JPH07278695A - Production of particle dispersion type alloy - Google Patents
Production of particle dispersion type alloyInfo
- Publication number
- JPH07278695A JPH07278695A JP6098173A JP9817394A JPH07278695A JP H07278695 A JPH07278695 A JP H07278695A JP 6098173 A JP6098173 A JP 6098173A JP 9817394 A JP9817394 A JP 9817394A JP H07278695 A JPH07278695 A JP H07278695A
- Authority
- JP
- Japan
- Prior art keywords
- powder
- alloy powder
- alloy
- dispersed
- particles
- 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.)
- Withdrawn
Links
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 156
- 239000000956 alloy Substances 0.000 title claims abstract description 156
- 239000002245 particle Substances 0.000 title claims abstract description 82
- 239000006185 dispersion Substances 0.000 title claims abstract description 45
- 238000004519 manufacturing process Methods 0.000 title claims description 23
- 239000000843 powder Substances 0.000 claims abstract description 151
- 239000000203 mixture Substances 0.000 claims abstract description 34
- 238000007711 solidification Methods 0.000 claims abstract description 10
- 230000008023 solidification Effects 0.000 claims abstract description 10
- 238000000034 method Methods 0.000 claims description 29
- 150000001875 compounds Chemical class 0.000 claims description 20
- 238000002156 mixing Methods 0.000 claims description 10
- 239000002184 metal Substances 0.000 claims description 9
- 229910052751 metal Inorganic materials 0.000 claims description 9
- 238000005551 mechanical alloying Methods 0.000 claims description 6
- 229910052758 niobium Inorganic materials 0.000 abstract description 7
- 229910001209 Low-carbon steel Inorganic materials 0.000 abstract description 3
- 239000002775 capsule Substances 0.000 abstract description 3
- 238000012856 packing Methods 0.000 abstract 1
- 239000000463 material Substances 0.000 description 24
- 238000005275 alloying Methods 0.000 description 9
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 description 8
- 230000000052 comparative effect Effects 0.000 description 8
- 238000005260 corrosion Methods 0.000 description 7
- 230000007797 corrosion Effects 0.000 description 7
- 238000001513 hot isostatic pressing Methods 0.000 description 7
- 229910052750 molybdenum Inorganic materials 0.000 description 7
- 229910052759 nickel Inorganic materials 0.000 description 7
- 229910052802 copper Inorganic materials 0.000 description 6
- 229910052742 iron Inorganic materials 0.000 description 6
- 229910052710 silicon Inorganic materials 0.000 description 6
- 229910052721 tungsten Inorganic materials 0.000 description 6
- 229910052796 boron Inorganic materials 0.000 description 5
- 229910052799 carbon Inorganic materials 0.000 description 5
- 150000001247 metal acetylides Chemical class 0.000 description 5
- 229910052719 titanium Inorganic materials 0.000 description 5
- 229910052748 manganese Inorganic materials 0.000 description 4
- 229910052804 chromium Inorganic materials 0.000 description 3
- 238000005336 cracking Methods 0.000 description 3
- 238000010586 diagram Methods 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 238000010438 heat treatment Methods 0.000 description 3
- 229910052749 magnesium Inorganic materials 0.000 description 3
- 150000004767 nitrides Chemical class 0.000 description 3
- 239000002994 raw material Substances 0.000 description 3
- 238000001953 recrystallisation Methods 0.000 description 3
- 238000005096 rolling process Methods 0.000 description 3
- 238000005299 abrasion Methods 0.000 description 2
- 229910052782 aluminium Inorganic materials 0.000 description 2
- 238000006243 chemical reaction Methods 0.000 description 2
- 230000002542 deteriorative effect Effects 0.000 description 2
- -1 for example Substances 0.000 description 2
- 229910052735 hafnium Inorganic materials 0.000 description 2
- 238000001192 hot extrusion Methods 0.000 description 2
