JPH03164471A - Carbon/metal composite and production thereof - Google Patents
Carbon/metal composite and production thereofInfo
- Publication number
- JPH03164471A JPH03164471A JP2096050A JP9605090A JPH03164471A JP H03164471 A JPH03164471 A JP H03164471A JP 2096050 A JP2096050 A JP 2096050A JP 9605090 A JP9605090 A JP 9605090A JP H03164471 A JPH03164471 A JP H03164471A
- Authority
- JP
- Japan
- Prior art keywords
- metal
- carbon
- fibers
- composite material
- metal fibers
- 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.)
- Granted
Links
- 239000002905 metal composite material Substances 0.000 title claims abstract description 44
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 title claims abstract description 41
- 229910052799 carbon Inorganic materials 0.000 title claims abstract description 27
- 238000004519 manufacturing process Methods 0.000 title claims description 16
- 239000000835 fiber Substances 0.000 claims abstract description 208
- 239000000843 powder Substances 0.000 claims abstract description 52
- 239000002131 composite material Substances 0.000 claims abstract description 38
- 239000000463 material Substances 0.000 claims abstract description 34
- 239000003575 carbonaceous material Substances 0.000 claims abstract description 33
- 229910052802 copper Inorganic materials 0.000 claims abstract description 20
- 238000010438 heat treatment Methods 0.000 claims abstract description 19
- 239000011159 matrix material Substances 0.000 claims abstract description 17
- 239000000203 mixture Substances 0.000 claims abstract description 16
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 11
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 7
- 229910052751 metal Inorganic materials 0.000 claims description 201
- 239000002184 metal Substances 0.000 claims description 200
- 238000007747 plating Methods 0.000 claims description 41
- 239000002994 raw material Substances 0.000 claims description 39
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 25
- 238000000034 method Methods 0.000 claims description 24
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims description 23
- 150000001247 metal acetylides Chemical class 0.000 claims description 21
- 239000010949 copper Substances 0.000 claims description 19
- 238000002156 mixing Methods 0.000 claims description 18
- 238000005275 alloying Methods 0.000 claims description 17
- 238000010304 firing Methods 0.000 claims description 16
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 7
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 claims description 7
- 229910017052 cobalt Inorganic materials 0.000 claims description 6
- 239000010941 cobalt Substances 0.000 claims description 6
- 239000002344 surface layer Substances 0.000 claims description 6
- 238000002844 melting Methods 0.000 claims description 5
- 230000008018 melting Effects 0.000 claims description 5
- 230000015572 biosynthetic process Effects 0.000 claims description 3
- 229910000831 Steel Inorganic materials 0.000 abstract description 62
- 239000010959 steel Substances 0.000 abstract description 62
- 238000005452 bending Methods 0.000 abstract description 31
- 229910001220 stainless steel Inorganic materials 0.000 abstract description 3
- 229920000914 Metallic fiber Polymers 0.000 abstract 4
- 238000000465 moulding Methods 0.000 description 35
- 238000006243 chemical reaction Methods 0.000 description 16
- 238000003763 carbonization Methods 0.000 description 13
- 239000011305 binder pitch Substances 0.000 description 10
- 239000010410 layer Substances 0.000 description 10
- 238000005299 abrasion Methods 0.000 description 9
- 238000000576 coating method Methods 0.000 description 9
- 239000011248 coating agent Substances 0.000 description 8
- 239000002245 particle Substances 0.000 description 8
- 239000011295 pitch Substances 0.000 description 8
- 238000012360 testing method Methods 0.000 description 8
- 238000005255 carburizing Methods 0.000 description 7
- 229910001567 cementite Inorganic materials 0.000 description 7
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 7
- 150000002739 metals Chemical class 0.000 description 7
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 6
- 230000007423 decrease Effects 0.000 description 6
- 230000000694 effects Effects 0.000 description 6
- 229910045601 alloy Inorganic materials 0.000 description 5
- 239000000956 alloy Substances 0.000 description 5
- 239000011230 binding agent Substances 0.000 description 5
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 4
- 229910000975 Carbon steel Inorganic materials 0.000 description 4
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 4
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 4
- 239000010962 carbon steel Substances 0.000 description 4
- 239000012299 nitrogen atmosphere Substances 0.000 description 4
- 238000010000 carbonizing Methods 0.000 description 3
- 229910052804 chromium Inorganic materials 0.000 description 3
- 239000011651 chromium Substances 0.000 description 3
- 239000011247 coating layer Substances 0.000 description 3
- 238000007796 conventional method Methods 0.000 description 3
- 238000001816 cooling Methods 0.000 description 3
- 238000005520 cutting process Methods 0.000 description 3
- 229910052742 iron Inorganic materials 0.000 description 3
- 229910052748 manganese Inorganic materials 0.000 description 3
- 239000011572 manganese Substances 0.000 description 3
- 230000013011 mating Effects 0.000 description 3
- 239000007769 metal material Substances 0.000 description 3
- 238000003825 pressing Methods 0.000 description 3
- 229920005989 resin Polymers 0.000 description 3
- 239000011347 resin Substances 0.000 description 3
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 3
- CSCPPACGZOOCGX-UHFFFAOYSA-N Acetone Chemical compound CC(C)=O CSCPPACGZOOCGX-UHFFFAOYSA-N 0.000 description 2
- 229920000049 Carbon (fiber) Polymers 0.000 description 2
- 229910001209 Low-carbon steel Inorganic materials 0.000 description 2
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 description 2
- 239000004917 carbon fiber Substances 0.000 description 2
- 239000011280 coal tar Substances 0.000 description 2
- 230000006866 deterioration Effects 0.000 description 2
- -1 etc. Substances 0.000 description 2
- 239000010439 graphite Substances 0.000 description 2
- 229910002804 graphite Inorganic materials 0.000 description 2
- 238000005259 measurement Methods 0.000 description 2
- 239000002923 metal particle Substances 0.000 description 2
- 239000012778 molding material Substances 0.000 description 2
- 229910052757 nitrogen Inorganic materials 0.000 description 2
- 239000005011 phenolic resin Substances 0.000 description 2
- 238000002791 soaking Methods 0.000 description 2
- 239000010935 stainless steel Substances 0.000 description 2
- 239000002345 surface coating layer Substances 0.000 description 2
- 229920001187 thermosetting polymer Polymers 0.000 description 2
- KXGFMDJXCMQABM-UHFFFAOYSA-N 2-methoxy-6-methylphenol Chemical compound [CH]OC1=CC=CC([CH])=C1O KXGFMDJXCMQABM-UHFFFAOYSA-N 0.000 description 1
- VHUUQVKOLVNVRT-UHFFFAOYSA-N Ammonium hydroxide Chemical compound [NH4+].[OH-] VHUUQVKOLVNVRT-UHFFFAOYSA-N 0.000 description 1
- 229910000640 Fe alloy Inorganic materials 0.000 description 1
- 229910000863 Ferronickel Inorganic materials 0.000 description 1
- 229910000990 Ni alloy Inorganic materials 0.000 description 1
- 238000002441 X-ray diffraction Methods 0.000 description 1
- 230000002159 abnormal effect Effects 0.000 description 1
- 239000000654 additive Substances 0.000 description 1
- 230000000996 additive effect Effects 0.000 description 1
- 238000004378 air conditioning Methods 0.000 description 1
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 1
- QGZKDVFQNNGYKY-UHFFFAOYSA-N ammonia Natural products N QGZKDVFQNNGYKY-UHFFFAOYSA-N 0.000 description 1
- 238000004458 analytical method Methods 0.000 description 1
- 239000012298 atmosphere Substances 0.000 description 1
- 150000001721 carbon Chemical class 0.000 description 1
- 239000000919 ceramic Substances 0.000 description 1
- 229910010293 ceramic material Inorganic materials 0.000 description 1
- 239000003610 charcoal Substances 0.000 description 1
- 239000003245 coal Substances 0.000 description 1
- 239000011294 coal tar pitch Substances 0.000 description 1
- 150000001879 copper Chemical class 0.000 description 1
- 230000002542 deteriorative effect Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000001125 extrusion Methods 0.000 description 1
- 239000002783 friction material Substances 0.000 description 1
- 230000005484 gravity Effects 0.000 description 1
- 238000007654 immersion Methods 0.000 description 1
- 238000000691 measurement method Methods 0.000 description 1
- 150000002815 nickel Chemical class 0.000 description 1
- 239000003921 oil Substances 0.000 description 1
- 230000001590 oxidative effect Effects 0.000 description 1
- 239000002006 petroleum coke Substances 0.000 description 1
- 229920001568 phenolic resin Polymers 0.000 description 1
- 238000007750 plasma spraying Methods 0.000 description 1
- 238000013001 point bending Methods 0.000 description 1
- 229910052573 porcelain Inorganic materials 0.000 description 1
- 239000011148 porous material Substances 0.000 description 1
- 238000002360 preparation method Methods 0.000 description 1
- 239000000523 sample Substances 0.000 description 1
- 239000003566 sealing material Substances 0.000 description 1
- 238000007493 shaping process Methods 0.000 description 1
- 230000035939 shock Effects 0.000 description 1
- HBMJWWWQQXIZIP-UHFFFAOYSA-N silicon carbide Chemical compound [Si+]#[C-] HBMJWWWQQXIZIP-UHFFFAOYSA-N 0.000 description 1
- 239000000377 silicon dioxide Substances 0.000 description 1
- 238000005245 sintering Methods 0.000 description 1
- 230000003746 surface roughness Effects 0.000 description 1
- 239000004094 surface-active agent Substances 0.000 description 1
- 238000010998 test method Methods 0.000 description 1
- 230000007704 transition Effects 0.000 description 1
- 238000007740 vapor deposition Methods 0.000 description 1
Landscapes
- Ceramic Products (AREA)
- Other Surface Treatments For Metallic Materials (AREA)
Abstract
Description
【発明の詳細な説明】
産業上の利用分野
この発明は摺動集電材料、特に鉄道用パンタグラフ摺板
に好適な、強度、耐摩耗性および電気的特性に優れた炭
素・金属複合材とその製造方法に関する。DETAILED DESCRIPTION OF THE INVENTION Field of Industrial Application This invention relates to a carbon-metal composite material with excellent strength, abrasion resistance, and electrical properties suitable for sliding current collector materials, especially railway pantograph sliding plates, and its Regarding the manufacturing method.
従来の技術
摺動集電材料として、従来は鋳造合金や焼結合金等の金
属系材料と炭素系材料とが用いられてきた。Conventional technology Metal materials such as cast alloys and sintered alloys and carbon materials have been used as sliding current collector materials.
