JPH02247362A - Composite reinforced alloy and metallic fiber - Google Patents
Composite reinforced alloy and metallic fiberInfo
- Publication number
- JPH02247362A JPH02247362A JP6896989A JP6896989A JPH02247362A JP H02247362 A JPH02247362 A JP H02247362A JP 6896989 A JP6896989 A JP 6896989A JP 6896989 A JP6896989 A JP 6896989A JP H02247362 A JPH02247362 A JP H02247362A
- Authority
- JP
- Japan
- Prior art keywords
- metal
- alloy
- composite
- brittlement
- intergranular
- 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.)
- Pending
Links
- 239000002131 composite material Substances 0.000 title claims abstract description 40
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 38
- 239000000956 alloy Substances 0.000 title claims abstract description 38
- 229920000914 Metallic fiber Polymers 0.000 title abstract 4
- 239000002184 metal Substances 0.000 claims abstract description 72
- 229910052751 metal Inorganic materials 0.000 claims abstract description 72
- 239000000835 fiber Substances 0.000 claims abstract description 35
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 27
- 238000002844 melting Methods 0.000 claims abstract description 22
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 21
- 230000008018 melting Effects 0.000 claims abstract description 20
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 17
- 238000004519 manufacturing process Methods 0.000 claims abstract description 12
- 229910052802 copper Inorganic materials 0.000 claims abstract description 11
- 238000005266 casting Methods 0.000 claims abstract description 8
- 229910052709 silver Inorganic materials 0.000 claims abstract description 5
- 239000011261 inert gas Substances 0.000 claims abstract description 3
- 239000011159 matrix material Substances 0.000 claims description 17
- 150000002739 metals Chemical class 0.000 claims description 13
- 229910001111 Fine metal Inorganic materials 0.000 claims 1
- 239000013078 crystal Substances 0.000 abstract description 5
- 238000002425 crystallisation Methods 0.000 abstract description 4
- 230000008025 crystallization Effects 0.000 abstract description 4
- 229910052737 gold Inorganic materials 0.000 abstract description 2
- 238000000034 method Methods 0.000 description 14
- 239000010949 copper Substances 0.000 description 11
- 239000000463 material Substances 0.000 description 7
- 238000005530 etching Methods 0.000 description 6
- 239000012071 phase Substances 0.000 description 6
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 5
- 229910000599 Cr alloy Inorganic materials 0.000 description 5
- 238000005260 corrosion Methods 0.000 description 4
- 230000007797 corrosion Effects 0.000 description 4
- 238000005482 strain hardening Methods 0.000 description 4
- 229910001182 Mo alloy Inorganic materials 0.000 description 3
- 210000001787 dendrite Anatomy 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 238000007711 solidification Methods 0.000 description 3
- 230000008023 solidification Effects 0.000 description 3
- 229910017813 Cu—Cr Inorganic materials 0.000 description 2
- 229910021578 Iron(III) chloride Inorganic materials 0.000 description 2
- -1 Mo and W Chemical class 0.000 description 2
- 238000009835 boiling Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 230000005496 eutectics Effects 0.000 description 2
- 239000012535 impurity Substances 0.000 description 2
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 2
- RBTARNINKXHZNM-UHFFFAOYSA-K iron trichloride Chemical compound Cl[Fe](Cl)Cl RBTARNINKXHZNM-UHFFFAOYSA-K 0.000 description 2
- 239000002245 particle Substances 0.000 description 2
- 229910052702 rhenium Inorganic materials 0.000 description 2
- 238000001878 scanning electron micrograph Methods 0.000 description 2
- 239000007858 starting material Substances 0.000 description 2
- 238000005491 wire drawing Methods 0.000 description 2
- 229910000881 Cu alloy Inorganic materials 0.000 description 1
- 229910017827 Cu—Fe Inorganic materials 0.000 description 1
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- 229910000691 Re alloy Inorganic materials 0.000 description 1
- 241000854711 Shinkai Species 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- 229910002056 binary alloy Inorganic materials 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 238000013329 compounding Methods 0.000 description 1
