以下であり、又品質安定性に劣り、充分満足すべ
きものとは言い難い。
一般に、ピツチ系炭素繊維においては、繊維断
面の分子凝集状態(以下断面高次構造という)
が、紡糸条件によつて種々異なつている。即ち、
基本的には、分子が繊維の同心円方向に結晶を構
成したり(いわゆるオニオン型)、繊維の中心か
ら放射状方向に結晶を構成したり(ラジアル型)、
或いは方向性を示すことなく任意の方向に分布し
たりする(ランダム型)形態に大別されるが、実
際の繊維においては、これ等が混在したものも存
在する。更に、たて割れ、クラツク、ボイド等の
欠陥が繊維の一部又は全体に存在する場合もあ
り、欠陥の有無を含めれば、ピツチ系炭素繊維の
断面高次構造の形態は、複雑多岐にわたる。そし
て、この様な各種の欠陥及び断面高次構造の存在
が、ピツチ系炭素繊維の品質安定性を低下させる
主な原因の一つとなつている。
上記の如き欠陥の発生及び断面高次構造の形成
は、紡糸用ピツチの物性によつても変化するが、
紡糸条件によつて最も大きく影響を受け、変動す
る。従つて、炭素繊維の品質安定性を高める為に
は、紡糸用ピツチの物性が若干ばらついたとして
も、常に欠陥がほとんど無く、一定の断面高次構
造を備えた炭素繊維を製造し得る紡糸技術を確立
する必要がある。即ち、たて割れ、クラツク、ボ
イド等の欠陥はほとんど発生させず、且つ高引張
強度を発現するに有効な高次断面構造であるオニ
オン型及び/又はランダム型構造を安定して形成
させる技術が必要である。
問題点を解決するための手段
本発明者は、上記の如き技術の現状に鑑みて鋭
意研究を重ねた結果、ピツチ系材料の溶融紡糸時
に、最終ノズル孔にいたる前に溶融ピツチ系材料
をして特定形状のキヤピラリー部を通過させるこ
とにより一定値以上の剪断応力を加え、次いで溶
融ピツチを実質的に剪断応力を加えない状態に一
旦保持した後、ノズル孔を通過させて紡糸を行な
う場合には、従来技術の問題点を実質的に解消若
しくは大巾に軽減し得ることを見出した。即ち、
本発明は、ピツチ系材料を溶融紡糸し、不融化
し、炭化するピツチ系炭素繊維の製造方法におい
て、最終ノズル孔にいたる前に溶融ピツチを円
形、異形又はスリツト型のキヤピラリー部を通過
させることにより最終ノズル孔でうける剪断応力
の1/2以上の剪断応力を加えた後、該溶融ピツ
チを一旦剪断応力を実質的に加えない状態に保持
し、次いでノズル孔を通過させて紡糸することを
特徴とするピツチ系炭素繊維の製造方法に係る。
本発明によると、上記炭化工程で黒鉛化すれば
ピツチ系黒鉛繊維を製造することもできる。従つ
て、本願明細書において、炭化は黒鉛化を含み、
炭素繊維とは黒鉛繊維をも含むものとして用い
る。
本発明においては、溶融ピツチ系材料を最終ノ
ズル孔の前に設けた円形、異形又はスリツト型の
キヤピラリー部を通過させることにより最終ノズ
ル孔でうける剪断応力の1/2以上の剪断応力を
加えた後、これを一旦剪断応力を実質的に加えな
い状態に保持し、次いで最終ノズル孔を通過させ
て紡糸することを必須とする。キヤピラリー部に
おいて溶融ピツチ系材料が受ける剪断応力が、最
終ノズル部での剪断応力の1/2未満である場合
には、所望の効果が充分に発揮されない。また、
キヤピラリー方式以外の方法で、例えば、緻密な
充填剤を間隙を通して剪断応力を加える場合に
も、所望の効果は得られない。更に、キヤピラリ
ー部で溶融ピツチ系材料に剪断応力を加えた後、
剪断応力を実質的に加えない状態に保持すること
なく、直ちに最終ノズル孔から紡糸を行なう場合
にも、本発明の効果は発揮されない。本発明で使
用するキヤピラリー部の断面の形状は、円形、ス
リツト型(或い長方型)、又はその他の異型(正
方形、十字形、Y字形その他)いずれであつても
良い。キヤピラリーの断面積及び長さも、必要な
剪断応力を付加し得るものであれば良く、特に限
定はされないが、通常断面積5×10-3〜5×102
mm程度、長さ0.1〜3.0mm程度である。