金属系材料は、強度および電気伝導性の点で優れている
が、アーク発生が多く、また摺動特性が不十分で、トロ
リー線や起電レール等の相手材の摩耗量が大きくなると
いう欠点がある。Metal-based materials are excellent in terms of strength and electrical conductivity, but have the drawbacks of frequent arcing, insufficient sliding properties, and increased wear on mating materials such as trolley wires and electromotive rails. There is.
炭素系材料は、潤滑性がよく、相手材の損耗を小さくで
きるが、電気比抵抗が大きく、集電中に発熱し易いとい
う欠点がある。Although carbon-based materials have good lubricity and can reduce wear and tear on the mating material, they have the drawback of having a high electrical resistivity and being likely to generate heat during current collection.
車両の高速化と冷房設備等による消費電力の増大に対応
するため、最近では炭素の浸れた摺動特性と金属の電気
伝導性を生かした炭素・金属複合材が摺動集電用材料と
して採用されつつある。In order to cope with the increasing speed of vehicles and the increase in power consumption due to air conditioning equipment, carbon-metal composites that take advantage of the sliding properties of carbon and the electrical conductivity of metals have recently been adopted as materials for sliding current collectors. It is being done.
このような炭素・金属複合材としては、炭素材の気孔に
特定の金属を加圧含浸させたものが特公昭５６−１４７
３２号に開示されている。As such a carbon-metal composite material, one in which the pores of a carbon material are impregnated with a specific metal under pressure was developed in Japanese Patent Publication No. 56-147.
It is disclosed in No. 32.
特開昭６０−２３８４０２号には、炭素材原料に良導電
性の金属を添加することにより得られた、金属粉含有炭
素材からなる集電材料が開示されている。JP-A-60-238402 discloses a current collecting material made of a metal powder-containing carbon material obtained by adding a highly conductive metal to a carbon material raw material.
特開昭６１−２４５９５７号には、金属繊維および／ま
たは炭素繊維を含有する炭素骨材とバインダーとを成形
、焼成した後、金属含浸を行う、集電材料の製造方法が
記載されている。JP-A No. 61-245957 describes a method for producing a current collector material, in which a carbon aggregate containing metal fibers and/or carbon fibers and a binder are formed and fired, and then impregnated with metal.
特開昭６２−７２５６４号には、炭素材原料に金属繊維
を配合し、常温で成形した後、焼成することからなる、
摺動集電用炭素材の製造方法が記載されている。JP-A No. 62-72564 discloses a method in which metal fibers are blended with a carbon material raw material, molded at room temperature, and then fired.
A method for manufacturing a carbon material for sliding current collectors is described.
特開昭６２−１９７３５２号には、炭素材原料に金属繊
維を一方向に配向させて配合した後、成形・焼成するこ
とからなる、摺動集電用炭素材の製造方法が記載されて
いる。JP-A No. 62-197352 describes a method for producing a carbon material for sliding current collectors, which comprises blending a carbon material raw material with metal fibers oriented in one direction, followed by molding and firing. .
特開昭６２−２１５７３１号には、ピッチ、金属繊維お
よび黒鉛の混合物を、温度４５０〜６００℃、成形圧力
４０ｋｇ／ｃｍ”以上で加熱加圧成形することからなる
、炭素・金属複合材系のブレーキ摩擦材の製造方法が記
載されている。JP-A No. 62-215731 discloses a carbon-metal composite material made by heating and press-molding a mixture of pitch, metal fibers and graphite at a temperature of 450 to 600°C and a molding pressure of 40 kg/cm or more. A method for manufacturing a brake friction material is described.
特開平１−１５７４６４号には、金属粉末を含有してい
てもよい炭素質マトリックス中に金網を含有させた、摺
動集電用炭素材が開示されている。JP-A-1-157464 discloses a carbon material for sliding current collector in which a wire mesh is contained in a carbonaceous matrix which may contain metal powder.
発明が解決しようとする課題
しかし、従来の炭素・金属複合材の大部分は、現在の主
流である金属焼結系摺板から炭素・金属複合材への移行
期、すなわち金属焼結系と炭素・金属複合材系の摺板の
混合使用時を想定したトロリー線（銅製）の荒れた状態
での摺動時の摺板摩耗が大きいという欠点がある。Problems to be Solved by the Invention However, most of the conventional carbon/metal composite materials are in the transition period from the current mainstream metal sintered sliding plates to carbon/metal composites, that is, the metal sintered and carbon・It has the disadvantage that the sliding plate suffers a lot of wear when the trolley wire (made of copper) is slid in a rough condition, which is intended for mixed use with metal composite sliding plates.
また、これら従来の炭素・金属複合材の大部分は、曲げ
強度等の強度特性が従来の金属系摺板に比べて低いもの
であった。そのため、走行中の振動、衝撃や架線に付着
した結氷や異常事態により外れたトロリー線ハンガイヤ
に衝突した場合、摺仮に欠損または破損が起り易く、従
来の金属系摺板に比して信頼性、安全性に劣るという問
題もあった。Furthermore, most of these conventional carbon-metal composite materials have lower strength properties such as bending strength than conventional metal sliding plates. Therefore, if a trolley wire hanger comes off due to vibrations, shocks, ice buildup on the overhead wire, or an abnormal situation during running, the sliding plate is likely to be damaged or damaged, making it less reliable than conventional metal sliding plates. There was also the problem of inferior safety.
さらに、炭素・金属複合材は、従来の金属系摺板と比較
し、電気比抵抗が高いという欠点もある。Furthermore, carbon-metal composite materials also have the disadvantage of having a higher electrical resistivity than conventional metal sliding plates.
電気比抵抗が高いと、ジュール熱によりトロリー線温度
の上昇を招き（これは例えば電車が停車した状態で冷暖
房装置や車内照明器具等を使用する条件下で顕著である
）、高テンションが付与されたトロリー線が断線に至る
可能性があり、非常に危険である。If the electrical resistivity is high, the temperature of the trolley wire will rise due to Joule heat (this is noticeable, for example, when the train is stopped and the air conditioner or lighting equipment inside the train is used), and high tension is applied to the trolley wire. This is extremely dangerous as the trolley wire may break.
炭素・金属複合材の強度特性や電気特性は、金属成分の
含有量を増大させることにより改善することができる。The strength and electrical properties of carbon-metal composites can be improved by increasing the content of metal components.
しかし、金属成分の含有量を増大させると、トロリー線
との間で発生するスパークが多くなり、トロリー線や摺
板の摩耗が増大するので好ましくない。However, if the content of the metal component is increased, more sparks will be generated between the contact wire and the contact wire, which will increase the wear of the contact wire and the sliding plate, which is not preferable.
この発明は曲げ強度等の強度特性や耐摩耗性に優れ、か
つ電気比抵抗が低く、安定したスパーク特性が得られる
パンタグラフ摺板に好適な炭素・金属複合材、金属焼結
系摺板と炭素・金属複合材系摺板との混合使用を想定し
た荒れたトロリー線に対して優れた耐摩耗性を示し、強
度、電気比抵抗も改善されたパンタグラフ摺板用の炭素
・金属複合材と、これらの炭素・金属複合材を製造する
方法を提案しようとするものである。This invention is a carbon-metal composite material suitable for pantograph sliding plates, which has excellent strength properties such as bending strength and wear resistance, low electrical resistivity, and stable spark characteristics, and a metal sintered sliding plate and carbon.・A carbon-metal composite material for pantograph sliding plates that exhibits excellent abrasion resistance against rough trolley wires and has improved strength and electrical resistivity, and is intended for mixed use with metal composite sliding plates. This paper attempts to propose a method for producing these carbon-metal composite materials.
課題を解決するための手段
この発明者は、従来の方法で得られる炭素・金属繊維複
合摺板の曲げ強度が低い原因について検討した結果、以
下のことを見い出した。Means for Solving the Problems The inventor investigated the cause of the low bending strength of carbon/metal fiber composite sliding plates obtained by conventional methods and discovered the following.
炭素・金属繊維複合摺板の曲げ強度が低い原因は、複合
材の焼成による炭化中に金属繊維がマトリックスのピッ
チや炭素粉により浸炭され、繊維中に金属炭化物が生成
することにある。例えば、スチールファイバーでは、鉄
の炭化物であるセメンタイト （ＦｅｓＣ）を多く含む
組成に変化する。The cause of the low bending strength of carbon/metal fiber composite sliding plates is that metal fibers are carburized by matrix pitch and carbon powder during carbonization by firing of the composite material, and metal carbides are generated in the fibers. For example, the composition of steel fiber changes to include a large amount of cementite (FesC), which is a carbide of iron.
スチールファイバー等の金属繊維の浸炭反応は、炭化温
度９００℃以下では顕著ではないが、炭素の強度が十分
に発現し、そのため通常の炭化工程に利用される１００
０℃付近の温度では浸炭反応が急速に進行する。The carburizing reaction of metal fibers such as steel fibers is not noticeable at carbonization temperatures of 900°C or lower, but the strength of carbon is sufficiently developed, and therefore 100°C, which is used in ordinary carbonization processes, is
At temperatures around 0°C, the carburizing reaction proceeds rapidly.
浸炭で生成するセメンタイトは、硬く、脆い特性を有し
、摺動材として使用した場合の耐摩耗性は良好であるが
、靭性が低く、複合材の曲げ強度を低下させるため、浸
炭反応を可及的に抑制する必要がある。Cementite produced by carburization has hard and brittle characteristics and has good wear resistance when used as a sliding material, but has low toughness and reduces the bending strength of composite materials, so it is difficult to carry out carburization reactions. It is necessary to suppress this issue in an effective manner.
そこで、この発明者は金属繊維、例えばスチールファイ
バーの浸炭反応抑制方法について種々検討した結果、下
記の知見を得た。Therefore, as a result of various studies on methods for suppressing the carburization reaction of metal fibers, such as steel fibers, the inventor obtained the following knowledge.
■ 成型前にスチールファイバーの表面を銅、ニッケル
、アルミニウム、コバルト等炭化物生成傾向が鉄以下の
異種材料で被覆したものを用いると、スチールファイバ
ーの浸炭反応が抑制され、複合材の強度が大きく改善さ
れる。■ If the surface of the steel fiber is coated with a dissimilar material such as copper, nickel, aluminum, or cobalt that has a tendency to generate carbides less than iron before forming, the carburization reaction of the steel fiber will be suppressed and the strength of the composite material will be greatly improved. be done.