- 230000006698 induction Effects 0.000 description 2
- 238000011835 investigation Methods 0.000 description 2
- 239000007788 liquid Substances 0.000 description 2
- 230000001050 lubricating effect Effects 0.000 description 2
- 238000000465 moulding Methods 0.000 description 2
- 229910001175 oxide dispersion-strengthened alloy Inorganic materials 0.000 description 2
- 229910021332 silicide Inorganic materials 0.000 description 2
- 239000011863 silicon-based powder Substances 0.000 description 2
- 239000002904 solvent Substances 0.000 description 2
- 238000005728 strengthening Methods 0.000 description 2
- 229910052715 tantalum Inorganic materials 0.000 description 2
- 229910052720 vanadium Inorganic materials 0.000 description 2
- 229910052727 yttrium Inorganic materials 0.000 description 2
- 229910052725 zinc Inorganic materials 0.000 description 2
- 229910052726 zirconium Inorganic materials 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 206010010144 Completed suicide Diseases 0.000 description 1
- 229910019018 Mg 2 Si Inorganic materials 0.000 description 1
- 229910016006 MoSi Inorganic materials 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- 238000005054 agglomeration Methods 0.000 description 1
- 230000002776 aggregation Effects 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
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 239000010953 base metal Substances 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 229910052791 calcium Inorganic materials 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 238000005097 cold rolling Methods 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
- 238000013329 compounding Methods 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 230000001747 exhibiting effect Effects 0.000 description 1
- 230000003631 expected effect Effects 0.000 description 1
- 239000010419 fine particle Substances 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 230000013011 mating Effects 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 239000011812 mixed powder Substances 0.000 description 1
- 238000010137 moulding (plastic) Methods 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 230000004580 weight loss Effects 0.000 description 1
Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は粒子分散型合金の製造方
法に関し、更に詳しくは、エンジン部材、ボイラー部材
など高温で使用される高温強度、クリープ特性に優れ、
更に加工性が要求される粒子分散型Ｆe基、Ｎi基、Ａl
基合金の製造方法、或いはプラスチック成形機シリンダ
用の耐摩耗、耐食性が要求される粒子分散型Ｎi基合金
の製造方法に好適な粒子分散型合金の製造方法に関す
る。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for producing a particle-dispersed alloy, and more specifically, it has excellent high-temperature strength and creep characteristics for use at high temperatures such as engine members and boiler members.
Particle-dispersed Fe group, Ni group, Al
The present invention relates to a method for producing a base alloy or a method for producing a particle-dispersed alloy suitable for a method for producing a particle-dispersed Ni-based alloy that requires wear resistance and corrosion resistance for a plastic molding machine cylinder.
【０００２】[0002]
【従来の技術】粒子分散型合金は、種々の方法で製造さ
れている。なかでも、Ｎi基合金、Ｆe基合金などの合金
種では、メカニカルアロイング法(以下、「ＭＡ法」と
呼ぶ)で粒子分散型粉末を製造し、この粒子分散型粉末
を成形固化処理して得られる粒子分散型粉末合金は、高
温強度、耐クリープ特性に優れている。2. Description of the Related Art Particle-dispersed alloys are manufactured by various methods. Among them, for alloy types such as Ni-based alloys and Fe-based alloys, a particle-dispersed powder is manufactured by a mechanical alloying method (hereinafter referred to as “MA method”), and the particle-dispersed powder is molded and solidified. The obtained particle dispersion type powder alloy is excellent in high temperature strength and creep resistance.
【０００３】このＭＡ法とは、一般に、母合金粉末に、
所定の量の微細な分散用粒子粉末を添加し、ボールミル
などの装置で機械的エネルギーを与えて強制的に該分散
用粒子を均一に分散させて粒子分散型粉末を得る方法で
ある。ＭＡ法を利用することで、通常の溶解鋳造方法で
生じる分散粒子粉末の凝集という問題が発生せず、均質
な粒子分散型合金を製造することができると云われてい
る。The MA method is generally applied to a master alloy powder.