キヤピラリー部と最終ノズル孔との間で溶融ピ
ツチに実質的に剪断応力を加えない状態でこれを
保持する時間は、使用するピツチの種類及び性
質、紡糸温度、単位時間当りのピツチ吐出量、キ
ヤピラリー部及びノズル孔の形状等により異な
り、特に制限されるものではないが、通常溶融ピ
ツチがキヤピラリー部を通過する時間の103〜105
程度の時間が好ましい。キヤピラリー部と最終ノ
ズル孔との間で溶融ピツチに剪断応力を加えない
為には、当該部分(以下応力緩和部という)をパ
ツク外壁及び/もしくはノズルの導入孔を除けば
何ら剪断応力が働かない様に空洞化したものとす
る。
本発明で使用する紡糸用ピツチは、ピツチ状物
質を不活性ガス流通下に熱重縮合させることによ
り得られる。ピツチ状物質としては、石油系ピツ
チ、石炭系ピツチ及び有機化合物からの熱分解残
渣ピツチのいずれであつても良い。特にコールタ
ールやコールタールピツチの様な石炭系ピツチを
原料とする場合には、熱重縮合に先立つて、特開
昭57−88016号公報に記載の方法に従つて、予め
原料ピツチを芳香族還元性溶剤により350〜500℃
で熱処理しておくことにより、紡糸性をより一層
改善することができるが、紡糸用ピツチとして
は、紡糸可能であれば特に限定されない。
本発明において使用する最終ノズル孔の断面積
については特に制限はないが、通常5×10-3〜
10-3mm2程度である。
本発明においては、上記の様にして得られたピ
ツチ繊維を常法に従つて、例えば酸素雰囲気中
300〜340℃程度で不融化した後、不活性ガス雰囲
気中1000〜3000℃程度で加熱することにより炭素
繊維化する。
本発明により得られる炭素繊維の断面高次構造
は、その一部もしくは全部がオニオン型構造を呈
する(第1図及び第2図参照)。一部がオニオン
型構造である場合には、内層部にオニオン型構造
が存在して、外層部にランダム型構造(第1図
a)又はラジアル型構造(第1図b)が存在す
る。
発明の効果
本発明によれば以下の如き効果が奏される。
(i) 最終的に得られる炭素繊維は、その内部にた
て割れ、クラツク、ボイド等のミクロ的欠陥を
ほとんど有しない。
(ii) 品質安定性に優れているので、原料たるピツ
チ系材料の物性が若干変動したとしても、繊維
断面の少なくとも一部がオニオン型である安定
した断面高次構造を有する炭素繊維が得られ
る。
(iii) 上記(i)及び(ii)の結果として、炭素繊維の引張
り強度が大巾に向上する。
(iv) 更に、多ホールノズルを使用する紡糸時の糸
切れ頻度が低くなり、安定した連続紡糸が可能
となる。
(vi) 炭素繊維の内部をオニオン構造としたまま表
面をオニオン、ランダム、ラジアルと変えるこ
とができるので、安定した炭素繊維の力学物性
を保持したまま、樹脂複合体及び炭素複合体に
おいて樹脂及び炭素と良好な接着性を持つ各種
表面分子配列を選択することが出来る。
実施例
以下に参考例及び比較例と共に実施例を示し、
本発明の特徴とするところをより一層明らかにす
る。
参考例 1
軟化点110℃、キノリン不溶分0.18%、ベンゼ
ン不溶分35%のコールタールピツチ1重量部と水
素化重アントラセン油2重量部との混合溶液をオ
ートクレーブ中で430℃で60分間攪拌下加熱した
後、加圧式フイルターで熱時過し、更に減圧下
300℃で水素化重アントランセン油を除去して、
還元ピツチを得た。
ガス導入管、熱電対、攪挾機及び留出分除去管
を備えた反応器に上記で得られた還元ピツチ50Kg
を入れ、攪拌下窒素ガスを導入しつつ410〜480℃
で低分子量成分の除去及び熱重縮合を行なつた。
反応時間及び温度の選択により得られた2種の熱
重縮合ピツチの性状を第1表にNo.1〜2として示
す。
参考例 2
水素化重アントラセン油との混合下における加
熱処理を経ることなく、参考例1と同様のコール
タールピツチを参考例1と同様にして熱重縮合反
応に供した。得られた熱重縮合ピツチの性状をNo.