■ 未被覆のスチールファイバーを使用しても、上記の
ような炭化物生成傾向の小さい異種金属元素を主成分と
する金属粉末を添加することによって、同様に炭化時の
スチールファイバーの浸炭反応が抑制される。■ Even if uncoated steel fibers are used, the carburization reaction of the steel fibers during carbonization can be similarly suppressed by adding a metal powder whose main component is a dissimilar metal element that has a low tendency to form carbides, as described above. Ru.
■ スチールファイバーの表面を上記のような炭化物生
成傾向の小さい異種金属と合金化させることによっても
、同様に浸炭反応が抑制される。■ The carburizing reaction can be similarly suppressed by alloying the surface of the steel fiber with a dissimilar metal that has a small tendency to form carbides, such as those mentioned above.
すなわち、この発明の要旨は、金属繊維の一部または全
部が表層に異種材料が被覆および／または合金化された
ものであること、金属繊維に加えて炭化物生成傾向がこ
れと同等もしくはこれより小さい異種金属粉末を含有す
ること、表層に異種材料が被覆および／または合金化さ
れた金属繊維と炭化物生成傾向の小さい異種金属粉末を
含有すること、表層に被覆する異種材料が炭化物生成傾
向が金属繊維と同等もしくはこれより小さい材料である
こと、上記異種材料および異種金属が銅、ニッケル、ア
ルミニウム、コバルトの少なくともｉｎであることを特
徴とする炭素・金属複合材である。That is, the gist of the present invention is that some or all of the metal fibers are coated and/or alloyed with a different material on the surface layer, and that the tendency to form carbides in addition to the metal fibers is equal to or smaller than that of the metal fibers. Contains a dissimilar metal powder; Contains a metal fiber whose surface layer is coated and/or alloyed with a dissimilar material and a dissimilar metal powder with a small tendency to generate carbides; The dissimilar material coated on the surface layer is a metal fiber with a tendency to generate carbides. The carbon-metal composite material is characterized in that the dissimilar materials and dissimilar metals are at least in the group consisting of copper, nickel, aluminum, and cobalt.
また、その製造方法として、金属繊維をめっき処理する
か、金属繊維を上記の異種金属粉末と混合後、融点以下
の温度゛で熱処理により合金化したものを複合材に含有
される金属繊維の一部または全部として炭素材料と混合
・成形・焼成すること、金属繊維の一部または全部をめ
っき処理後、炭素材原料と混合・成形・焼成することに
よって金属繊維を合金化すること、マトリックス中に金
属繊維に加えて炭化物生成傾向がこれと同等もしくはこ
れより小さい異種金属粉末を混合し、成形・焼成するこ
と、およびこれらの組合せであることを特徴とするもの
である。In addition, as a manufacturing method, metal fibers are plated, or metal fibers are mixed with the above-mentioned dissimilar metal powder and then alloyed by heat treatment at a temperature below the melting point. Mixing, shaping, and firing a part or all of the metal fibers with a carbon material; After plating a part or all of the metal fibers, alloying the metal fibers by mixing, molding, and firing the metal fibers with a carbon material raw material; It is characterized by mixing metal fibers with dissimilar metal powders having the same or smaller tendency to form carbides, and then molding and firing the mixture, as well as a combination thereof.
作 用
この発明の炭素・金属複合材に使用される炭素材原料と
しては、■自己焼結性メソフェーズ粉、■バインダーピ
ッチと炭素質や黒鉛質の骨材からなる２元系原料、■フ
ェノール樹脂のような熱硬化性樹脂等、種々のものが使
用可能である。Function The carbon material raw materials used in the carbon-metal composite material of this invention include: ■ Self-sintering mesophase powder, ■ Binary raw material consisting of binder pitch and carbonaceous or graphite aggregate, ■ Phenol resin. Various thermosetting resins can be used, such as thermosetting resins such as .
ここで、二元系原料における炭素質の骨材としては、耐
摩耗性の面から、ピッチや石炭等を１０００℃程度で炭
化処理したコークス粉や、フェノール樹脂を炭化して得
られる等方性炭素等の硬度の高いものが好ましい。Here, from the viewpoint of wear resistance, the carbonaceous aggregate in the binary raw material is coke powder obtained by carbonizing pitch or coal at about 1000℃, or isotropic aggregate obtained by carbonizing phenolic resin. A material with high hardness such as carbon is preferable.
バインダーピッチとしては、コールタール中ピッチや、
これをさらに熱処理して得られる高軟化点ピッチ等を使
用できる。Binder pitches include coal tar medium pitch,
A high softening point pitch obtained by further heat-treating this or the like can be used.
なお、ピッチとしては、加熱時流動性を示すもので、か
つ可及的に低揮発分の方が複合材の強度、摩耗性が向上
し、好ましい。The pitch is preferably one that exhibits fluidity when heated and has as low a volatile content as possible, since this improves the strength and abrasion resistance of the composite material.
パンタグラフ摺板には、上記の高硬度骨材とバインダー
ピッチとを主成分とする二元系炭素材原料が、価格と性
能の両面から好ましい。For pantograph sliding plates, a binary carbon material raw material containing the above-mentioned high-hardness aggregate and binder pitch as main components is preferable in terms of both price and performance.
次に、金属繊維としては、薄板切削法、ビビリ振動切削
法、ワイヤー切削法、延伸法等の種々の方法で製造され
た繊維状あるいはウール状のものが使用できる。繊維の
形状は特に限定されず、針状、くさび状、波状、網状、
あるいはそれらの混合物のいずれでもよい。Next, as the metal fiber, fibrous or wool-like materials manufactured by various methods such as a thin plate cutting method, a chatter vibration cutting method, a wire cutting method, and a drawing method can be used. The shape of the fibers is not particularly limited and may be needle-like, wedge-like, wavy, net-like,
Or a mixture thereof may be used.
金属繊維の材質は特に限定されるものではなく、普通鋼
、高張力鋼、ステンレス鋼等から製造されたスチールフ
ァイバー さらには銅ファイバー等の鋼基外の金属の繊
維が使用できる。材質としては、低炭素鋼製のスチール
ファイバーが最も良好な性能を示す。スチール製の繊維
の場合、マンガンやクロムは浸炭反応を促進し、得られ
た複合材の強度を低下させるため、これらの元素の含有
量ができるだけ低いことが望まれる。The material of the metal fiber is not particularly limited, and steel fibers made from ordinary steel, high-strength steel, stainless steel, etc., and fibers of metals other than steel, such as copper fibers, can be used. As for the material, steel fiber made from low carbon steel shows the best performance. In the case of steel fibers, it is desirable that the content of these elements be as low as possible, since manganese and chromium accelerate the carburization reaction and reduce the strength of the resulting composite material.
金属繊維のサイズも特に限定されないが、高い強度の成
形体を得るという観点からは、通常は太さ（繊維径、よ
り厳密には相当直径、すなわち繊維の断面を同じ断面積
を持つ円と考えることにより求められる繊維直径）０．
５ｍｍ以下、特に０．３ｍｍ以下で、長さ１ｍｍ以上、
好ましくは３ｏＩＩＩ＋以上のものが好ましい。ただし
、形状の異なる２種以上の金属繊維を用いる時は、繊維
径約１ｍｍまでのより太い繊維を一部使用することもで
きる。The size of the metal fibers is not particularly limited either, but from the perspective of obtaining a molded product with high strength, the thickness (fiber diameter, more precisely equivalent diameter), i.e. the cross section of the fiber is considered to be a circle with the same cross-sectional area. Fiber diameter determined by ) 0.
5 mm or less, especially 0.3 mm or less, and 1 mm or more in length,
Preferably, it is 3oIII+ or more. However, when using two or more types of metal fibers with different shapes, it is also possible to partially use thicker fibers with a fiber diameter of up to about 1 mm.
金属繊維のアスペクト比は、一般には１０以上が好まし
い。アスペクト比が１００を超える繊維も使用できるが
、炭素材原料との混合時に繊維がからみやすく、繊維の
均一分散が困難であるので、多量には配合しない方が好
ましい。Generally, the aspect ratio of the metal fiber is preferably 10 or more. Although fibers with an aspect ratio exceeding 100 can be used, it is preferable not to mix them in large amounts because the fibers tend to get entangled when mixed with the carbon material raw material and it is difficult to uniformly disperse the fibers.
金属４１ｔ維の配合量は特に限定されないが、耐摩耗性
、機械的強度および電気比抵抗の面から、少なくとも１
０体積％以上の金属繊維の配合が好ましい。５０〜６０
体積％の高い配合量も可能であるが、金属繊維の配合量
が５０％を超えるとスペークが多くなり、複合材の摩耗
量が多くなる傾向がある。The amount of metal 41t fibers is not particularly limited, but from the viewpoint of wear resistance, mechanical strength, and electrical resistivity, at least 1
It is preferable to include metal fibers in an amount of 0% by volume or more. 50-60
Although a high volume % blending amount is possible, if the blending amount of metal fiber exceeds 50%, the number of spaces increases and the amount of wear of the composite material tends to increase.
このため、金属繊維の配合量は、好ましくは１０〜４０
体積％、より好ましくは１５〜３５体積％である。For this reason, the blending amount of metal fiber is preferably 10 to 40
% by volume, more preferably 15-35% by volume.
金属繊維の表面被覆は、めっき、蒸着等の任意の方法で
実施できるが、めっきが一般的である。The surface of the metal fiber can be coated by any method such as plating or vapor deposition, but plating is commonly used.
表面被覆層の厚みは、０．１ｍｍ程度と薄くても、浸炭
反応抑制に十分な効果がある。また、被覆層の厚みの上
限は特にないが、経済性の観点からは層厚は１０ｍｍ以
下が適当である。好ましい層厚は０．１〜５μｍ、特に
０．２〜１μｍである。Even if the thickness of the surface coating layer is as thin as about 0.1 mm, it is sufficiently effective in suppressing the carburizing reaction. Further, although there is no particular upper limit to the thickness of the coating layer, from the viewpoint of economic efficiency, the layer thickness is suitably 10 mm or less. Preferred layer thicknesses are between 0.1 and 5 μm, especially between 0.2 and 1 μm.