- 238000004090 dissolution Methods 0.000 description 1
- 238000011978 dissolution method Methods 0.000 description 1
- 239000004744 fabric Substances 0.000 description 1
- 229910052739 hydrogen Inorganic materials 0.000 description 1
- 239000001257 hydrogen Substances 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- FBAFATDZDUQKNH-UHFFFAOYSA-M iron chloride Chemical compound [Cl-].[Fe] FBAFATDZDUQKNH-UHFFFAOYSA-M 0.000 description 1
- 239000007791 liquid phase Substances 0.000 description 1
- 239000000155 melt Substances 0.000 description 1
- 239000002923 metal particle Substances 0.000 description 1
- 238000003672 processing method Methods 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 239000012779 reinforcing material Substances 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
Abstract
Description
【発明の詳細な説明】
（技術分野）
本発明は、Ｖｌａ金属（Ｃｒ、Ｍｏ、Ｗ）等の粒界が脆
くて加工が難しい金属と延性に富む母相金属との２和合
金を塑性加工し、粒界脆性金属の微細繊維で複合強化し
てなる合金と、これより取り出すことが可能な粒界脆性
金属微細繊維に関するものである。さらに詳しくは、こ
の発明は、単結晶的な粒界脆性金属相を延性に富む母相
金属中に溶解鋳造晶出により均一に分散した２相合金を
冷間、温間、もしくは熱間加工することにより、粒界脆
性金属相を繊維径１０μｍ以下に加工して強化した複合
合金と、この複合強化合金より母相合金を選択的にエツ
チング等により溶かして形成した粒界脆性金属の微細繊
維に関するものである。Detailed Description of the Invention (Technical Field) The present invention deals with plastic processing of a binary alloy of a metal with brittle grain boundaries and difficult to process, such as Vla metal (Cr, Mo, W), and a matrix metal with high ductility. The present invention also relates to an alloy compositely reinforced with grain-boundary brittle metal fine fibers and grain-boundary brittle metal fine fibers that can be extracted from the alloy. More specifically, the present invention involves cold, warm, or hot working a two-phase alloy in which a single-crystal grain-boundary brittle metal phase is uniformly dispersed in a ductile parent metal by melting, casting, and crystallization. Accordingly, the present invention relates to a composite alloy strengthened by processing a grain boundary brittle metal phase to a fiber diameter of 10 μm or less, and a fine fiber of a grain boundary brittle metal formed by selectively melting a matrix alloy from this composite reinforced alloy by etching or the like. It is something.
（従来の技術とその課題）
Ｃｒ、Ｍｏ、ＷのＶｉａ金属やその他の高融点金属、も
しくはその合金は化学的に安定で、高温耐食性に優れ、
しかも高強度なものとして注目されているが、これら金
属の多くのものは、結晶粒界が脆いという欠点があるた
め、その特徴を生かした材料として充分に使いきれてい
ないのが実状である。(Prior art and its problems) Via metals such as Cr, Mo, and W and other high-melting point metals or their alloys are chemically stable and have excellent high-temperature corrosion resistance.
Moreover, although they are attracting attention for their high strength, many of these metals have the disadvantage of brittle grain boundaries, so in reality they cannot be used to the fullest as materials that take advantage of this feature.
このような粒界が脆い金属に関しては、多結晶とせずに
単結晶材料として使用することや、繊維状金属として他
の金属と複合化することなどが考えられてきている。Regarding such metals with brittle grain boundaries, it has been considered to use them as single crystal materials instead of polycrystalline materials, or to combine them with other metals as fibrous metals.
しかしながら、単結晶材料についてはその製造と使用に
多くの制約があり、コスト的にも高いものとなる。また
現実的な展開が期待される複合材料についても、これら
の粒界脆性金属を繊維として製造する場合、通常は多結
晶インゴットを出発素材とする限り、粒界への微量不純
物元素の偏析のために加工途中で粒界で割れ易く、その
ため特に冷間で加工することは極めて困難である。一方
、Ｖｉａ金属のＭｏ、Ｗでは、熱間、温間加工を行えば
、結晶粒界組織を壊することができ、線径が０、１ｃｍ
程度まで伸線が可能である。しかし、熱間、温間加工を
行う必要があるため製造コストが増加し、しかも熱間、
温間加工によって６０，１簡より細い径の４１１雌を得
るのは極めて難しい、さらに、Ｃｒに関しては熱間、温
間加工することも難しく、細線を得るのが極めて困難で
ある。また、Ｃｒ。However, single-crystal materials have many restrictions on their manufacture and use, and are also expensive. In addition, regarding composite materials that are expected to be used in practical applications, when these grain-boundary brittle metals are produced as fibers, as long as polycrystalline ingots are normally used as the starting material, there is a risk of segregation of trace impurity elements at the grain boundaries. It is easy to crack at grain boundaries during processing, and therefore it is extremely difficult to process, especially in cold processing. On the other hand, in Via metals such as Mo and W, the grain boundary structure can be broken by hot and warm processing, and the wire diameter can be reduced to 0.1 cm.