3として第1表に示す。
INDUSTRIAL APPLICATION FIELD The present invention relates to a method for producing pitch carbon fiber. Prior art and its problems Compared to carbon fibers made from organic synthetic fibers such as polyacrylonitrile as precursors, carbon fibers made from pitch-based materials can be produced at lower manufacturing costs and with a higher modulus of elasticity. Due to its ease of use, it is expected to be a material with lower cost and higher performance. However, commercially available pitch carbon fibers have a tensile strength of about 200 Kg/mm 2 or less, and have poor quality stability, so it is difficult to say that they are fully satisfactory. In general, in pitch-based carbon fibers, the molecular aggregation state (hereinafter referred to as cross-sectional higher-order structure) of the fiber cross section is
However, it varies depending on the spinning conditions. That is,
Basically, the molecules form crystals in the concentric direction of the fiber (so-called onion type), or the molecules form crystals in the radial direction from the center of the fiber (radial type).
It is roughly divided into two types: one is distributed in any direction without showing any directionality (random type), but in actual fibers, there are some that are a mixture of these types. Furthermore, defects such as vertical cracks, cracks, and voids may be present in part or all of the fibers, and if the presence or absence of defects is included, the morphology of the cross-sectional higher-order structure of pitch-based carbon fibers is complex and diverse. The existence of such various defects and cross-sectional higher-order structures is one of the main causes of deteriorating the quality stability of pitch-based carbon fibers. The occurrence of defects and the formation of cross-sectional higher-order structures as described above vary depending on the physical properties of the spinning pitch, but
It is most greatly influenced and fluctuated by the spinning conditions. Therefore, in order to improve the quality stability of carbon fibers, it is necessary to develop a spinning technology that can always produce carbon fibers with almost no defects and a constant cross-sectional higher-order structure, even if the physical properties of the spinning pitch vary slightly. need to be established. In other words, there is a technology that can stably form onion-type and/or random-type structures, which are high-order cross-sectional structures that are effective for developing high tensile strength and that hardly generate defects such as vertical cracks, cracks, and voids. is necessary. Means for Solving the Problems As a result of extensive research in view of the current state of the technology as described above, the inventor of the present invention has discovered that during melt spinning of pitch-based materials, the molten pitch-based material is spun before reaching the final nozzle hole. When the molten pitch is passed through a capillary part of a specific shape to apply a shear stress of a certain value or more, and then the molten pitch is temporarily held in a state where no shear stress is applied, the molten pitch is passed through a nozzle hole to perform spinning. discovered that the problems of the prior art can be substantially eliminated or greatly reduced. That is,
The present invention is a method for producing pitch-based carbon fiber in which pitch-based material is melt-spun, infusible, and carbonized, and the molten pitch is passed through a circular, irregularly shaped, or slit-type capillary section before reaching the final nozzle hole. After applying a shear stress of 1/2 or more of the shear stress received at the final nozzle hole, the molten pitch is held in a state where no shear stress is applied substantially, and then the molten pitch is passed through the nozzle hole for spinning. The present invention relates to a method for producing pitch-based carbon fibers. According to the present invention, pitch-based graphite fibers can also be produced by graphitizing in the carbonization step. Therefore, in this specification, carbonization includes graphitization,
Carbon fiber is used to include graphite fiber. In the present invention, a shear stress of 1/2 or more of the shear stress experienced at the final nozzle hole is applied by passing the molten pitch-based material through a circular, irregularly shaped, or slit-shaped capillary section provided in front of the final nozzle hole. After that, it is essential to hold the fiber in a state where no shear stress is applied to it, and then pass it through a final nozzle hole for spinning. If the shear stress applied to the molten pitch-based material in the capillary section is less than 1/2 of the shear stress at the final nozzle section, the desired effect will not be sufficiently exhibited. Also,
Even when shearing stress is applied by a method other than the capillary method, for example, through a gap in a dense filler, the desired effect cannot be obtained. Furthermore, after applying shear stress to the molten pitch material in the capillary section,
The effects of the present invention are not exhibited even when spinning is immediately performed from the final nozzle hole without maintaining a state in which shear stress is not substantially applied. The cross-sectional shape of the capillary portion used in the present invention may be circular, slit-shaped (or rectangular), or other irregular shapes (square, cross-shaped, Y-shaped, etc.). The cross-sectional area and length of the capillary are not particularly limited as long as they can apply the necessary shear stress, but usually have a cross-sectional area of 5 x 10 -3 to 5 x 10 2
The length is about 0.1 to 3.0 mm. The time to hold the molten pitch in a state where no shear stress is applied to it between the capillary section and the final nozzle hole depends on the type and properties of the pitch used, the spinning temperature, the pitch discharge amount per unit time, and the capillary. The time required for the molten pitch to pass through the capillary is usually 10 3 to 10 5 , although it varies depending on the shape of the capillary and the nozzle hole, and is not particularly limited.