This is a method in which a predetermined amount of fine dispersion particle powder is added, and mechanical energy is applied by a device such as a ball mill to forcibly disperse the dispersion particles uniformly to obtain a particle dispersion type powder. It is said that the use of the MA method can produce a homogeneous particle-dispersed alloy without causing the problem of agglomeration of the dispersed particle powder that occurs in the usual melting and casting method.
【０００４】分散用粒子として熱力学的に安定である酸
化物を用いる酸化物分散強化型合金では、分散させた酸
化物粒子がそのままの形で製品にも存在し、クリープ特
性の改善に大きな効果を発揮していることは周知の事実
である。In an oxide dispersion strengthening alloy that uses a thermodynamically stable oxide as the dispersing particles, the dispersed oxide particles exist in the product as they are, which is a great effect for improving the creep characteristics. It is a well-known fact that it is exerting.
【０００５】しかしながら、一般に、酸化物分散強化型
合金は、延性に乏しく、室温での加工性に難点があり、
複雑な形状の部材を製造するときの問題点となってい
る。However, in general, the oxide dispersion strengthened alloy has poor ductility and has a problem in workability at room temperature.
This is a problem when manufacturing a member having a complicated shape.
【０００６】一方、近年になって、ＭＡ法は、単に微細
粒子を分散させるだけではないプロセスであることが明
らかになってきた。On the other hand, in recent years, it has become clear that the MA method is a process that does not merely disperse fine particles.
【０００７】例えば、酸化物粉末をＭＡ処理して添加し
た場合にも、製品中に分散させた酸化物のサイズが原料
として添加した酸化物粉末粒子のサイズより微細である
ことが多く、ＭＡ処理中に酸化物粒子に何らかの現象が
生じていることが予想されている。For example, even when the oxide powder is subjected to MA treatment and added, the size of the oxide dispersed in the product is often finer than the size of the oxide powder particles added as a raw material, and the MA treatment is carried out. It is expected that some phenomenon will occur in the oxide particles.
【０００８】この点に関し、「素形材」(１９９１年５
月、第７頁)には、耐摩耗性を確保するために炭化物、
ホウ化物などを分散させた場合には、添加した原料組成
と異なる複合ホウ化物や、形態の異なる炭化物が製品中
に分散することが報告されている。[0008] In this regard, "form material" (May 1991)
Mon, page 7), in order to secure wear resistance,
It has been reported that when a boride or the like is dispersed, a composite boride having a different raw material composition or a carbide having a different form is dispersed in the product.
【０００９】このように、ＭＡ処理は、単に分散粒子を
分散させるだけでなく、ＭＡ処理中に、分散させようと
して添加した粉末粒子が一度固溶して固化成形処理によ
って再析出したり、母合金粉末中の合金元素と反応し
て、添加した粉末粒子と異なる組成の化合物が析出した
りすることがある。最悪の場合、例えば、耐摩耗性向上
を期待して添加した分散粒子が、製品中では完全に消失
してしまい、耐摩耗性に効果のない異なる化合物が分散
する結果が生じる。As described above, in the MA treatment, not only the dispersed particles are dispersed, but the powder particles added to be dispersed during the MA treatment are once solid-dissolved and re-precipitated by the solidification molding treatment, or the mother treatment is performed. A compound having a composition different from that of the added powder particles may be precipitated by reacting with the alloy element in the alloy powder. In the worst case, for example, the dispersed particles added in the hope of improving wear resistance will disappear completely in the product, resulting in the dispersion of different compounds having no effect on wear resistance.
【００１０】[0010]
【発明が解決しようとする課題】以上の如く、従来、Ｍ
Ａ法を利用して製造した粒子分散型粉末を固化成形処理
して得られる粒子分散型合金の場合、母合金粉末の組成
や、分散させる粒子との組合せに拘束条件がかかった
り、或いは酸化物分散型合金の場合には加工性を犠牲に
しなければならなかったりするという問題点があった。As described above, the conventional M
In the case of a particle-dispersed alloy obtained by solidifying and molding a particle-dispersed powder manufactured by the method A, the composition of the mother alloy powder or the combination with the particles to be dispersed imposes constraint conditions or oxides. In the case of the dispersion type alloy, there was a problem that workability had to be sacrificed.