Wire drawing is possible to a certain extent. However, the manufacturing cost increases due to the need to perform hot and warm processing.
It is extremely difficult to obtain a 411 female wire with a diameter smaller than 60.1 by warm working.Furthermore, it is also difficult to perform hot working with Cr, making it extremely difficult to obtain a fine wire. Also, Cr.
Ｍｏ、Ｗに対し水素雰囲気中で帯溶融精製などにより高
純度化を行うとその加工性が幾らか改善されることが知
られているが、中間焼鈍なしに冷間加工でインゴットか
ら細線を直接得るのは極めて困難である。It is known that the processability of Mo and W can be improved to some extent by purifying Mo and W by band-melting refining in a hydrogen atmosphere. It is extremely difficult to obtain.
他方、粒界脆性金属の細線を利用した複合強化材料に関
しては、線径が０．１−０．５ ａｙａのＭｏあるいは
Ｗ細線を真空中において鋳くるんで溶融銅と複合化する
技術がすでに知られているが、複合前にＭｏ、Ｗ細線を
熱間加工して予め用意する必要があり、また、銅とＭｏ
、Ｗ４１１線との界面における空隙を小さくするため高
圧凝固鋳造法等を採用する必要がある。しかも、複合化
の際に１１００℃以上の高温になることからＭｏ、Ｗ４
１線の再結晶化ならびに脆化は避けられず、このように
して得られた複合体そのものをさらに冷間加工すること
も困難である。それゆえ、長尺の複合合金細線や薄板を
得るのは龍しい、Ｃｒに関しては熱間加工によってもそ
れ自身の繊維を得るのが難しく、溶融銅で鋳くるんだ複
合合金は現在も存在していない。On the other hand, regarding composite reinforcing materials using thin wires of grain-boundary brittle metal, there is already a known technology in which Mo or W thin wires with a wire diameter of 0.1-0.5 aya are cast in a vacuum and composited with molten copper. However, it is necessary to prepare the Mo and W fine wires by hot processing before combining them, and it is also necessary to prepare the Mo and W thin wires in advance.
In order to reduce the voids at the interface with the W411 wire, it is necessary to employ a high-pressure solidification casting method or the like. Moreover, since the temperature reaches 1100℃ or more during compounding, Mo, W4
One-line recrystallization and embrittlement are unavoidable, and it is also difficult to further cold-work the composite body obtained in this way. Therefore, it is difficult to obtain long composite alloy thin wires or thin plates.As for Cr, it is difficult to obtain its own fibers even through hot working, and composite alloys cast with molten copper do not even exist today. do not have.
なお、Ｃｕ−Ｃｒ複合合金に関しては、共晶組成で一方
向凝固してＣｒウィスカーが分散した接金銅合金が得ら
れることが報告されている。しかし、共晶組成が小さく
、Ｃｒウィスカーの体積率が僅か約１．６％のため、機
械的強度は母相の銅の強度とほとんど同じである。また
、一方向凝固を利用して長尺の細線や薄板を得るのは極
めて困難である。Regarding the Cu-Cr composite alloy, it has been reported that a welded copper alloy with eutectic composition and unidirectional solidification in which Cr whiskers are dispersed can be obtained. However, since the eutectic composition is small and the volume fraction of Cr whiskers is only about 1.6%, the mechanical strength is almost the same as that of the copper matrix. Furthermore, it is extremely difficult to obtain long thin wires or thin plates using unidirectional solidification.
２相合金を冷間加工して第２相の繊維を分散した複合合
金としては、Ｃｕ−Ｖ、Ｃｕ−Ｎｂ。Examples of composite alloys in which second phase fibers are dispersed by cold working a two-phase alloy include Cu-V and Cu-Nb.
Ｃｕ−Ｆｅ、Ｃｕ−（Ｆｅ、Ｃｒ）、Ｃｕ Ａｇ＋Ａ
ｇ Ｆｅが知られているが、いずれもその第２相がも
ともと良好な加工性を有しているものであり、Ｖｌａ金
属のような、潜在的に優れた機械的強度を有するが、粒
界が脆い金属で繊維強化された複合合金を、２相合金を
冷間加工することにより作製した報告はない。Cu-Fe, Cu-(Fe, Cr), Cu Ag+A
G-Fe is known, but all of them have good processability in their second phase, and like Vla metal, they have potentially excellent mechanical strength, but grain boundary There has been no report on fabricating a composite alloy fiber-reinforced with a brittle metal by cold working a two-phase alloy.