A certain amount of time is preferable. In order to avoid applying shear stress to the molten pitch between the capillary part and the final nozzle hole, no shear stress is applied to that part (hereinafter referred to as the stress relaxation part) except for the pack outer wall and/or the nozzle introduction hole. Assume that it is hollowed out. The spinning pitch used in the present invention is obtained by subjecting a pitch-like material to thermal polycondensation under an inert gas flow. The pitch-like substance may be any of petroleum-based pitch, coal-based pitch, and pyrolysis residue pitch from organic compounds. In particular, when coal tar or coal-based pitch such as coal tar pitch is used as a raw material, prior to thermal polycondensation, the raw material pitch must be converted into aromatic 350-500℃ with reducing solvent
The spinnability can be further improved by heat-treating the material, but the pitch for spinning is not particularly limited as long as it is capable of spinning. There is no particular restriction on the cross-sectional area of the final nozzle hole used in the present invention, but it is usually 5×10 -3 ~
It is about 10 -3 mm 2 . In the present invention, the pitch fibers obtained as described above are processed in a conventional manner, for example, in an oxygen atmosphere.
After being infusible at about 300 to 340°C, it is turned into carbon fiber by heating at about 1000 to 3000°C in an inert gas atmosphere. The cross-sectional higher-order structure of the carbon fiber obtained according to the present invention partially or completely exhibits an onion-type structure (see FIGS. 1 and 2). When a portion has an onion-type structure, the onion-type structure exists in the inner layer part, and the random-type structure (FIG. 1a) or radial-type structure (FIG. 1b) exists in the outer layer part. Effects of the Invention According to the present invention, the following effects are achieved. (i) The carbon fiber finally obtained has almost no microscopic defects such as vertical cracks, cracks, and voids inside it. (ii) It has excellent quality stability, so even if the physical properties of the raw material Pitch-based material vary slightly, carbon fibers with a stable cross-sectional higher-order structure in which at least a part of the fiber cross section is onion-shaped can be obtained. . (iii) As a result of (i) and (ii) above, the tensile strength of carbon fibers is greatly improved. (iv) Furthermore, the frequency of yarn breakage during spinning using a multi-hole nozzle is reduced, making stable continuous spinning possible. (vi) Since the surface of the carbon fiber can be changed to onion, random, or radial while maintaining the onion structure inside the carbon fiber, the resin and carbon can be changed in resin composites and carbon composites while maintaining the stable mechanical properties of carbon fiber. Various surface molecular arrangements with good adhesion can be selected. Examples Examples are shown below along with reference examples and comparative examples,
The features of the present invention will be further clarified. Reference Example 1 A mixed solution of 1 part by weight of coal tar pitch with a softening point of 110°C, 0.18% quinoline insoluble content and 35% benzene insoluble content and 2 parts by weight of hydrogenated heavy anthracene oil was stirred in an autoclave at 430°C for 60 minutes. After heating, pass through a pressure filter and then under reduced pressure.
Remove hydrogenated heavy anthranthene oil at 300℃,
I got a reduced pitch. 50 kg of the reduced pitch obtained above was placed in a reactor equipped with a gas inlet tube, thermocouple, stirrer, and distillate removal tube.
and heated to 410-480℃ while stirring and introducing nitrogen gas.