【００１１】本発明の目的は、上記従来技術の問題点を
解決し、ＭＡ処理により得られる粒子分散型粉末を原料
粉末として使用しても、所望の特性を得る目的で添加し
た分散用粒子が製品中においても該特性を発揮させるこ
とができる粒子分散型合金の製造方法を提供することに
ある。The object of the present invention is to solve the above-mentioned problems of the prior art, and even if the particle-dispersed powder obtained by MA treatment is used as the raw material powder, the particles for dispersion added for the purpose of obtaining desired characteristics are It is an object of the present invention to provide a method for producing a particle-dispersed alloy capable of exhibiting the characteristics even in a product.
【００１２】また、本発明の他の目的は、更に、酸化
物、炭化物、ホウ化物等をＭＡ処理により分散させる場
合においても、これらの分散粒子をその組成を変えるこ
となく製品中に分散させることができる粒子分散型合金
の製造方法を提供することにある。Another object of the present invention is to disperse the dispersed particles in the product without changing the composition even when the oxides, carbides, borides, etc. are dispersed by MA treatment. Another object of the present invention is to provide a method for producing a particle-dispersed alloy capable of achieving the above.
【００１３】また、本発明の他の目的は、更に、酸化物
をＭＡ処理により分散させる場合に加工性の優れた酸化
物分散型合金を製造できる方法を提供することにある。Another object of the present invention is to provide a method capable of producing an oxide-dispersed alloy having excellent workability when the oxide is dispersed by MA treatment.
【００１４】[0014]
【課題を解決するための手段】前記課題を解決するため
の手段として、本発明は、ＭＡ処理で粒子を分散させた
合金粉末を使用し、該粉末を高温で加圧し固化処理して
粒子分散型合金を製造するに際して、 純金属粉末又は合金粉末(非ＭＡ粉末)を準備する工程
と、 この純金属粉末又は合金粉末と同一の成分組成を有す
る粉末を母合金粉末とし、この母合金粉末中に、該母合
金粉末を構成する元素から製造中に生成する如何なる化
合物よりも熱的に安定な化合物からなる分散用粒子をメ
カニカルアロイング処理で分散させた合金粉末(ＭＡ合
金粉末)を製造する工程と、 上記の工程で準備した非ＭＡ粉末と、上記の工程
で製造したＭＡ合金粉末とを混合し、高温で加圧して固
化処理することを特徴とする粒子分散型合金の製造方法
を要旨としている。As a means for solving the above-mentioned problems, the present invention uses an alloy powder in which particles are dispersed by MA treatment, and the powder is pressed at high temperature to be solidified to disperse the particles. When manufacturing a mold alloy, a step of preparing pure metal powder or alloy powder (non-MA powder), and a powder having the same composition as the pure metal powder or alloy powder is used as the master alloy powder. To produce an alloy powder (MA alloy powder) in which dispersion particles made of a compound which is more thermally stable than any compound produced during production from the elements constituting the mother alloy powder are dispersed by mechanical alloying treatment. A process for producing a particle-dispersed alloy is characterized in that the non-MA powder prepared in the above process and the MA alloy powder produced in the above process are mixed and pressed at a high temperature for solidification treatment. As It
【００１５】また、他の本発明は、ＭＡ処理で粒子を分
散させた合金粉末を使用し、該粉末を高温で加圧し固化
処理して粒子分散型合金を製造するに際して、 純金属粉末又は合金粉末を母合金粉末とし、この母合
金粉末中に、該母合金粉末を構成する元素から製造中に
生成する如何なる化合物よりも熱的に安定な化合物から
なる分散用粒子をメカニカルアロイング処理で分散させ
た合金粉末(ＭＡ合金粉末)を製造する工程と、 上記の工程で用いた母合金粉末と同一の組成をベー
スとし、これに更に１種以上の合金元素を添加した成分
組成の合金粉末(非ＭＡ合金粉末)を準備する工程と、 上記の工程で製造したＭＡ合金粉末と、上記の工程
で準備した非ＭＡ合金粉末とを混合し、高温で加圧し
て固化処理することを特徴とする粒子分散型合金の製造
方法を要旨としている。In another aspect of the present invention, an alloy powder in which particles are dispersed by MA treatment is used, and when the powder is pressed at a high temperature and solidified to produce a particle dispersion type alloy, a pure metal powder or an alloy is used. The powder is used as a master alloy powder, and dispersion particles made of a compound that is more thermally stable than any compound generated during the production from the elements that constitute the master alloy powder are dispersed in the master alloy powder by mechanical alloying treatment. Based on the same composition as the mother alloy powder used in the above step and the step of producing the alloy powder (MA alloy powder), an alloy powder having a component composition in which one or more alloy elements are further added ( Non-MA alloy powder), the MA alloy powder produced in the above step, and the non-MA alloy powder prepared in the above step are mixed, and pressurized at high temperature for solidification treatment. Of particle-dispersed alloy The manufacturing method is the main point.