金属繊維の表面被覆に用いる材料としては、炭化物生成
傾向が金属繊維の金属以下の任意の材料を使用できるが
、パンタグラフ摺板の場合には、耐浸炭性に優れている
ことの他に、さらに電気比抵抗が低いことが必要である
ため、銅、ニッケル、アルミニウムおよびコバルトの１
ａもしくは２種以上の金属材料が好ましい。被覆層とし
て電気比抵抗が高いものを用いると、金属繊維の導電性
が有効に発現せず、複合材の電気比抵抗が著しく高くな
り、パンタグラフ摺板には不適当となるからである。As the material used for the surface coating of the metal fibers, any material can be used that has a tendency to generate carbides less than that of the metal of the metal fibers, but in the case of pantograph sliding plates, in addition to having excellent carburization resistance, it also has the following properties: Since it is necessary to have low electrical resistivity, copper, nickel, aluminum and cobalt are used.
A or two or more kinds of metal materials are preferred. This is because if a material with a high electrical resistivity is used as the coating layer, the electrical conductivity of the metal fibers will not be effectively developed, and the electrical resistivity of the composite material will become extremely high, making it unsuitable for pantograph sliding plates.
しかし、ブレーキ材や摺動材等の非集電用途に用いると
きは、電気比抵抗は問題とならないため、アルミナ、炭
化ケイ素（ＳｉＣ）、シリカ（Ｓｉｎ−）等の電気比抵
抗の高いセラミックス等の材料も表面被覆層として使用
可能である。セラミックス材料の被覆は、プラズマ溶射
等により実施できる。However, when used in non-current collecting applications such as brake materials and sliding materials, electrical resistivity is not a problem, so ceramics with high electrical resistivity such as alumina, silicon carbide (SiC), and silica (Sin-) are used. materials can also be used as the surface coating layer. Coating with the ceramic material can be performed by plasma spraying or the like.
表面を炭化物生成傾向の小さい異種材料で被覆した金属
繊維を使用すると、成形体を炭化する際の金属繊維の浸
炭反応が実質的に抑制され、得られた複合材の強度、特
に曲げ強度が大きく改善される。When using metal fibers whose surfaces are coated with a dissimilar material with a low tendency to form carbides, the carburization reaction of the metal fibers during carbonization of the compact is substantially suppressed, and the strength of the resulting composite material, especially the bending strength, is increased. Improved.
このためには、全部の金属繊維の表面を異種材料で被覆
してもよい。しかし、金属繊維の表面被覆処理は、曲げ
強度の改善には非常に有効であるが、硬くて耐摩耗性に
優れたセメンタイトが少なくなるため、得られた炭素・
金属複合材の耐摩耗性が多少劣化する傾向がある。For this purpose, the surfaces of all metal fibers may be coated with a different material. However, although surface coating treatment of metal fibers is very effective in improving bending strength, it reduces the amount of cementite that is hard and has excellent wear resistance.
The wear resistance of metal composites tends to deteriorate to some extent.
この複合材の耐摩耗性の劣化を防止するために、金属繊
維の一部に、表面被覆が施されていないものを使用する
こともできる。この表面被覆のない金属繊維は、炭化時
にマトリックスの炭素と反応して、耐摩耗性に優れたセ
メンタイトを生成するので、得られた複合材の耐摩耗性
が向上する。このように、表面被覆された金属繊維と、
未被覆の金属繊維とを混合使用することにより、曲げ強
度と耐摩耗性のバランスのとれた炭素・金属複合材が得
られる。In order to prevent deterioration of the abrasion resistance of this composite material, it is also possible to use metal fibers that are not surface coated in part. This metal fiber without a surface coating reacts with carbon in the matrix during carbonization to produce cementite with excellent wear resistance, so that the wear resistance of the resulting composite material is improved. In this way, surface-coated metal fibers and
By mixing and using uncoated metal fibers, a carbon-metal composite material with a good balance of bending strength and wear resistance can be obtained.
表面被覆された金属繊維と非被覆の金属繊維とを混合使
用する場合、両者の配合比率は特に限定されないが、セ
メンタイトは少量でも耐摩耗性の改善効果が大きいので
、良好な曲げ強度を確保するように、表面被覆された金
属繊維の比率は、好ましくは全繊維の５０重量％以上、
より好ましくは６５重量％以上とする。When using a mixture of surface-coated metal fibers and uncoated metal fibers, the mixing ratio of the two is not particularly limited, but even a small amount of cementite has a large effect on improving wear resistance, so good bending strength is ensured. As such, the proportion of surface-coated metal fibers is preferably 50% by weight or more of the total fibers,
More preferably, it is 65% by weight or more.
金属繊維の炭化時の浸炭反応は、炭化物生成傾向が金属
繊維の金属以下の異種金属の粉末を、金属繊維と共に炭
素材原料中に添加することによっても効果的に抑制でき
、得られる複合材の強度の改善をもたらす。The carburizing reaction during carbonization of metal fibers can also be effectively suppressed by adding powder of a dissimilar metal whose carbide generation tendency is lower than that of the metal fiber to the carbon material raw material together with the metal fibers, and the resultant composite material Provides improved strength.
金属粉としては、炭化物生成傾向が金属繊維の金属以下
の任意の金属もしくは合金の粉末が使用できる。スチー
ルファイバーの場合は、銅、ニッケル、アルミニウム、
コバルト等が好ましい。As the metal powder, any metal or alloy powder whose carbide generation tendency is lower than that of the metal fiber can be used. For steel fibers, copper, nickel, aluminum,
Cobalt and the like are preferred.
このような金属粉を添加して製造した炭素・金属繊維複
合材の元素分布をＥ ＰＭＡ （ｅｌｅｃｔｒｏｎｐｒ
ｏｂｅ ｍ１ｃｒｏ ａｎａｌｙｚｅｒ）により調べた
ところ、金属繊維の内部に添加金属元素の存在が認めら
れた。E PMA (electron pr
As a result of examination using an OBE M1CRO analyzer, the presence of additional metal elements inside the metal fibers was confirmed.
また、Ｘ線回折による分析でセメンタイトがほとんど認
められなかった。In addition, almost no cementite was observed in X-ray diffraction analysis.
これらの分析結果から、炭化のための焼成時に、添加し
た金属粉が接触する金属繊維中に拡散して合金化し、こ
れが金属繊維の浸炭反応を抑制することが判明した。These analysis results revealed that during firing for carbonization, the added metal powder diffuses into the contacting metal fibers to form an alloy, which suppresses the carburization reaction of the metal fibers.
マンガンやクロムのように、炭化物生成傾向が大きな金
属粉を配合すると、得られた炭素・金属複合材の強度は
、金属粉を配合しない場合よりもさらに低下する。その
原因は、浸炭反応が促進されて金属繊維の強度が低下す
るとともに、金属繊維と炭素マトリックスとの界面に空
隙（ボイド）が生成し、繊維とマトリックスとの接合性
が悪化するためであることが判明した。When a metal powder with a strong tendency to form carbides, such as manganese or chromium, is blended, the strength of the resulting carbon-metal composite material is further reduced than when no metal powder is blended. The reason for this is that the carburizing reaction is accelerated, which reduces the strength of the metal fibers, and also creates voids at the interface between the metal fibers and the carbon matrix, deteriorating the bonding properties between the fibers and the matrix. There was found.
有用な金属粉は、前記のような炭化物生成傾向の小さい
１種もしくは２種以上の元素を含む金属粉である。２種
以上の元素を含む金属粉は、単独の元素を主成分とする
２種以上の金属粉の混合物、あるいは２種以上の元素を
合金化した合金粉末のいずれでもよい。A useful metal powder is a metal powder containing one or more elements that have a small tendency to form carbides as described above. The metal powder containing two or more types of elements may be either a mixture of two or more metal powders containing a single element as a main component, or an alloy powder obtained by alloying two or more elements.
また、添加金属粉の純度は、マンガンやクロム等の望ま
しくない元素の量が多くならない範囲であれば、あまり
問題とはならない。例えばフェロニッケルのような、鉄
とニッケルとの合金も使用できる。Further, the purity of the added metal powder does not matter much as long as the amount of undesirable elements such as manganese and chromium does not increase. Alloys of iron and nickel, such as ferronickel, can also be used.
添加する金属粉の平均粒径は約１００μｍ以下、特に約
０．５〜５０μｍが好ましい。金属粉の平均粒径が約１
００μｍを超えると、金属粒子の周囲にクラックが発生
し易くなり、また金属粒子と金属４！＆維との接触点の
数が減少するため、合金化による浸炭反応抑制の効果が
低下する。The average particle diameter of the metal powder to be added is preferably about 100 μm or less, particularly about 0.5 to 50 μm. The average particle size of metal powder is approximately 1
If it exceeds 00 μm, cracks tend to occur around the metal particles, and the metal particles and metal 4! & Since the number of contact points with the fibers decreases, the effect of suppressing the carburizing reaction by alloying decreases.
炭化物生成傾向の小さい金属粉を配合する場合には、金
属繊維は未被覆のものでもよい。上記した添加金属粉の
効果により、未被覆の金属繊維を使用しても、得られた
炭素・金属複合材の強度は満足できる程度に改善される
。また、金属繊維の一部または全部として、上記のよう
に表面被覆した金属繊維を使用することもでき、それに
より、曲げ強度の一層大きな改善が得られる。When blending metal powder with a small tendency to form carbides, the metal fibers may be uncoated. Due to the effect of the above-mentioned additive metal powder, the strength of the obtained carbon-metal composite material is improved to a satisfactory extent even if uncoated metal fibers are used. It is also possible to use surface-coated metal fibers as described above as some or all of the metal fibers, which results in an even greater improvement in bending strength.
金属繊維の表面被覆と、金属粉の添加の両方を用いる場
合、被覆金属と金属粉の種類は、いずれも炭化物生成傾
向が金属繊維の金属と同等が、これより小さい限り、同
じものでも、異なるものでもよい。When using both the surface coating of metal fibers and the addition of metal powder, the types of coating metal and metal powder may be the same or different, as long as the tendency to form carbides is equal to but smaller than that of the metal of the metal fibers. It can be anything.
金属粉の配合方法としては、単に金属粉を金属繊維と共
に炭素材原料に添加し、常法により混合しただけでも、
目的の効果は達成される。しかし、炭素材原料に加える
前に、金属繊維（未被覆または一部もしくは全部が表面
被覆のいずれでもよい）と金属粉のみを予め混合して、
金属繊維に金属粉を付着させた後、炭素材原料と混合す
ると、より高い複合材の強度が得られる。As for the mixing method of metal powder, it is possible to simply add the metal powder to the carbon material raw material together with the metal fibers and mix them using a conventional method.
The desired effect is achieved. However, before adding it to the carbon material raw material, only the metal fibers (which may be uncoated or partially or fully surface coated) and metal powder are mixed in advance.