このように、Ｖｌａ金属等の粒界脆性金属については、
その特性と、繊維複合化の加工法の発展が期待されなが
らも、依然として解決しなければならない多くの課題を
かかえている。In this way, for grain boundary brittle metals such as Vla metal,
Although there are high expectations for the development of its properties and processing methods for fiber composites, there are still many issues that need to be resolved.
この発明は、以上の通りの事情に鑑みてなされたもので
あり、従来は実現できなかった粒界脆性金属の微細繊維
と、これにより複合強化した合金を提供することを目的
としている。The present invention has been made in view of the above circumstances, and aims to provide fine fibers of grain boundary brittle metal, which could not be achieved conventionally, and an alloy compositely strengthened by the fine fibers.
（課題を解決するための手段）
この発明は、上記の課題を解決するものとして、Ｖｌａ
金属（Ｃｒ、Ｍｏ、Ｗ）等の粒界脆性金属と延性に富む
母相金属との溶解鋳造晶出により形成した２相合金を塑
性加工して粒界脆性金属のａｔ細繊維を複合化してなる
複合強化合金とその製造方法、および、その合金母相金
属から粒界脆性金属のＦＲＭＡ繊維を取出してなる粒界
脆性金属の繊維とその製造方法をも提供する。(Means for Solving the Problems) This invention solves the above problems by
A two-phase alloy formed by melting, casting, and crystallization of a grain-boundary brittle metal such as metal (Cr, Mo, W) and a ductile matrix metal is plastically worked to composite the at-fine fibers of the grain-boundary brittle metal. The present invention also provides a composite reinforced alloy and a method for manufacturing the same, as well as fibers of a grain-boundary brittle metal obtained by extracting FRMA fibers of a grain-boundary brittle metal from a matrix metal of the alloy, and a method for manufacturing the same.
粒界脆性金属としては、たとえば、Ｃｒ、Ｍｏ。Examples of grain boundary brittle metals include Cr and Mo.
Ｗが単独で用いられてもよいし、あるいは、これらの成
分が２種以上含まれたＣｒ−Ｍｏ、Ｃｒ−Ｗ、 Ｍ ｏ
−Ｗ、 Ｃｒ−Ｍ ｏ−Ｗ等の合金であってもよい、こ
れに対応する母相金属にも特別の限定はないが、延性の
大きなきなＣｕ、Ａｇおよび／またはＡｕが好適なもの
として例示される。W may be used alone, or Cr-Mo, Cr-W, Mo containing two or more of these components
It may be an alloy such as -W, Cr-Mo-W, etc. There is no particular limitation on the corresponding matrix metal, but Cu, Ag and/or Au, which have high ductility, are preferred. Illustrated as.
Ｃｕ、Ａｇに添加されるＣｒ、Ｍｏ、Ｗあるいはそれら
の合金は、優れた複合合金の機械強度を得るためにｌａ
ｔ％以上、また、良好な冷間加工生を保持する上から５
０８ｔ％以下の範囲とし、Ａｕに添加されるＭｏ、Ｗあ
るいはそれらの合金も同様の理由でｆａｔ％以上、５０
ａｔ％以下の範囲に、さらに、Ａｕに添加されるＣｒ、
Ｃｒ−Ｍｏ。Cr, Mo, W or their alloys added to Cu, Ag are la
t% or more, and also maintains good cold workability.
For the same reason, Mo, W, or their alloys added to Au should be in the range of 0.8 t% or less, and the content should be 50 t% or less for the same reason.
Cr added to Au in a range of at% or less,
Cr-Mo.
Ｃｒ−Ｗの量は、Ｃｒを第２相として晶出させるために
２０ａｔ％以上、また、良好な冷間加工生を保持する上
から５０ａｔ％以下の範囲とするのが好ましい。The amount of Cr-W is preferably in the range of 20 at % or more in order to crystallize Cr as a second phase, and 50 at % or less in order to maintain good cold workability.
忍解鋳造晶出においては、粒界脆性金属が融点の高いＭ
ｏ、Ｗの場合には、母相金属の沸点を上昇させるために
１気圧以上の不活性ガス雰囲気中で溶解を行ってもよい
。In Shinkai casting crystallization, the grain boundary brittle metal has a high melting point.