The removal of low molecular weight components and thermal polycondensation were carried out.
The properties of two types of thermal polycondensation pitches obtained by selecting reaction times and temperatures are shown in Table 1 as Nos. 1 and 2. Reference Example 2 The same coal tar pitch as in Reference Example 1 was subjected to a thermal polycondensation reaction in the same manner as in Reference Example 1 without undergoing heat treatment while mixing with hydrogenated heavy anthracene oil. The properties of the resulting thermal polycondensation pitch were determined by No.
3 in Table 1.
【表】
注:軟化点は、スイス メトラー社製軟
化点測定装置により測定した。
実施例 1〜3
直径0.15mm、長さ0.4mmの細管100本からなるキ
ヤピラリー部、容積約15cm3の応力緩和部及び直径
0.2mm、長さ0.4mmのノズル(ノズル孔数100個)
を備えた紡糸装置を使用して、参考例1及び2で
得た熱重縮合ピツチNo.1〜3を紡糸した。この紡
糸過程において、ピツチはキヤピラリー部におい
て最終ノズル孔かうける剪断応力の約250%の剪
断応力を加えられ、次いで応力緩和で剪断応力を
受けない状態におかれ、最終ノズル孔で再び剪断
応力を加えられた。
かくして得たピツチ繊維を空気中300℃で30分
間不融化処理し、次いでN2ガス雰囲気中で1200
℃まで加熱して炭素繊維を得た。
第2表に直径10μmのピツチ繊維を糸切れを生
ずることなく連続して紡糸し得る平均時間(hr)、
上記で得た炭素繊維の断面高次構造及び欠陥含有
率を示す。[Table] Note: Softening point was measured using a softening point measuring device manufactured by Swiss Mettler.
Examples 1 to 3 A capillary section consisting of 100 thin tubes with a diameter of 0.15 mm and a length of 0.4 mm, a stress relaxation section with a volume of about 15 cm 3 and a diameter
0.2mm, length 0.4mm nozzle (100 nozzle holes)
Thermal polycondensation pitches Nos. 1 to 3 obtained in Reference Examples 1 and 2 were spun using a spinning apparatus equipped with the following. During this spinning process, the pitch is subjected to a shear stress of approximately 250% of the shear stress applied to the final nozzle hole in the capillary section, then placed in a state where it is not subjected to shear stress by stress relaxation, and then shear stress is applied again at the final nozzle hole. Added. The thus obtained pitch fiber was infusible in air at 300°C for 30 minutes, and then heated in an N2 gas atmosphere for 1200°C.
Carbon fibers were obtained by heating to ℃. Table 2 shows the average time (hr) required to continuously spin pitch fibers with a diameter of 10 μm without yarn breakage.
The cross-sectional higher-order structure and defect content of the carbon fiber obtained above are shown.
【表】
又、実施例1,2及び3で得られた炭素繊維の
断面高次構造を示す走査型電子顕微鏡写真をそれ
ぞれ第3図(約2600倍)、第4図(約8000倍)及
び第5図(約1700倍)として示す。
実施例 4〜6
第3表に示す形状及び本数のキヤピラリー部、
容積約18cm3の応力緩和部及び直径0.2mm、長さ0.4
mmのノズル(ノズル孔数100個)を備えた紡糸装
置を使用して、参考例1で得た熱重縮合ピツチNo.
1を紡糸し、得られたピツチ繊維を実施例1〜3
と同様にして不融化及び炭化処理して炭素繊維を
得た。
得られた炭素繊維の断面高次構造及び欠陥含有
率を第3表に示す。[Table] Scanning electron micrographs showing the cross-sectional higher-order structures of the carbon fibers obtained in Examples 1, 2, and 3 are shown in Figure 3 (approximately 2600 times), Figure 4 (approximately 8000 times), and Figure 4 (approximately 8000 times), respectively. It is shown as Figure 5 (approximately 1700x magnification). Examples 4 to 6 Capillary portions having the shape and number shown in Table 3,
Stress relaxation part with a volume of approximately 18 cm 3 , diameter 0.2 mm, length 0.4
Using a spinning device equipped with a mm nozzle (100 nozzle holes), the thermal polycondensation pitch No. obtained in Reference Example 1 was prepared.