If metal powder is attached to metal fibers and then mixed with a carbon material raw material, higher strength of the composite material can be obtained.
この場合、金属粉が付着した金属繊維に、樹脂系や油脂
等の結合剤や界面活性剤を少量添加して付着性を高める
と、より効果的である。In this case, it is more effective to increase the adhesion by adding a small amount of a binder or surfactant such as resin or oil to the metal fiber to which the metal powder has adhered.
金属繊維に加えて上記の金属粉を添加する場合、その添
加量は特に制限されないが、金属繊維が全く未被覆のも
のである場合で、金属粉の好ましい配合量は原料全体の
０．５〜２０体積％、より好ましくは １〜１０体積％
である。金属繊維が上記のように表面被覆されている場
合には、金属粉の配合量は少なくすることができる。When adding the above-mentioned metal powder in addition to metal fibers, the amount added is not particularly limited, but when the metal fibers are completely uncoated, the preferred amount of metal powder is 0.5 to 0.5 of the total raw material. 20% by volume, more preferably 1-10% by volume
It is. When the surface of the metal fiber is coated as described above, the amount of metal powder added can be reduced.
上記したように、炭化工程中の金属繊維の浸炭反応は、
金属繊維に炭化物生成傾向が小さい金属が合金化される
ことで抑制される。したがって、金属繊維をこのような
金属と予め合金化させておくことにより、金属繊維の浸
炭反応とそれによる強度低下を防止することができる。As mentioned above, the carburization reaction of metal fibers during the carbonization process is
This can be suppressed by alloying metal fibers with metals that have a small tendency to form carbides. Therefore, by alloying the metal fiber with such a metal in advance, it is possible to prevent the carburization reaction of the metal fiber and the resulting decrease in strength.
このような事前合金化は、例えばスチールファイバーを
、炭化物生成傾向が鉄基下の銅、ニッケル、コバルト、
アルミニウムの一種もしくは２種以上の合金元素の金属
で被覆するか、および／またはこれらの合金元素を含む
金属粉と混合した後、炭素材原料と混合する前に、高温
で熱処理して合金元素を金属繊維の内部に拡散させ、合
金化することにより実施できる。表面被覆や金属粉の添
加は、前記と同様でよい。熱処理温度は、金属繊維の融
点以下で、金属繊維の内部に実質量の合金元素を拡散さ
せるのに十分な温度および時間で行う。Such pre-alloying can be used, for example, to prepare steel fibers with iron-based copper, nickel, cobalt,
After coating aluminum with a metal containing one or more alloying elements and/or mixing it with metal powder containing these alloying elements, the alloying element is heat-treated at a high temperature before being mixed with the carbon material raw material. This can be carried out by diffusing into the interior of metal fibers and alloying them. The surface coating and addition of metal powder may be the same as described above. The heat treatment temperature is below the melting point of the metal fibers and is carried out at a temperature and for a time sufficient to diffuse a substantial amount of the alloying element into the interior of the metal fibers.
スチールファイバーの場合の熱処理条件は、合金元素に
よっても異なるが、約６００〜１１００℃の温度で約３
０分〜３時間程度であろう。The heat treatment conditions for steel fibers vary depending on the alloying element, but at a temperature of about 600 to 1100 °C, about 3
It will take about 0 minutes to 3 hours.
炭素材原料に混合する前に事前合金化のための熱処理を
実施しなくても、炭素・金属複合材の製造過程で、炭素
材原料の炭化のために成形体を焼成する工程で、金属繊
維は上記の熱処理と同様の温度に相当の時間さらされる
。Even if heat treatment for pre-alloying is not performed before mixing with the carbon material raw material, metal fibers can is exposed to temperatures similar to those in the heat treatment described above for a considerable period of time.
したがって、この発明により、金属繊維の一部もしくは
全部として炭化物生成傾向の小さい異種金属で表面被覆
された金属繊維を炭素材原料に配合するか、および／ま
たは金属繊維に加えて炭化物生成傾向の小さい異種金属
の金属粉を炭素材原料に配合すると、成形体の焼成工程
でこれらの異種金属が金属繊維とある程度合金化され、
それによりセメンタイトの生成が抑制されて強度改善が
得られる。Therefore, according to the present invention, a metal fiber whose surface is coated with a dissimilar metal having a small tendency to form carbides is blended into the carbon material raw material as part or all of the metal fiber, and/or a metal fiber having a small tendency to form carbides is added to the carbon material raw material. When metal powders of dissimilar metals are blended into carbon material raw materials, these dissimilar metals are alloyed to some extent with metal fibers during the firing process of the compact, and
This suppresses the formation of cementite and improves the strength.
成形方法としては、押出し成型法、ＣＩＰ（ｃｏｌｄ
１ｓｏｓｔａｔｉｃ ｐｒｅｓｓ）法等の冷間型込め法
、加圧加熱成形法等を含む各種の方法が採用できる。Molding methods include extrusion molding, CIP (cold
Various methods can be employed, including a cold molding method such as a 1sostatic press method, a pressure heating molding method, and the like.
成形で得られた成形体は、常法で炭化して、炭素・スチ
ールファイバー複合材とすることができる。このうち、
バインダーとしてピッチを使用した二元系の材料原料を
使用し、加圧加熱成形する方法が、最も強度および耐摩
耗性の良好な炭素・金属複合材が得られる。The molded body obtained by molding can be carbonized by a conventional method to form a carbon/steel fiber composite material. this house,
A method that uses a binary material raw material using pitch as a binder and pressurizes and heat-forms it yields a carbon-metal composite material with the best strength and wear resistance.
加圧加熱成形条件としては、バインダーピッチが固化す
る温度域、すなわち４８０℃以上の温度域で加圧下に加
熱することが、・強度および耐摩耗性の発現のために好
ましい。したがって、加圧加熱成形の加圧加熱最高温度
が４８０℃以上、より好ましくは５００℃以上となるよ
うにする。As for the pressure and heat molding conditions, it is preferable to heat under pressure in a temperature range where the binder pitch solidifies, that is, a temperature range of 480° C. or higher, in order to develop strength and wear resistance. Therefore, the maximum pressure and heating temperature in pressure and heat molding is set to be 480°C or higher, more preferably 500°C or higher.
加圧加熱温度の上限は約６００℃であり、これを超える
と成形時に成形体中に割れが発生し易くなる。The upper limit of the pressure and heating temperature is about 600° C., and if this temperature is exceeded, cracks are likely to occur in the molded product during molding.
加圧加熱成形の圧力は、少なくとも常温〜加圧加熱最高
温度の一部において、好ましくは４０ｋｇ／ｃｍ″以上
、より好ましくは８０ｋｇ／ｃｍ”以上とする。The pressure for pressurizing and heating molding is preferably 40 kg/cm'' or more, more preferably 80 kg/cm'' or more at least at room temperature to a portion of the pressurizing and heating maximum temperature.
成形圧力が４０ｋｇ／ｃｍ″ より低いと、バインダー
と金属繊維間の結合力が低下し、耐摩耗性が劣化する傾
向がある。When the molding pressure is lower than 40 kg/cm'', the bonding force between the binder and the metal fibers tends to decrease, and the abrasion resistance tends to deteriorate.
成形体の焼成は、非酸化性雰囲気中において金属繊維の
融点より低温で行う。これにより炭素材原料が炭化して
炭素質マトリックス中に金属繊維が分布する炭素・金属
複合材が得られる。The molded body is fired in a non-oxidizing atmosphere at a temperature lower than the melting point of the metal fiber. As a result, the carbon material raw material is carbonized to obtain a carbon-metal composite material in which metal fibers are distributed in a carbonaceous matrix.
焼成温度は、炭素の強度を十分に発現させるという点か
ら９００℃以上が好ましい。一方、焼成温度が１１００
℃を超えると、表面被覆金属繊維を使用した場合の被覆
層の溶融による効果の減少や、金属繊維自体の変質によ
る複合材の強度低下が起るので好ましくない。したがっ
て、好ましい焼成温度は９００〜１０５０℃である。The firing temperature is preferably 900° C. or higher in order to fully develop the strength of carbon. On the other hand, the firing temperature is 1100
If the temperature exceeds .degree. C., it is not preferable because the effect of the surface-coated metal fibers due to melting of the coating layer decreases or the strength of the composite material decreases due to deterioration of the metal fibers themselves. Therefore, the preferred firing temperature is 900-1050°C.
こうして得られた炭素・金属複合材は、特に鉄道用パン
タグラフ摺板に好適な強度、耐摩耗性および電気特性を
有するが、その他の集電摺動部材（例えば集電ブラシ）
、あるいは単なる摺動部材（例えばブレーキ軸受、シー
ル材）にも利用可能である。The carbon-metal composite material thus obtained has strength, wear resistance, and electrical properties particularly suitable for railway pantograph sliding plates, but is also suitable for use in other current collecting sliding members (e.g. current collecting brushes).
Alternatively, it can also be used for simple sliding members (eg, brake bearings, sealing materials).
実施例
次に、この発明の実施例を示す。なお、本実施例はこの
発明を制限するものではない。Examples Next, examples of the present invention will be shown. Note that this example does not limit the present invention.
実施例１ 本実施例は、銅めっきした金属繊維の使用例を示す。Example 1 This example shows the use of copper-plated metal fibers.
レギュラーグレード石油コークスを１０００℃で炭化し
た後、直径１０ｍｍのステンレス球を詰めた振動ミルに
入れ、４時間粉砕して平均粒径１１．５μｍのコークス
粉を得、これを成型用骨材として用いた。After carbonizing regular grade petroleum coke at 1000°C, it was placed in a vibrating mill packed with stainless steel balls with a diameter of 10 mm, and crushed for 4 hours to obtain coke powder with an average particle size of 11.5 μm, which was used as aggregate for molding. there was.
バインダーピッチとしては、コールタールｍｍｌ（ｇの
減圧下４４０℃で１時間熱処理して得た軟化点２５０℃
のコールタールピッチを６０メツシユ以下に粉砕して用
いた。The binder pitch is coal tar mml (g) with a softening point of 250°C obtained by heat treatment at 440°C for 1 hour under reduced pressure.
Coal tar pitch was ground to 60 mesh or less and used.