In the case of O and W, dissolution may be performed in an inert gas atmosphere of 1 atm or more in order to raise the boiling point of the parent phase metal.
さらにまた、Ｃｒ、Ｍｏ、Ｗには繊維の冷間加工性を改
善するためにｌａｔ％以上のＲｅを添加してもよい、た
だし、Ｃｒ−Ｒｅ、Ｍｏ−Ｒｅ。Furthermore, lat% or more of Re may be added to Cr, Mo, and W in order to improve the cold workability of the fibers, however, Cr-Re and Mo-Re.
Ｗ −Ｒｅの金属間化合物を生成させないためには緋加
するＲｅ量は３７ａｔ％以下とするのが好ましい、なお
、Ｍｏ−Ｒｅは超電導特性の優れた合金線材であり、Ｍ
ｏ−Ｒｅ微細繊維が分散した複合合金線は超電導線材と
しても使用できる。In order to prevent the formation of intermetallic compounds of W-Re, the amount of Re added is preferably 37 at% or less.Moreover, Mo-Re is an alloy wire with excellent superconducting properties, and M
A composite alloy wire in which o-Re fine fibers are dispersed can also be used as a superconducting wire.
次に実施例を示してさらに詳しくこの発明について説明
する。もちろん、この発明は以下の実施例によって限定
されるものではない。Next, the present invention will be explained in more detail by showing examples. Of course, the invention is not limited to the following examples.
実施例１〜３
高純度Ｃｒ （９９，９９ｍａｓｓ％）と電解不純Ｃｒ
（９９，２＋１ａＳＳ％）の２種類のＣｒを原材料とし
てＣｕ−１０ａｔ％Ｃｒ、Ｃｕ−２０ａｔ％Ｃｒ合金を
各々０．５気圧Ａｒ雰囲気中で非消耗電極型アーク溶解
法により溶解した。添付した図面の第１図（ａ＞に示し
たように、Ｃｕ−２０ａｔ％Ｃｒ合金においては結晶方
位が揃った単結晶的なＣｒのデンドライトが融液から成
長し、−ｍに、Ｃｕマトリックス中に分散する。ついで
、これを溝ロールと線引きにより断面減少率（線径０．
６ａｍ）で９９，８％まで冷間伸線すると、原料Ｃｒの
組成及び純度に依らず、第１図（ｂ）に示したようにＣ
ｒデンドライトが加工変形し、厚さ０．２μｍ、幅４μ
ｍ以下のリボン状繊維となる。Examples 1 to 3 High purity Cr (99,99mass%) and electrolytic impurity Cr
Using two types of Cr (99,2+1aSS%) as raw materials, Cu-10at%Cr and Cu-20at%Cr alloys were each melted by a non-consumable electrode type arc melting method in an Ar atmosphere of 0.5 atm. As shown in Figure 1 (a) of the attached drawings, in the Cu-20at%Cr alloy, single-crystalline Cr dendrites with uniform crystal orientation grow from the melt, and -m, in the Cu matrix. Then, this is drawn with a groove roll to reduce the area reduction rate (wire diameter 0.
6 am) to 99.8%, regardless of the composition and purity of the raw Cr, as shown in Figure 1(b),
r dendrite is processed and deformed to a thickness of 0.2 μm and a width of 4 μm.
It becomes a ribbon-like fiber of less than m.
また、表１にはＣｕ−Ｃｒ複合線の引張り降伏強度と電
気抵抗値を示した。Ｃｕ線に比べて引っ張り強度が大幅
に上昇している。Further, Table 1 shows the tensile yield strength and electrical resistance value of the Cu-Cr composite wire. The tensile strength is significantly higher than that of Cu wire.
なお、得られた複合強化合金中に分散されたＣｒの繊維
は、母相金属のＣｕを第２塩化鉄でエツチングすること
により容易に抽出できた。Note that the Cr fibers dispersed in the obtained composite reinforced alloy could be easily extracted by etching the parent metal Cu with ferric chloride.