1 and the resulting pitch fibers were used in Examples 1 to 3.
Carbon fibers were obtained by infusibility and carbonization treatment in the same manner as above. Table 3 shows the cross-sectional higher-order structure and defect content of the obtained carbon fibers.
【表】
異型断面キヤピラリー部を有する紡糸装置を使
用する場合にも、欠陥がほとんど無く、内層オニ
オン型の断面高次構造を有する炭素繊維が得られ
ることが明らかである。
比較例 1〜3
直径0.2mm、長さ0.4mmのノズル(ノズル孔数
100個)を備えた紡糸装置を使用して、参考例1
及び2で得た熱重縮合ピツチNo.1〜3を紡糸した
後、実施例1〜3と同一条件下に不融化及び炭化
処理を行なつて炭素繊維を得た。
得られた炭素繊維の断面高次構造及び欠陥含有
率、並びに直径10μmのピツチ繊維を紙切れを生
ずることなく連続して紡糸し得る平均時間(hr)
を第4表に示す。
比較例 4
キヤピラリー部の大きさが直径0.3mm、長さ0.6
mm(本数100本)である以外は実施例1と同じ紡
糸装置を用いて、参考例1で得た熱重縮合ピツチ
No.1を紡糸した。この紡糸過程では、ピツチはキ
ヤピラリー部において最終ノズル孔でうける剪断
応力の約30%の剪断応力を加えられた。得られた
ピツチ繊維を実施例1と同一条件下に不融化及び
炭化処理を行なつて炭素繊維を得た。
炭素繊維の断面高次構造及び欠陥含有率を第4
表に示す。
又本比較例で得られた炭素繊維の断面高次構造
を示す走査型電子顕微鏡写真(約2800倍)を第6
図として示す。炭素繊維の長さ方向に走る割れ、
ボイドなどの存在が認められる。
比較例 5
直径0.15mm、長さ0.4mmの細管100本からなるキ
ヤピラリー部と直径0.2mm、長さ0.4mmのノズル部
(ノズル孔数100個)とが実質的に直結されている
紡糸装置を使用して、参考例1で得た熱重縮合ピ
ツチNo.1を紡糸した。この紡糸過程においては、
ピツチは、キヤピラリー部において最終ノズル孔
でうける剪断応力の約250%の剪断応力を加えら
れ、次いで直ちに最終ノズル孔で剪断応力を加え
られた。
得られたピツチ繊維を実施例1〜3と同一条件
下に不融化及び炭化処理に供して炭素繊維を得
た。
炭素繊維の断面高次構造及び欠陥含有率を第4
表に示す。
又、本比較例で得られた炭素繊維の断面高次構
造を示す走査型電子顕微鏡写真(約4000倍)を第
7図として示す。炭素繊維の長さ方向に走る割れ
の存在が認められる。[Table] It is clear that even when using a spinning device having a capillary portion with an irregular cross-section, carbon fibers with almost no defects and an inner layer having an onion-type cross-sectional higher-order structure can be obtained. Comparative Examples 1 to 3 Nozzles with a diameter of 0.2 mm and a length of 0.4 mm (number of nozzle holes
Reference Example 1
After spinning the thermal polycondensation pitch Nos. 1 to 3 obtained in 2 and 2, infusibility and carbonization were performed under the same conditions as in Examples 1 to 3 to obtain carbon fibers. Cross-sectional higher-order structure and defect content of the obtained carbon fibers, and average time (hr) for continuous spinning of pitch fibers with a diameter of 10 μm without producing paper breaks
are shown in Table 4. Comparative example 4 The size of the capillary part is 0.3 mm in diameter and 0.6 in length.
The thermopolycondensation pitch obtained in Reference Example 1 was produced by using the same spinning device as in Example 1 except that the diameter was 100 mm (number of fibers).
No. 1 was spun. During this spinning process, a shear stress of approximately 30% of the shear stress experienced at the final nozzle hole was applied to the pitch in the capillary section. The obtained pitch fiber was subjected to infusibility and carbonization treatment under the same conditions as in Example 1 to obtain carbon fiber. The cross-sectional higher-order structure and defect content of carbon fiber are
Shown in the table. In addition, a scanning electron micrograph (approximately 2800 times) showing the cross-sectional higher-order structure of the carbon fiber obtained in this comparative example is shown in the sixth column.