【００１６】[0016]
【作用】以下に本発明を更に詳細に説明する。The present invention will be described in more detail below.
【００１７】本発明者は、ＭＡ処理時に分散用として添
加した粒子の形態と、固化処理後に製品中に観察される
粒子の形態が変化したり、或いは異なる化合物が現われ
る例を詳細に調査し、分散用粒子粉末の組成と合金粉末
の組成を検討した結果、これらの例での分散用粒子と合
金粉末の組成の組合せには共通点があることを見い出し
た。The present inventor conducted a detailed investigation on an example in which the morphology of particles added for dispersion during MA treatment and the morphology of particles observed in the product after the solidification treatment are changed or different compounds appear, As a result of examining the composition of the dispersion particle powder and the composition of the alloy powder, it was found that the combination of the composition of the dispersion particle and the composition of the alloy powder in these examples has a common point.
【００１８】すなわち、１つ目の共通点は、分散させる
粒子の標準生成自由エネルギーが比較的不安定であるこ
と、２つ目の共通点は、母合金粉末の合金元素の中には
製造中に分散用粒子の成分元素と反応して安定な化合物
を作るものがあること、である。That is, the first common point is that the standard free energy of formation of the particles to be dispersed is relatively unstable, and the second common point is that some of the alloy elements of the mother alloy powder are not manufactured. There are those that react with the constituent elements of the particles for dispersion to form a stable compound.
【００１９】これらの共通点の意味するところは、ＭＡ
処理中に分散用粒子が母合金粉末中に固溶し、固化処理
中の加熱時に熱力学的に安定な化合物が析出するという
ことである。添加した分散粒子と同じ化合物が再析出す
る場合は問題はないが、異なる化合物が析出する場合
は、分散用粒子添加のときに期待する効果が得られなく
なり、問題が生じてくる。The meaning of these common points is that MA
That is, the particles for dispersion are solid-solved in the mother alloy powder during the treatment, and a thermodynamically stable compound is precipitated during heating during the solidification treatment. If the same compound as the added dispersed particles is reprecipitated, there is no problem, but if a different compound is precipitated, the expected effect cannot be obtained when the dispersing particles are added, which causes a problem.
【００２０】したがって、熱力学的に安定な分散用粒
子を添加するか、母合金粉末中の合金組成を改良し
て、所望する分散粒子が析出するように成分調整を行え
ばよいことになる。Therefore, the thermodynamically stable dispersion particles may be added or the alloy composition in the mother alloy powder may be improved to adjust the components so that the desired dispersion particles are precipitated.
【００２１】しかし、他の要求特性(耐酸化性、強度確
保など)を考慮すると、組成を変更できない場合や、分
散用粒子を変更できない場合などは問題を解決できな
い。However, considering other required characteristics (such as oxidation resistance and securing of strength), the problem cannot be solved when the composition cannot be changed or when the dispersion particles cannot be changed.