実施例４
Ｃｕ−ｆｌａｔ％ＭＯ合金を溶解することを試みた。Ｃ
ｕの沸点（２５６６℃、１気圧）がＭｏの融点（２６１
７℃、１気圧）より低いため、Ｃｕ −Ｍ ｏ合金液相
を得るのは通常の減圧下での非消耗電極型アーク溶解法
ではできなかった０次にＣｕの沸点を上昇させるために
１０気圧のＡｒ雰囲中で同じく非消耗電極型アーク溶解
法により溶解を試みたが、水冷銅ハースへの熱の逃げが
著しく、試料を一様に溶解できなかった。そこで高圧下
でさらに高温溶解が可能な方法として１０気圧のＡｒ雰
囲気中で消耗電極型アーク溶解法により溶解を行い、第
２図（ａ）に示したように、球状Ｍｏが鋼中に一様に分
散した組織が得られた。これを実施例１と同じように冷
間加工すると第２図（ｂ）に示したようにＭｏの繊維が
得られた。Example 4 An attempt was made to melt a Cu-flat% MO alloy. C
The boiling point of u (2566°C, 1 atm) is the melting point of Mo (261
7°C, 1 atm), the Cu-Mo alloy liquid phase could not be obtained using the normal non-consumable electrode type arc melting method under reduced pressure. Melting was attempted using the same non-consumable electrode type arc melting method in an Ar atmosphere at atmospheric pressure, but the loss of heat to the water-cooled copper hearth was significant and the sample could not be melted uniformly. Therefore, as a method that allows melting at a higher temperature under high pressure, melting was performed using the consumable electrode type arc melting method in an Ar atmosphere of 10 atm, and as shown in Figure 2 (a), spherical Mo was uniformly distributed in the steel. A dispersed tissue was obtained. When this was cold worked in the same manner as in Example 1, Mo fibers were obtained as shown in FIG. 2(b).
実施例５
Ｃｕ−１０ａｔ％（Ｃｒ−５ａｔ％Ｍｏ）、Ａｕ−１０
ａｔ％（Ｍｏ−５８ｔ％Ｃｒ）合金を、１０気圧のＡｒ
雰囲気中で消耗電極型溶解法により溶解した。実施例１
と同様にＣｕ、Ａｕ母相中にデンドライト状のＣｒ−Ｍ
ｏ、Ｍｏ−Ｃｒ合金粒子がそれぞれ一様に分散した組織
が得られた。これを溝ロールと線引きにより断面減少率
（線径が０．６ｍ）で９９．８％まで冷間伸線すると、
実施例１と同様にＣｒ−Ｍｏ、Ｍｏ−Ｃｒ合金デンドラ
イトが加工変形し、厚さ０．２μｍ、幅４μｍ以下のリ
ボン状Ｃｒ−Ｍｏ、Ｍｏ−Ｃｒ繊維となった。Example 5 Cu-10at% (Cr-5at%Mo), Au-10
at% (Mo-58t%Cr) alloy was heated with Ar at 10 atm.
It was dissolved by a consumable electrode type dissolution method in an atmosphere. Example 1
Similarly, there is dendrite-like Cr-M in the Cu and Au matrix.
A structure in which Mo-Cr alloy particles were uniformly dispersed was obtained. When this is cold drawn to a cross-section reduction rate of 99.8% (wire diameter is 0.6 m) using a grooved roll and wire drawing,
As in Example 1, the Cr-Mo and Mo-Cr alloy dendrites were processed and deformed to become ribbon-like Cr-Mo and Mo-Cr fibers with a thickness of 0.2 μm and a width of 4 μm or less.
実施例６
Ｃｕ−１０８ｔ％（Ｍｏ−３５ａｔ％Ｒｅ）合金を、１
０気圧のＡｒ雰囲気中で消耗電極型溶解法により溶解し
た。実施例２と同様に球状のＭｏ−Ｒｅ合金粒子が一様
に分散した組織が得られた。これを径が０，５噛の細線
に加工して超電導特性を測定し、１２にの温度を得た。Example 6 Cu-108t% (Mo-35at%Re) alloy was
It was melted by a consumable electrode type melting method in an Ar atmosphere at 0 atm. As in Example 2, a structure in which spherical Mo-Re alloy particles were uniformly dispersed was obtained. This was processed into a thin wire with a diameter of 0.5 degrees, and its superconducting properties were measured, and a temperature of 12 degrees was obtained.
（発明の効果）
この発明により、次のような特長を有する繊維複合強化
合金が実現される。(Effects of the Invention) According to the present invention, a fiber composite reinforced alloy having the following features is realized.
（１） 粒界脆性金属の本来有している優れた機械的強
度が複合材料の強度向上に反映され、きわめて機械的強
度の優れた複合材料となる。(1) The inherently excellent mechanical strength of grain boundary brittle metals is reflected in the improved strength of the composite material, resulting in a composite material with extremely excellent mechanical strength.