Shown as a diagram. Cracks running along the length of the carbon fiber,
The existence of voids etc. is recognized. Comparative Example 5 A spinning device was constructed in which a capillary section consisting of 100 thin tubes with a diameter of 0.15 mm and a length of 0.4 mm and a nozzle section (number of nozzle holes of 100) with a diameter of 0.2 mm and a length of 0.4 mm were substantially directly connected. Using this, thermal polycondensation pitch No. 1 obtained in Reference Example 1 was spun. In this spinning process,
The pitch was sheared in the capillary section at approximately 250% of the shear stress experienced at the final nozzle hole, and then immediately sheared at the final nozzle hole. The obtained pitch fibers were subjected to infusibility and carbonization treatment under the same conditions as in Examples 1 to 3 to obtain carbon fibers. The cross-sectional higher-order structure and defect content of carbon fiber are
Shown in the table. Further, FIG. 7 shows a scanning electron micrograph (approximately 4000 times magnification) showing the cross-sectional higher-order structure of the carbon fiber obtained in this comparative example. The presence of cracks running in the length direction of the carbon fibers is observed.
【表】
第2表に示す実施例1〜3の結果と第4表に示
す比較例1〜3の結果との対比から明らかな如
く、キヤピラリー部と応力緩和部とを有しない紡
糸装置を使用する場合には、原料ピツチが同一で
あつても、連続紡糸性に劣り、断面高次構造はラ
ジアル型で且つ欠陥含有率が高い。
第2表に示す実施例1の結果と、第4表に示す
比較例4の結果との対比から明らかな如く、キヤ
ピラリー部にて、最終ノズル孔でうける1/2以
下の剪断応力を加えた場合には、たて割れ、クラ
ツク等の欠陥含有率が高い。
更に、第2表に示す実施例1の結果と第4表に
比較例5の結果との対比から明らかな如く、キヤ
ピラリー部と最終ノズル部との間に応力緩和部を
有しない紡糸装置を使用する場合にも、断面高次
構造はラジアル型であり、欠陥含有率も高い。[Table] As is clear from the comparison between the results of Examples 1 to 3 shown in Table 2 and the results of Comparative Examples 1 to 3 shown in Table 4, a spinning device without a capillary part and a stress relaxation part was used. In this case, even if the raw material pitch is the same, the continuous spinnability is poor, the cross-sectional higher-order structure is radial, and the defect content is high. As is clear from the comparison between the results of Example 1 shown in Table 2 and the results of Comparative Example 4 shown in Table 4, a shear stress of 1/2 or less of that at the final nozzle hole was applied at the capillary part. In some cases, the content of defects such as vertical cracks and cracks is high. Furthermore, as is clear from the comparison between the results of Example 1 shown in Table 2 and the results of Comparative Example 5 shown in Table 4, a spinning device without a stress relaxation part between the capillary part and the final nozzle part was used. Even in this case, the cross-sectional higher-order structure is radial type and the defect content is high.
第1図及び第2図は、本発明方法により得られ
る炭素繊維の断面高次構造を示す模式図、第3図
乃至第5図は、実施例1,2及び3で得られた炭
素繊維の断面高次構造を示す走査型電子顕微鏡写
真であり、第6図及び第7図は、比較例4及び5
で得られた炭素繊維の断面高次構造を示す走査型
電子顕微鏡写真である。
Figures 1 and 2 are schematic diagrams showing the cross-sectional higher-order structure of carbon fibers obtained by the method of the present invention, and Figures 3 to 5 are diagrams of carbon fibers obtained in Examples 1, 2, and 3. FIGS. 6 and 7 are scanning electron micrographs showing cross-sectional higher-order structures, and FIGS.
This is a scanning electron micrograph showing the cross-sectional higher-order structure of the carbon fiber obtained in .