【００２２】この対策として、本発明では、第１に、熱
力学的に安定な分散用粒子を添加する、或いは第２に、
ＭＡ処理にかける分散用粒子を含む粉末の組成は分散用
粒子と反応しないように成分調整し、ＭＡ処理にかける
と分散用粒子と反応してしまうような組成の粉末は、Ｍ
Ａ処理を回避して、ＭＡ処理後の固化処理時に混合する
方法を見い出すに至ったものである。As measures against this, in the present invention, firstly, thermodynamically stable dispersion particles are added, or secondly,
The composition of the powder containing the particles for dispersion subjected to MA treatment is adjusted so that the particles do not react with the particles for dispersion, and the powder having a composition which reacts with the particles for dispersion when subjected to MA treatment is M
The present inventors have found a method of avoiding the A treatment and mixing during the solidification treatment after the MA treatment.
【００２３】この手法は、分散用粒子が母合金粉末の合
金元素と反応する場合にとどまらず、一般に応用できる
手法である。例えば、酸化物分散強化型合金のように加
工性を犠牲にして、高温強度、耐クリープ特性を上げる
合金の場合にも、母合金粉末にＭＡ法により酸化物を分
散させたＭＡ合金粉末と、この母合金粉末と同一の組成
の非ＭＡ合金粉末とを適量混合して固化処理することに
より、少なくともＭＡ処理時の分散用酸化物の反応を回
避できるので、ある程度の加工性を確保することができ
る。This method is not limited to the case where the dispersing particles react with the alloy element of the mother alloy powder, and is a method that can be generally applied. For example, in the case of an alloy such as an oxide dispersion strengthened alloy that improves high-temperature strength and creep resistance at the expense of workability, a MA alloy powder in which an oxide is dispersed in a mother alloy powder by an MA method, By mixing an appropriate amount of this mother alloy powder and a non-MA alloy powder having the same composition and solidifying the mixture, it is possible to avoid at least the reaction of the oxide for dispersion during the MA treatment, so that a certain degree of workability can be ensured. it can.
【００２４】次に本発明の製造条件について説明する。Next, the manufacturing conditions of the present invention will be described.
【００２５】まず、本発明の一つの特徴は、高温で加圧
して固化処理するための混合粉末として、ＭＡ処理した
合金粉末(ＭＡ合金粉末)と、ＭＡ処理しない粉末(非Ｍ
Ａ粉末)とを混合する点である。これにより、ＭＡ処理
によって分散用粒子と反応する元素をＭＡ処理しない粉
末中に添加でき、また、ＭＡ処理した粉末だけを固化処
理する場合に比べ、ＭＡ処理しない粉末の組成を耐食
性、高温強度等々の特性が得られる組成とすることがで
き、成分調整の自由度を増すことができる。First, one feature of the present invention is that MA-treated alloy powder (MA alloy powder) and non-MA-treated powder (non-M powder) are used as a mixed powder for pressurizing and solidifying at high temperature.
(A powder). As a result, an element that reacts with the particles for dispersion by the MA treatment can be added to the powder not subjected to the MA treatment, and the composition of the powder not subjected to the MA treatment can be compared with corrosion resistance, high temperature strength, etc. It is possible to obtain a composition capable of obtaining the above characteristics, and it is possible to increase the degree of freedom in adjusting the components.
【００２６】ＭＡ処理しない粉末としては、純金属粉末
或いは１種以上の合金元素を含む合金粉末(不可避的不
純物を含む)を選定できる。純金属粉末には、例えば、
Ｎi、Ｃo、Ｆeなどが挙げられる。合金粉末には、例え
ば、Ｎi基合金、Ｆe基合金、Ａl基合金などが挙げら
れ、これらの合金の成分系及び組成は、粒子分散型合金
の用途に要求される特性が発揮されるような種々の合金
元素を含有させた組成が可能である。As the powder not subjected to MA treatment, pure metal powder or alloy powder containing one or more kinds of alloy elements (including inevitable impurities) can be selected. For pure metal powder, for example,
Ni, Co, Fe and the like can be mentioned. Examples of the alloy powder include Ni-based alloys, Fe-based alloys, and Al-based alloys, and the component systems and compositions of these alloys are such that the characteristics required for the use of particle-dispersed alloys are exhibited. Compositions containing various alloying elements are possible.