＜２） Ｃｒ、Ｍｏ、Ｗは高融点金属で化学的に安定
な金属であることから、高温で耐食性に優れた高強度複
合合金が得られる。<2) Since Cr, Mo, and W are metals with high melting points and are chemically stable, a high-strength composite alloy with excellent corrosion resistance at high temperatures can be obtained.
（３） お互いの固溶度が極めて小さな２相合金を出発
材料としていることから電気伝導度が小さい銅を母相金
属とした場合、強磁界の発生を可能とする高強度高電気
伝導度複合材料が製造できる。(3) A high-strength, high-electrical-conductivity composite that can generate a strong magnetic field when the parent metal is copper, which has low electrical conductivity because the starting material is a two-phase alloy with extremely low solid solubility in each other. Materials can be manufactured.
（４） ２相合金の溶解鋳造によって粒界脆性金属粒子
を母相中に一様に分散させることができるので、その後
冷間加工して得られる黴、ｉｎ＋ｍ維複合合金の機械的
強度、電気伝導度、耐食性等の物理化学的性質は極めて
一様である。(4) By melting and casting a two-phase alloy, the grain boundary brittle metal particles can be uniformly dispersed in the matrix, so the mechanical strength and electrical properties of the mold, in+m fiber composite alloy obtained by subsequent cold working can be improved. Physical and chemical properties such as conductivity and corrosion resistance are extremely uniform.
（５） この発明の方法においては初めから複合化され
た合金を冷間加工するだけであるので、従来の様な別途
脆性金属を加工しその後複合化する工程が省略され、そ
の製造コストが著しく節減される。(5) In the method of the present invention, since the composite alloy is simply cold-worked from the beginning, the conventional process of separately processing brittle metal and then composite is omitted, and the manufacturing cost is significantly reduced. Saved.
（６） 複合材として塑性加工できるので、細線や薄板
等の任意の形状の材料が容易に得られる。(6) Since it can be plastically worked as a composite material, materials of arbitrary shapes such as thin wires and thin plates can be easily obtained.
（７） 複合合金の加工度を制御することによって分散
している繊維の間隔を容易に制御でき、その間隔をきわ
めて狭くすることによって複合剤から予測される値以上
のｆｉ械的強度を実現できる。(7) By controlling the degree of processing of the composite alloy, the spacing between the dispersed fibers can be easily controlled, and by making the spacing extremely narrow, it is possible to achieve fi mechanical strength that exceeds the value expected from the composite agent. .
（８） 母相を優先的にエツチングで溶かしたり、また
は、融点の差を利用して母相のみを溶かすことにより、
粒界脆性金属の繊維だけを取り出すことができる。この
方法は、粒界脆性金属の繊維の製造法としても注目され
る。従来製造が不可能だった粒界脆性金属繊維が得られ
るだけでなく、しかも冷間加工により容易に得られるこ
とからその製造コストも低い、これらの繊維は先端技術
素材としての活用が可能である６例えば高温耐食性金属
繊維布等のこれまでにない新しい応用が考えられるなど
、その経済的波及効果は大きい。(8) By preferentially dissolving the matrix by etching, or by utilizing the difference in melting points to melt only the matrix,
Only fibers of grain boundary brittle metal can be extracted. This method is also attracting attention as a method for producing grain boundary brittle metal fibers. Not only can we obtain grain-boundary brittle metal fibers that were previously impossible to manufacture, but they can also be easily obtained through cold working, so the manufacturing cost is low. These fibers can be used as cutting-edge technology materials. 6.The economic ripple effect is large, for example, new applications such as high-temperature corrosion-resistant metal fiber cloth can be considered.
第１図（ａ）＜ｂ）は、Ｃｕ−２０ａｔ％Ｃｒ合金の溶
解ｍ織と、これを加工した後の組織を、それぞれ、研磨
断面を第２塩化鉄エツチング液で腐食した後の金属組織
として示した図面代用の走査電子顕微鏡写真である。
第２図（ａ）（ｂ）は、Ｃｕ−１１ａｔ％Ｍｏ合金の溶
解組織と、これを加工した後の組織を、それぞれ、研磨
断面を第２塩化鉄エツチング液で腐食した後の金属組織
として示した図面代用の走査電子顕微鏡写真である。Figure 1 (a) < b) shows the melted microstructure of Cu-20at%Cr alloy and the structure after processing, respectively, and the metal structure after etching the polished cross section with iron chloride etching solution. This is a scanning electron micrograph shown as a drawing. Figures 2 (a) and (b) show the dissolved structure of the Cu-11at%Mo alloy and the structure after processing, respectively, and the metal structure after the polished cross section was etched with a ferric chloride etching solution. This is a scanning electron micrograph used as a substitute for the drawing shown.