金属繊維としては、０． １ｍｍＸ ０． １ｍｍＸ
＆さ３■の低炭素鋼繊維（材質： ＳＰＣＣ−ＩＢ）を
用いた。このスチールファイバーを、重量比で８０倍量
のめっき液（組成を第１表に示す）中に、第２表に示す
所定の時間、室温で浸漬して銅めつきを施した。その後
、繊維をめっき液から取出し、十分に水洗し、アセトン
で洗浄後、窒素中１００℃で乾燥して、銅めっきされた
スチールファイバーを得た。このめっき層の平均めっき
層厚を第２表に併せて示す。As a metal fiber, 0. 1mm x 0. 1mmX
A low carbon steel fiber (material: SPCC-IB) with a diameter of 3 cm was used. The steel fibers were immersed in a plating solution (composition shown in Table 1) of 80 times the weight (composition shown in Table 1) at room temperature for a predetermined period of time shown in Table 2 to perform copper plating. Thereafter, the fibers were taken out from the plating solution, thoroughly washed with water, washed with acetone, and dried at 100° C. in nitrogen to obtain copper-plated steel fibers. The average plating layer thickness of this plating layer is also shown in Table 2.
なお、金属繊維にめっきを施した場合の繊維上に形成さ
れた平均めっき層厚みは、繊維の公称形状、めっき金属
の付着重量、および金属繊維の金属とめっき金属の真比
重に基いて算出した。In addition, the average plating layer thickness formed on the fiber when plating is applied to the metal fiber was calculated based on the nominal shape of the fiber, the attached weight of the plating metal, and the true specific gravity of the metal of the metal fiber and the plating metal. .
これらの原料を、コークス粉２２重量部、バインダーピ
ッチ１０重量部、ファイバー６８重量部の比率で混合し
、成形原料として用いた。スチールファイバーの量は、
成形体中での体積換算での比率が約３０体積％となる量
であった。These raw materials were mixed in a ratio of 22 parts by weight of coke powder, 10 parts by weight of binder pitch, and 68 parts by weight of fibers and used as a forming raw material. The amount of steel fiber is
The amount was such that the ratio in terms of volume in the molded body was about 30% by volume.
この成形原料を加圧加熱成形装置を用いて成形した。そ
の際、成形原料３５０ｇを内径１００ｍｍの鋼製金型に
入れ、昇温速度１０℃／ｍｉｎで３５０℃まで無加圧で
加熱し、３５０℃から２２０ｋｇ／ｃｍ’で加圧しなが
ら５℃／ｍｉｎの昇温速度で５４０℃まで昇温し、２２
０ｋｇ／ｃｍ ”、５４０℃に１．５時間保持した後、
冷却して成形体を得た。This molding raw material was molded using a pressure and heat molding device. At that time, 350 g of the forming raw material was placed in a steel mold with an inner diameter of 100 mm, heated at a temperature increase rate of 10°C/min to 350°C without pressure, and then heated from 350°C to 5°C/min while applying pressure at 220 kg/cm'. The temperature was raised to 540℃ at a heating rate of 22
0kg/cm”, after being held at 540°C for 1.5 hours,
A molded body was obtained by cooling.
得られた成型体を粉コークス中に詰め、窒素雰囲気中で
室温から１００℃／ｈｒの昇温速度で４８０℃まで昇温
させ、この温度に２時間保持した後、１５℃／ｈｒで１
０００℃まで昇温させ、この温度に３時間保。The obtained molded body was packed in coke powder, heated from room temperature to 480°C at a heating rate of 100°C/hr in a nitrogen atmosphere, held at this temperature for 2 hours, and then heated at a rate of 15°C/hr for 1 hour.
000℃ and kept at this temperature for 3 hours.
持した後冷却して、炭素・スチールファイバー複合材を
得た。After holding and cooling, a carbon/steel fiber composite material was obtained.
得られた炭素・金属複合材の曲げ強度を測定した。測定
方法は、この複合材から１０ｍｍ Ｘ ６０ｍｍ Ｘ厚
み１０ｍｍ （成形体厚みが約１０ｍｍのときは焼上り
のまま）の試験片の６Ｏｒａｍの辺の方向が複合材の長
辺と一致するように切出し、曲げスパン４０ｍ＋ｍで３
点曲げ試験法により測定した。曲げ試験時の荷重負荷方
向は、成形時のプレス方向と同方向とした。The bending strength of the obtained carbon/metal composite material was measured. The measurement method was to cut out a 10 mm x 60 mm x 10 mm thick (as baked when the molded product is about 10 mm thick) test piece from this composite material so that the direction of the 6-oram side coincided with the long side of the composite material. , bending span 40m+m 3
Measured by point bending test method. The load direction during the bending test was the same as the pressing direction during molding.
曲げ強度の測定結果を第２表に示す。なお、第２表には
比較のために、金属繊維として銅めっき無しのスチール
ファイバーのみを用いた炭素・スチールファイバー曲げ
強度を合せて示す。The measurement results of bending strength are shown in Table 2. For comparison, Table 2 also shows the bending strength of carbon/steel fibers using only steel fibers without copper plating as the metal fibers.
第２表の結果より、同めっきによる表面被覆を施したス
チールファイバーから得られた複合材は、銅めっき無し
の繊維を用いたものに比べて、曲げ強度が著しく改善さ
れていることがわかる。From the results in Table 2, it can be seen that the bending strength of composites obtained from steel fibers coated with the same plating is significantly improved compared to those using fibers without copper plating.
第１表 めっき液組成 第２表 めっき層厚みと曲げ強度 実施例２ 本実施例はニッケルめっき繊維を使用した例を示す。Table 1 Plating solution composition Table 2 Plating layer thickness and bending strength Example 2 This example shows an example using nickel-plated fibers.
実施例１と同じスチールファイバーに、第３表に示すめ
っき液を使用した無電解ニッケルめっきを施して得た、
ニッケルめっきされたスチールファイバーを使用し、実
施例１を繰返した。Obtained by electroless nickel plating using the plating solution shown in Table 3 on the same steel fiber as in Example 1.
Example 1 was repeated using nickel plated steel fibers.
なお、ニッケルめっきは、スチールファイバーに対して
重量比で１００倍量を使用しためっき液中に繊維を２０
分間浸漬して施した。めっき中、めっき液のＰＲはアン
モニア水の添加により９に調整し、また液温を８５℃に
保持した。めっき終了後、スチールファイバーを実施例
１と同様に水洗および乾燥し、ニッケルめっきされたス
チールファイバーを得た。この繊維の表面めっき層の平
均厚みは約１．２μｍであった。For nickel plating, add 20% of the fibers to the plating solution using 100 times the weight of the steel fibers.
It was applied by soaking for a minute. During plating, the PR of the plating solution was adjusted to 9 by adding aqueous ammonia, and the solution temperature was maintained at 85°C. After completion of plating, the steel fibers were washed with water and dried in the same manner as in Example 1 to obtain nickel-plated steel fibers. The average thickness of the surface plating layer of this fiber was about 1.2 μm.
このニッケルめっきされたスチールファイバーを使用し
て得た、繊維配合量３０体積％の炭素・スチール複合材
の曲げ強度は１８００ｋｇ／ｃｍ ’ と高い値を示し
た。The bending strength of a carbon-steel composite material with a fiber content of 30% by volume obtained using this nickel-plated steel fiber was as high as 1800 kg/cm'.
第３表 めっき液組成
実施例３
本実施例は、めっき繊維と非めっき繊維との両者を配合
した例を示す。Table 3 Plating Solution Composition Example 3 This example shows an example in which both plated fibers and non-plated fibers were blended.
実施例１で使用したものと同じスチールファイバーを１
重量比で１０倍量の実施例１の第１表に示す組成のめっ
き液中に２０℃の室温で２時間浸漬した後、十分水洗し
、その後窒素中１００℃で乾燥して、銅めっきされたス
チールファイバーを得た。このスチールファイバーの平
均めっき層厚みを実施例１に記載のように算出したとこ
ろ、約０．５μｍであった。1 of the same steel fibers used in Example 1
After being immersed for 2 hours at room temperature of 20°C in a plating solution having a composition shown in Table 1 of Example 1 in an amount 10 times the amount by weight, it was thoroughly washed with water, and then dried at 100°C in nitrogen to form a copper plated product. obtained steel fiber. The average plating layer thickness of this steel fiber was calculated as described in Example 1 and was approximately 0.5 μm.
次に、実施例１で用いたものと同じコークス粉およびバ
インダーピッチに、前記の銅めっきスチールファイバー
および／またはめっきしていない未被覆のスチールファ
イバーを、第４表に示す割合で混合しく金属繊維の比率
は約３０体積％）、得られた成形原料４５０ｇを、内寸
１００ｍｍＸ １０（ｌｎｍの鋼製金型に入れ、加圧加
熱成形した。Next, the copper-plated steel fibers and/or unplated uncoated steel fibers were mixed with the same coke powder and binder pitch as those used in Example 1 in the proportions shown in Table 4. 450 g of the obtained molding raw material was placed in a steel mold with an inner dimension of 100 mm x 10 (1 nm), and was pressurized and heated.
加圧加熱成形は、昇温速度３℃／ｍｉｎで昇温を行い、
室温から３００℃までは１ｋｇ／ｃｍ ”の加圧、３０
０℃から５５０℃までは２００ｋｇ／ｃｍ’で加圧し、
５５０℃、２００ｋｇ／ｃａｂ”に１時間保持した後、
冷却することにより行った。For pressure and heat molding, the temperature is raised at a temperature increase rate of 3°C/min.
From room temperature to 300℃, pressurize at 1 kg/cm, 30
From 0℃ to 550℃, pressurize at 200kg/cm'.
After holding at 550℃ and 200kg/cab for 1 hour,
This was done by cooling.
この成形体を、実施例１と同様の方法で炭化・焼成処理
して、炭素・スチール複合材を得た。この複合材の曲げ
強度を測定した。This molded body was carbonized and fired in the same manner as in Example 1 to obtain a carbon/steel composite material. The bending strength of this composite material was measured.
さらに、複合材の摩耗試験を、ビン・オン・ディスク型
の摩耗試験機により行った。その際、摺動面のサイズが
８ｍｍ Ｘ ８ｍｍで、摺動面がプレス面と平行な摩耗
試験片を作成した。相手材としては、直径３００ＩＩＩ
ｒｎの銅板（摺動部半径１３２＋＋ｕｏ、摺動面粗さ９
０μｍ）を用い、摺動面と銅板の間に５ＯＡ、５０Ｈｚ
の交流を通電しながら押付は荷重３ｋｇ、摺動速度１１
００ｋ／ｈｒの条件下、１時間回転摺動させた。この摺
動。Furthermore, abrasion testing of the composite material was conducted using a bottle-on-disk type abrasion tester. At that time, a wear test piece was prepared in which the size of the sliding surface was 8 mm x 8 mm, and the sliding surface was parallel to the press surface. The mating material is 300III in diameter.
rn copper plate (sliding part radius 132++uo, sliding surface roughness 9
0μm), 5OA, 50Hz between the sliding surface and the copper plate.