【００２７】一例として、Ｎi基合金としては、Ｎiをベ
ースとして、Ｃr、Ｍo、Ｓi、Ｃu、Ｗ、Ｂなどの合金元
素の１種又は２種以上を適量添加した成分系が挙げられ
る。合金元素の添加量は、Ｃrは３０％以下、Ｓi、Ｃ
u、Ｗ、Ｂはそれぞれ５％以下が望ましい。As an example, the Ni-based alloy includes a component system in which one or more alloying elements such as Cr, Mo, Si, Cu, W and B are added in an appropriate amount based on Ni. The amount of alloying elements added is such that Cr is 30% or less, Si, C
u, W, and B are each preferably 5% or less.
【００２８】Ｆe基合金としては、Ｆeをベースとして、
Ｃ、Ｓi、Ｍn、Ｎi、Ｃr、Ｎb、Ｖ、Ｔi、Ａl、Ｃa、Ｚ
r、Ｍo、Ｔa、Ｈf、Ｙなどの合金元素の１種又は２種以
上を適量添加した成分系が挙げられる。合金元素の添加
量はＣ、Ｓi、Ｍnは２％以下、Ｎi、Ｃr、Ａlは３０％
以下、Ｎb、Ｖ、Ｔi、Ｃa、Ｚr、Ｍo、Ｔa、Ｈf、Ｙは
それぞれ１％以下が望ましい。The Fe-based alloy is based on Fe,
C, Si, Mn, Ni, Cr, Nb, V, Ti, Al, Ca, Z
A component system in which an appropriate amount of one or more alloying elements such as r, Mo, Ta, Hf and Y is added may be mentioned. The amount of alloying elements added is 2% or less for C, Si and Mn, and 30% for Ni, Cr and Al.
Hereinafter, Nb, V, Ti, Ca, Zr, Mo, Ta, Hf, and Y are preferably 1% or less.
【００２９】Ａl基合金としては、Ａlをベースとして、
Ｓi、Ｆe、Ｃu、Ｍn、Ｍg、Ｚn、Ｎi、Ｔiなどの合金元
素の１種又は２種以上を適量添加した成分系が挙げられ
る。合金元素の添加量は、Ｓiは２０％以下、Ｆe、Ｃ
u、Ｍn、Ｍg、Ｚn、Ｎi、Ｔiは１５％以下が望ましい。As the Al-based alloy, based on Al,
An example is a component system in which one or more alloying elements such as Si, Fe, Cu, Mn, Mg, Zn, Ni and Ti are added in appropriate amounts. The amount of alloying elements added is 20% or less for Si, Fe, and C.
u, Mn, Mg, Zn, Ni, and Ti are preferably 15% or less.
【００３０】一方、ＭＡ処理にかける粉末は、母合金粉
末と分散用粒子とであるが、これらの母合金粉末と分散
用粒子の組合せ方としては、第１に、母合金粉末から製
造中に生成する如何なる化合物(炭化物、窒化物、酸化
物、ホウ化物、珪化物など)よりも熱的に安定な化合物
(炭化物、窒化物、酸化物、ホウ化物、珪化物など)を分
散用粒子として選定し、第２に、製造中に互いに反応せ
ず或いは反応し難い組成のものを選定する。On the other hand, the powder to be subjected to the MA treatment is the mother alloy powder and the dispersing particles. The first method of combining the mother alloy powder and the dispersing particles is as follows. A compound that is more thermally stable than any compound that forms (carbides, nitrides, oxides, borides, silicides, etc.)