Claims (1)
するピツチ系炭素繊維の製造方法において、最終
ノズル孔にいたる前に溶融ピツチを円形、異形又
はスリツト型のキヤピラリー部を通過させること
により最終ノズル孔で受ける剪断応力の1/2以
上の剪断応力を加えた後、該溶融ピツチを一旦剪
断応力を実質的に加えない状態に保持し、次いで
ノズル孔を通過させて紡糸することを特徴とする
ピツチ系炭素繊維の製造方法。1. In a method for manufacturing pitch-based carbon fiber in which pitch-based material is melt-spun, infusible, and carbonized, the final nozzle is made by passing the molten pitch through a circular, irregularly shaped, or slit-shaped capillary section before reaching the final nozzle hole. After applying a shear stress of 1/2 or more of the shear stress received in the hole, the molten pitch is once held in a state where no shear stress is applied substantially, and then passed through the nozzle hole to be spun. A method for producing pitch-based carbon fiber.
Priority Applications (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP1284886A JPS62170527A (en) | 1986-01-22 | 1986-01-22 | Production of pitch-based carbon fiber |
PCT/JP1987/000041 WO1990007594A1 (en) | 1986-01-22 | 1987-01-22 | Process for producing pitch-base carbon fiber |
US07/105,428 US4859381A (en) | 1986-01-22 | 1987-01-22 | Process for preparing pitch-type carbon fibers |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP1284886A JPS62170527A (en) | 1986-01-22 | 1986-01-22 | Production of pitch-based carbon fiber |
Publications (2)
Publication Number | Publication Date |
---|---|
JPS62170527A JPS62170527A (en) | 1987-07-27 |
JPH0413450B2 true JPH0413450B2 (en) | 1992-03-09 |
Family
ID=11816814
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP1284886A Granted JPS62170527A (en) | 1986-01-22 | 1986-01-22 | Production of pitch-based carbon fiber |
Country Status (2)
Country | Link |
---|---|
JP (1) | JPS62170527A (en) |
WO (1) | WO1990007594A1 (en) |
Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2009031570A1 (en) | 2007-09-03 | 2009-03-12 | National Printing Bureau, Incorporated Administrative Agency | Forgery prevention printed matter |
WO2010032718A1 (en) | 2008-09-16 | 2010-03-25 | 独立行政法人 国立印刷局 | Forgery preventive printed matter, method for producing same, and recording medium in which dot data creation software is stored |
WO2010038824A1 (en) | 2008-10-03 | 2010-04-08 | 独立行政法人 国立印刷局 | Forgery preventive printed matter |
Citations (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS59168127A (en) * | 1983-03-15 | 1984-09-21 | Toray Ind Inc | Production of carbon fiber |
JPS60194120A (en) * | 1984-03-08 | 1985-10-02 | Mitsubishi Chem Ind Ltd | Production of pitch fiber |
JPS60239520A (en) * | 1984-05-11 | 1985-11-28 | Mitsubishi Chem Ind Ltd | Carbon fiber |
JPS60252723A (en) * | 1984-05-30 | 1985-12-13 | Mitsubishi Chem Ind Ltd | Production of pitch based carbon fiber |
-
1986
- 1986-01-22 JP JP1284886A patent/JPS62170527A/en active Granted
-
1987
- 1987-01-22 WO PCT/JP1987/000041 patent/WO1990007594A1/en unknown
Patent Citations (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS59168127A (en) * | 1983-03-15 | 1984-09-21 | Toray Ind Inc | Production of carbon fiber |
JPS60194120A (en) * | 1984-03-08 | 1985-10-02 | Mitsubishi Chem Ind Ltd | Production of pitch fiber |
JPS60239520A (en) * | 1984-05-11 | 1985-11-28 | Mitsubishi Chem Ind Ltd | Carbon fiber |
JPS60252723A (en) * | 1984-05-30 | 1985-12-13 | Mitsubishi Chem Ind Ltd | Production of pitch based carbon fiber |
Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2009031570A1 (en) | 2007-09-03 | 2009-03-12 | National Printing Bureau, Incorporated Administrative Agency | Forgery prevention printed matter |
WO2010032718A1 (en) | 2008-09-16 | 2010-03-25 | 独立行政法人 国立印刷局 | Forgery preventive printed matter, method for producing same, and recording medium in which dot data creation software is stored |
WO2010038824A1 (en) | 2008-10-03 | 2010-04-08 | 独立行政法人 国立印刷局 | Forgery preventive printed matter |
Also Published As
Publication number | Publication date |
---|---|
JPS62170527A (en) | 1987-07-27 |
WO1990007594A1 (en) | 1990-07-12 |
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