When pressing while applying AC current, the load was 3 kg and the sliding speed was 11
Rotation and sliding was performed for 1 hour under the condition of 00 k/hr. This sliding.
時間の経過後、試験片の摺動面の摩耗厚みを測定し、耐
摩耗性を評価した。After the elapse of time, the abrasion thickness of the sliding surface of the test piece was measured and the abrasion resistance was evaluated.
また、電気比抵抗は、上記と同様の試験片（１０ｍｍ
Ｘ １０ｍｍ Ｘ厚み１０ｍｍ）を用いて、電流の流れ
る方向が長さ６０＋ｎｍの方向となるようにして４端子
法により測定した。In addition, the electrical specific resistance was measured using the same test piece as above (10 mm
Measurement was performed using a four-terminal method using a 4-terminal probe (10 mm x 10 mm thick), with the current flowing direction being in the direction of the length 60+nm.
これらの試験結果を第４表に併せて示す。These test results are also shown in Table 4.
第４表から明らかなごとく、めっき繊維と非めっき繊維
とを配合したもの、およびめっき繊維のみを用いたもの
は、めっき繊維を用いずに非めっき繊維のみを用いたも
のに比べて、
曲げ強度お上
び電気比抵抗共に優れている。As is clear from Table 4, the flexural strength of the mixture of plated fibers and non-plated fibers, and the one using only plated fibers, is higher than the one using only non-plated fibers without plated fibers. Excellent in both height and electrical resistivity.
以下余白
実施例４
実施例１で使用したものと同じコークス粉、バインダー
ピッチに実施例１に記載したものと同じ未被覆（めっき
処理前のもの）スチールファイバーと、さらに銅粉（平
均粒径５μｍ）、ニッケル粉（平均粒径１０μｍ）、ア
ルミニウム粉（平均粒径１０μｌ）およびコバルト粉（
平均粒径１０μｍ）から選ばれた金属粉（いずれもＪＩ
Ｓ １級グレード）を使用して、成形原料を調整した。The following blank space is used in Example 4: the same coke powder and binder pitch as used in Example 1, the same uncoated (before plating) steel fiber as described in Example 1, and copper powder (average particle size: 5 μm). ), nickel powder (average particle size 10 μm), aluminum powder (average particle size 10 μl), and cobalt powder (
Metal powder selected from average particle size 10 μm (both JI
A molding raw material was prepared using a molding material (S1 grade).
配合割合は、コークス粉２５重量部、バインダーピッチ
１０重量部、スチールファイバー５５重量部、金属粉１
０重量部であった。スチールファイバーの量は、成形体
中での体積換算での比率が約２５体積％となる量であっ
た。The blending ratio is 25 parts by weight of coke powder, 10 parts by weight of binder pitch, 55 parts by weight of steel fiber, and 1 part by weight of metal powder.
It was 0 parts by weight. The amount of steel fiber was such that the ratio in terms of volume in the molded body was about 25% by volume.
比較のために、金属粉として、炭化物生成傾向がスチー
ルより大きいマンガン粉またはクロム粉を用いた成形原
料、および金属粉を添加せず、スチールファイバーを６
５重量部に増加して添加した成形原料も調整した。For comparison, molding raw materials using manganese powder or chromium powder, which have a greater tendency to form carbides than steel, as metal powder, and steel fiber without adding metal powder were used.
The molding raw material added in an increased amount of 5 parts by weight was also prepared.
これらの成形原料を、実施例１に記載の方法と同様に、
成形および焼成・炭化して炭素・スチル複合材を得た。These molding raw materials were processed in the same manner as described in Example 1,
A carbon/still composite material was obtained by molding, firing, and carbonization.
この複合材の曲げ強度を第５に示す。The bending strength of this composite material is shown in the fifth column.
第５表から明らかなように、本発明により炭物生成傾向
の小さい金属粉を添加した複合材は金属粉を添加しない
ものに比べて曲げ強度が太く向上したが、マンガン粉ま
たはクロム粉を配すると、金属粉を添加しないものより
曲げ強度低下した。As is clear from Table 5, the bending strength of the composite material to which metal powder with a small tendency to form charcoal was added according to the present invention was significantly improved compared to that of the composite material without the addition of metal powder. As a result, the bending strength was lower than that without adding metal powder.
以下余白
表
化
き
一
が
第
（ζ
実施例５
実施例４のＮ０１１と同じ銅粉を使用し、成形材中のス
チールファイバーの体積比率が２５体積％、銅粉とコー
クス粉とを合せた体積比率が５３体体積上なるように、
銅粉の添加率を０．５〜１０体積％σ範囲内で変化させ
た成形原料を使用し、実施例４と同様に成形および焼成
・炭化して炭素・スチール複合材を得た。この複合材の
曲げ試験結果を、各成分の配合量と併せて第６表に示す
。The following blanks are shown in Table 1 (ζ Example 5 The same copper powder as N011 in Example 4 was used, the volume ratio of steel fiber in the molding material was 25% by volume, and the combined volume of copper powder and coke powder So that the ratio increases by 53 body volumes,
Using molding raw materials in which the addition rate of copper powder was varied within the range of 0.5 to 10% by volume σ, a carbon-steel composite material was obtained by molding, firing, and carbonization in the same manner as in Example 4. The bending test results of this composite material are shown in Table 6 together with the blending amounts of each component.
第６表から明らかなように、得られた炭素・スチール複
合材はいずれも高い曲げ強度を示し、０．５体積％とい
う少量の銅粉の添加でも曲げ強度が実質的に改善された
。As is clear from Table 6, all of the obtained carbon-steel composites exhibited high bending strength, and the bending strength was substantially improved even with the addition of a small amount of copper powder of 0.5% by volume.
以下余白
第
表
＊ （
）内は配合時宜量部数
実施例６
本実施例は、めっき繊維に金属粉をさらに配合した例を
示す。The following is a margin table * ( ) indicates the number of parts as appropriate when blending Example 6 This example shows an example in which metal powder was further blended into the plated fibers.
実施例１で使用したコークス粉およびバインダーピッチ
に、実施例１と同様に銅めっきされたスチールファイバ
ーおよび／または非めっきのスチールファイバー、およ
び金属粉として実施例４で用いたニッケル粉を配合して
成形原料を調整した。The coke powder and binder pitch used in Example 1 were mixed with copper-plated steel fibers and/or non-plated steel fibers as in Example 1, and the nickel powder used in Example 4 as metal powder. The molding raw materials were adjusted.
銅めっきには重量比で繊維の２０倍量の実施例１に記載
のめっき液にスチールファイバーを室温（２０℃）で１
時間浸漬することにより行った。この銅めっき層の平均
めっき厚みは０．２μｍであった。For copper plating, steel fibers were added to the plating solution described in Example 1 in an amount 20 times the weight of the fibers at room temperature (20°C).
This was done by soaking for a period of time. The average plating thickness of this copper plating layer was 0.2 μm.
上記の各成分を第７表に示す割合で配合して得た成形原
料３００ ｇを、内径１００ｍｍの鋼製金型に入れ、実
施例３と同様の条件で加熱加圧成形した。次に、得られ
た成形体を粉コークス中に詰め、窒素雰囲気中で室温か
ら１００℃／ｈｒの昇温速度で１０００℃まで温度を上
げ、１０００℃に３時間保持した後、冷却して炭素・ス
チール複合材を得た。この複合材の曲げ強度を第７表に
併せて示す。300 g of a molding raw material obtained by blending the above components in the proportions shown in Table 7 was placed in a steel mold with an inner diameter of 100 mm, and molded under heat and pressure under the same conditions as in Example 3. Next, the obtained compact was packed in coke powder, and the temperature was raised from room temperature to 1000°C at a rate of 100°C/hr in a nitrogen atmosphere, held at 1000°C for 3 hours, and then cooled and carbonated.・Obtained steel composite material. The bending strength of this composite material is also shown in Table 7.
金属粉とめっき金属ｇＩ！維とを併用することにより、 曲げ強度の一層の向上が可能となった。Metal powder and plated metal gI! By using it together with fiber, It has become possible to further improve bending strength.
以下余白
実施例７および８は、炭化物生成傾向が金属繊維の金属
以下の異種金属を事前に合金化した金属繊維の使用例を
示す。Examples 7 and 8 below show examples of the use of metal fibers in which dissimilar metals having a carbide generation tendency lower than that of the metal fibers are alloyed in advance.
実施例７
実施例１で使用したものと同じスチールファイバーに、
実施例１で用いた銅めつき液に、より同様に銅めっきを
施した。めっき液の使用量は、重量比で繊維の４０倍量
、めっき液浸漬時間は室温（２０℃）で２時間であった
。得られた銅めっき繊維の平均めっき層厚みは０．６１
Ｉｍであった。Example 7 The same steel fiber used in Example 1 was
Copper plating was performed using the copper plating solution used in Example 1 in a similar manner. The amount of plating solution used was 40 times the weight of the fibers, and the immersion time in the plating solution was 2 hours at room temperature (20° C.). The average plating layer thickness of the obtained copper-plated fiber was 0.61
It was Im.
このめっき処理スチールファイバーを、磁製ルツボに入
れ、さらにその周辺に粉コークスを充填し、窒素雰囲気
中３００℃／ｈｒの昇温速度で１０００℃まで昇温し、
１０００℃に２時間保持した後、冷却して銅が合金化し
たスチールファイバーを得た。これを金属繊維として成
形原料の調整に用いた。This plated steel fiber was placed in a porcelain crucible, the surrounding area was filled with coke powder, and the temperature was raised to 1000°C at a heating rate of 300°C/hr in a nitrogen atmosphere.
After being held at 1000° C. for 2 hours, it was cooled to obtain a copper-alloyed steel fiber. This was used as a metal fiber to prepare a molding raw material.
成形原料は、実施例１に記載のコークス粉２５重量部、
実施例１記載と同様のバインダーピッチ（熱処理温度４
５０℃）１０重量部、上記の銅合金化スチールファイバ
ー６５重量部の比率で配合することにより得た。繊維の
比率は、体積換算で３０体積％となる量であった。The molding raw material was 25 parts by weight of the coke powder described in Example 1,
Binder pitch similar to that described in Example 1 (heat treatment temperature 4
50° C.) and 65 parts by weight of the above-mentioned copper alloyed steel fiber. The proportion of fiber was 30% by volume.