Claims (12)
晶出させて形成した２相合金を塑性加工して微細金属繊
維を複合化してなることを特徴とする複合強化合金。(1) A composite reinforced alloy characterized in that it is made by plastically working a two-phase alloy formed by melting, casting, and crystallizing a grain-boundary brittle metal and a ductile matrix metal to form a composite with fine metal fibers.
求項（１）記載の複合強化合金。(2) The composite reinforced alloy according to claim (1), which is obtained by hot or warm plastic working of a two-phase alloy.
る請求項（１）記載の複合強化合金。(3) The composite reinforced alloy according to claim (1), wherein Cr, Mo and/or W are grain boundary brittle metals.
る請求項（３）記載の複合強化合金。(4) The composite reinforced alloy according to claim (3), wherein Re is added to Cr, Mo and/or W.
請求項（１）記載の複合強化合金。(5) The composite reinforced alloy according to claim (1), wherein the matrix metal is Cu, Ag and/or Au.
合金の製造方法。(6) A method for producing a composite reinforced alloy characterized by the composite according to claim (1).
不活性ガス雰囲気で溶解する請求項（６）記載の複合強
化合金の製造方法。(7) The method for producing a composite reinforced alloy according to claim (6), wherein Mo or W is a grain boundary brittle metal and is melted in an inert gas atmosphere of 1 atmosphere or more.
晶出させて形成した２相合金を塑性加工して得られた請
求項（１）記載の繊維複合強化合金より母相金属を取除
いてなることを特徴とする粒界脆性金属繊維。(8) A matrix metal obtained by plastic working a two-phase alloy formed by melting, casting and crystallizing a grain boundary brittle metal and a ductile matrix metal. A grain boundary brittle metal fiber characterized in that it is obtained by removing grain boundary brittle metal fibers.
る粒界脆性金属繊維の製造方法。(9) A method for producing grain boundary brittle metal fibers, characterized by removing the matrix metal according to claim (8).
してなる請求項（８）記載の金属繊維。(10) The metal fiber according to claim (8), comprising Cr, Mo and/or W as the grain boundary brittle metal.
なる請求項（１０）記載の金属繊維。(11) The metal fiber according to claim (10), wherein Re is added to Cr, Mo and/or W.
てなる請求項（８）記載の金属繊維。(12) The metal fiber according to claim (8), comprising Cu, Ag and/or Au as a matrix metal.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP6896989A JPH02247362A (en) | 1989-03-20 | 1989-03-20 | Composite reinforced alloy and metallic fiber |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP6896989A JPH02247362A (en) | 1989-03-20 | 1989-03-20 | Composite reinforced alloy and metallic fiber |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH02247362A true JPH02247362A (en) | 1990-10-03 |
Family
ID=13389013
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP6896989A Pending JPH02247362A (en) | 1989-03-20 | 1989-03-20 | Composite reinforced alloy and metallic fiber |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH02247362A (en) |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS49135819A (en) * | 1973-05-04 | 1974-12-27 | ||
| JPS5135603A (en) * | 1974-09-20 | 1976-03-26 | Hitachi Ltd | SENIKYOKAFUKUGOZAIRYO NO SOSEIKAKOHO |
| JPS62267050A (en) * | 1986-05-13 | 1987-11-19 | Fujikura Ltd | Production of in-situ rod for fiber dispersion type superconducting wire |
| JPS6353225A (en) * | 1987-03-31 | 1988-03-07 | Honda Motor Co Ltd | Cylinder sleeve for engine |
-
1989
- 1989-03-20 JP JP6896989A patent/JPH02247362A/en active Pending
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS49135819A (en) * | 1973-05-04 | 1974-12-27 | ||
| JPS5135603A (en) * | 1974-09-20 | 1976-03-26 | Hitachi Ltd | SENIKYOKAFUKUGOZAIRYO NO SOSEIKAKOHO |
| JPS62267050A (en) * | 1986-05-13 | 1987-11-19 | Fujikura Ltd | Production of in-situ rod for fiber dispersion type superconducting wire |
| JPS6353225A (en) * | 1987-03-31 | 1988-03-07 | Honda Motor Co Ltd | Cylinder sleeve for engine |
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