また、比較のために、上記スチールファイバーをそのま
ま配合した成形原料を調整し、この成形原料４５０ｇを
使用し、加圧加熱成形時の加圧を２００ｋｇ／ｃｍｍ″
とした以外は、実施例Ｉと同じ条件で成形および炭化
・焼成した。In addition, for comparison, we prepared a molding raw material containing the above-mentioned steel fiber as it was, used 450 g of this molding raw material, and applied a pressure of 200 kg/cm'' during pressure and heat molding.
The molding, carbonization and firing were carried out under the same conditions as in Example I except for the following.
得られた炭素・スチール複合材の曲げ強度を調べた結果
、合金化処理繊維を配合した場合が１８５０ｋｇ／ｃｍ
”、未被覆繊維を配合した場合が１２５０ｋｇ／ ｃｍ
’であった。As a result of examining the bending strength of the obtained carbon-steel composite material, it was 1850 kg/cm when alloyed fiber was blended.
”, 1250 kg/cm with uncoated fibers
'Met.
実施例８
実施例１に記載のスチールファイバーを、重量比で２倍
量の平均粒径２０μｍのニッケル粉と共に、ロータリー
・キルンに入れ、回転させながら窒素雰囲気中で昇温速
度５００℃／ｈｒで９００℃まで昇温し、この温度に１
時間保持した後冷却した。その後、ニッケル粉を分離し
て、ニッケルが合金化したスチールファイバーを得た。Example 8 The steel fiber described in Example 1 was placed in a rotary kiln together with twice the weight of nickel powder having an average particle size of 20 μm, and heated at a heating rate of 500°C/hr in a nitrogen atmosphere while rotating. Raise the temperature to 900℃, and at this temperature
After holding for a period of time, it was cooled. The nickel powder was then separated to obtain nickel-alloyed steel fibers.
このニッケル合金化スチールファイバーを使用して、実
施例７と同様に成形原料の調整、成形および焼成・炭化
を行った。得られた炭素・スチール複合材の曲げ強度は
１９８０ｋｇ／ｃｍ” であった。Using this nickel alloyed steel fiber, preparation of a forming raw material, forming, and firing/carbonization were performed in the same manner as in Example 7. The bending strength of the carbon/steel composite material obtained was 1980 kg/cm''.
発明の効果
上記の実施例からも明らかなごとく、この発明の炭素・
金属複合材は、優れた強度特性、特に曲げ強度と耐魔耗
性とを備え、かつ電気比抵抗が低く、安定したスパーク
特性が得られる、パンタグラフ摺板に極めて好適である
。Effects of the invention As is clear from the above examples, the carbon and
Metal composite materials are extremely suitable for pantograph sliding plates because they have excellent strength properties, especially bending strength and wear resistance, low electrical resistivity, and stable spark characteristics.
また、その製造方法としても、金属繊維のめっき処理等
被覆処理工程が増えるだけであるため、製造コストが大
幅に高くつくことはなく、比較的安価に高品質の炭素・
金属複合材を提供できる。In addition, since the manufacturing method only requires an additional coating process such as metal fiber plating, the manufacturing cost does not increase significantly, and high-quality carbon and carbon fibers can be produced at a relatively low cost.
We can provide metal composites.
Claims (1)
材において、該金属繊維の一部または全部が表層に異種
材料が被覆および／または合金化されたものであること
を特徴とする炭素・金属複合材。 ２ 請求項１記載の金属繊維表層への被覆がめっき処理であ
ることを特徴とする炭素・金属複合材。 ３ 炭素質マトリックス中に金属繊維を含む炭素・金属複合
材において、マトリックス中に該金属繊維に加えて炭化
物生成傾向がこれと同等もしくはこれより小さい異種金
属粉末を含有することを特徴とする炭素・金属複合材。 ４ 炭素質マトリックス中に金属繊維を含む炭素・金属複合
材において、該金属繊維の一部または全部が表層に異種
材料が被覆および／または合金化されたものであり、さ
らに炭化物生成傾向が該金属繊維と同等もしくはこれよ
り小さい異種金属の粉末を含有したことを特徴とする炭
素・金属複合材。 ５ 請求項１、２および４記載の異種材料が、炭化物生成傾
向が該金属繊維と同等もしくはこれより小さい材料であ
ることを特徴とする炭素・金属複合材。 ６ 請求項１〜５記載の異種材料または異種金属が銅、ニッ
ケル、アルミニウムおよびコバルトの少なくとも１種で
あることを特徴とする炭素・金属複合材。 ７ 炭素質マトリックス中に金属繊維を含む炭素・金属複合
材の製造方法において、金属繊維をめっき処理するか、
金属繊維を炭化物生成傾向がこれと同等もしくはこれよ
り小さい異種金属粉末と混合後、該金属繊維の融点以下
の温度で熱処理により合金化したものを複合材と含有さ
れる金属繊維の一部または全部として炭素材料と混合・
成形・焼成することを特徴とする炭素・金属複合材の製
造方法。 ８ 炭素質マトリックス中に金属繊維を含む炭素・金属複合
材の製造方法において、金属繊維の一部または全部をめ
っき処理後炭素材原料と混合・成形・焼成することによ
り金属繊維を合金化することを特徴とする炭素・金属複
合材の製造方法。 ９ 炭素質マトリックス中に金属繊維を含む炭素・金属複合
材において、マトリックス中に該金属繊維に加えて炭化
物生成傾向がこれと同等もしくはこれより小さい異種金
属粉末を混合し、成形・焼成することにより金属繊維を
合金化することを特徴とする炭素・金属複合材の製造方
法。 １０ 炭素質マトリックス中に金属繊維を含む炭素・金属複合
材の製造方法において、金属繊維の合金化方法が請求項
７〜９記載の組合せであることを特徴とする炭素・金属
複合材の製造方法。[Scope of Claims] 1. In a carbon-metal composite material containing metal fibers in a carbonaceous matrix, some or all of the metal fibers are coated and/or alloyed with a different material on the surface layer. Characteristic carbon/metal composite material. 2. A carbon-metal composite material, wherein the metal fiber surface layer according to claim 1 is coated with a plating treatment. 3. A carbon-metal composite material containing metal fibers in a carbonaceous matrix, characterized in that the matrix contains, in addition to the metal fibers, a dissimilar metal powder with a tendency to form carbides equal to or smaller than that of the metal fibers. Metal composite. 4. A carbon-metal composite material containing metal fibers in a carbonaceous matrix, in which some or all of the metal fibers are coated and/or alloyed with a different material on the surface layer, and the carbide formation tendency is higher than that of the metal. A carbon-metal composite material characterized by containing dissimilar metal powder that is equal to or smaller than fibers. 5. A carbon-metal composite material, wherein the dissimilar material according to claim 1, 2, or 4 is a material whose carbide formation tendency is equal to or smaller than that of the metal fiber. 6. A carbon-metal composite material, wherein the dissimilar material or dissimilar metal according to claims 1 to 5 is at least one of copper, nickel, aluminum, and cobalt. 7 In the method for manufacturing a carbon-metal composite material containing metal fibers in a carbonaceous matrix, the metal fibers are plated or
A metal fiber is mixed with a dissimilar metal powder having a similar or smaller tendency to form carbides, and then alloyed by heat treatment at a temperature below the melting point of the metal fiber, resulting in a composite material and some or all of the metal fibers contained. Mixed with carbon material as
A method for producing a carbon/metal composite material, which is characterized by forming and firing. 8. In a method for manufacturing a carbon-metal composite material containing metal fibers in a carbonaceous matrix, alloying the metal fibers by plating some or all of the metal fibers and then mixing, forming, and firing the metal fibers with a carbon material raw material. A method for producing a carbon-metal composite material characterized by: 9 In a carbon-metal composite material containing metal fibers in a carbonaceous matrix, in addition to the metal fibers, a dissimilar metal powder with a tendency to generate carbides is mixed with the metal fibers in the matrix, and the mixture is molded and fired. A method for producing a carbon-metal composite material, which comprises alloying metal fibers. 10. A method for producing a carbon-metal composite material containing metal fibers in a carbonaceous matrix, wherein the method for alloying the metal fibers is a combination according to claims 7 to 9. .
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2096050A JPH0794346B2 (en) | 1989-04-12 | 1990-04-10 | Carbon-metal composite material and manufacturing method thereof |
Applications Claiming Priority (9)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP9384289 | 1989-04-12 | ||
| JP1-93842 | 1989-04-12 | ||
| JP1-162892 | 1989-06-26 | ||
| JP16289389 | 1989-06-26 | ||
| JP1-162893 | 1989-06-26 | ||
| JP16289289 | 1989-06-26 | ||
| JP1-209771 | 1989-08-14 | ||
| JP20977189 | 1989-08-14 | ||
| JP2096050A JPH0794346B2 (en) | 1989-04-12 | 1990-04-10 | Carbon-metal composite material and manufacturing method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH03164471A true JPH03164471A (en) | 1991-07-16 |
| JPH0794346B2 JPH0794346B2 (en) | 1995-10-11 |
Family
ID=27525667
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2096050A Expired - Lifetime JPH0794346B2 (en) | 1989-04-12 | 1990-04-10 | Carbon-metal composite material and manufacturing method thereof |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0794346B2 (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN110436924A (en) * | 2019-08-30 | 2019-11-12 | 中国科学院山西煤炭化学研究所 | A kind of high-speed train pantograph leaching copper carbon slide plate material and preparation method thereof |
| CN115921851A (en) * | 2022-12-14 | 2023-04-07 | 华南理工大学 | Semi-metal carbon sliding plate material for pantograph of vehicle and preparation method thereof |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH01157464A (en) * | 1987-12-14 | 1989-06-20 | Nippon Steel Corp | Carbon material for sliding current collection and production thereof |
-
1990
- 1990-04-10 JP JP2096050A patent/JPH0794346B2/en not_active Expired - Lifetime
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH01157464A (en) * | 1987-12-14 | 1989-06-20 | Nippon Steel Corp | Carbon material for sliding current collection and production thereof |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN110436924A (en) * | 2019-08-30 | 2019-11-12 | 中国科学院山西煤炭化学研究所 | A kind of high-speed train pantograph leaching copper carbon slide plate material and preparation method thereof |
| CN115921851A (en) * | 2022-12-14 | 2023-04-07 | 华南理工大学 | Semi-metal carbon sliding plate material for pantograph of vehicle and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0794346B2 (en) | 1995-10-11 |
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