(Carbides, nitrides, oxides, borides, silicides, etc.) are selected as particles for dispersion, and secondly, those having a composition that does not react with each other or hardly reacts with each other during manufacturing.
【００３１】このような熱的に安定な化合物(分散用粒
子)としては、例えば、Ｆe、Ｎiベース合金中のＹ
2Ｏ3、ＺrＯ2などの酸化物、Ｆeベース合金中のＴiＣ、
ＺrＣなどの炭化物やＴiＮなどの窒化物、Ｎi、Ｆeベー
ス合金中のＺrＢ2、ＴiＢ2などのホウ化物、Ａlベース
合金中のＭg2Ｓi、Ｆeベース合金中のＭoＳi2などの珪
化物が挙げられる。Examples of such thermally stable compounds (dispersion particles) include, for example, Y in Fe and Ni base alloys.
2 O 3 , oxides such as ZrO 2 , TiC in Fe-based alloys,
Carbides such as ZrC and nitrides such as TiN, borides such as Ni, Fe-based alloys ZrB 2 and TiB 2 , suicides such as Mg 2 Si in Al-based alloys and MoSi 2 in Fe-based alloys. To be
【００３２】一方、互いに反応し易い元素と化合物(分
散用粒子)としては、例えば、Ｖ化合物(例、ＶＣ)とＮb
の組合せ、Ｙ2Ｏ3とＴiの組合せ、Ｆe酸化物とＹ、Ｔ
i、Ｚrの組合せ、ＡlＮとＴiの組合せ、ＣrＢ、Ｖ等が
挙げられる。On the other hand, examples of the element and the compound (dispersion particles) that easily react with each other include V compound (eg, VC) and Nb.
, Y 2 O 3 and Ti, Fe oxide and Y, T
Examples include i, Zr combination, AlN and Ti combination, CrB, V and the like.
【００３３】但し、分散用粒子と反応し易い元素を添加
したい場合には、非ＭＡ粉末中に含有させることができ
る。すなわち、ＭＡ法にかけるのに用いた母合金(純金
属又は合金)の組成をベースとし、これに上記の分散用
粒子と反応し易い元素を添加した組成の合金粉末を非Ｍ
Ａ合金粉末とする。その際、分散用粒子と反応し易い元
素と共に他の合金元素を添加してもよく、或いは分散用
粒子と反応せず或いは反応し難い合金元素だけを添加し
てもよい。However, if it is desired to add an element that easily reacts with the particles for dispersion, the element can be contained in the non-MA powder. That is, based on the composition of the mother alloy (pure metal or alloy) used for the MA method, an alloy powder having a composition in which an element that easily reacts with the above-mentioned particles for dispersion is added is non-M
A alloy powder is used. At that time, other alloying elements may be added together with the element which easily reacts with the dispersing particles, or only the alloying element which does not react with the dispersing particles or hardly reacts with the dispersing particles.
【００３４】なお、ＭＡ合金粉末と非ＭＡ粉末又は非Ｍ
Ａ合金粉末とを混合し、高温で加圧して固化処理する方
法としては、ＨＩＰ(熱間等方静水圧プレス)、熱間押出
し法或いはそれらの類似方法が用いられる。MA alloy powder and non-MA powder or non-M powder
As a method of mixing with the A alloy powder and pressurizing at high temperature for solidification treatment, HIP (hot isostatic pressing), hot extrusion method or a similar method thereof is used.
【００３５】また、ＭＡ合金粉末中の分散用粒子の配合
量及び粒径は、通常のＭＡ法にて採用されている程度の
量及び粒径でよく、例えば、母合金粉末は粒度１００メ
ッシュ(粒径約１５０μm)以下、分散用粒子は平均粒径
約２０nmのものが用いられる。また、非ＭＡ粉末粒径は
母合金の粒径と同じにすればよい。更に、非ＭＡ粉末と
ＭＡ合金粉末との混合量も適宜決めることができるが、
その際、ＭＡ合金粉末の混合量があまり少ないと、ＭＡ
法による分散粒子の効果が期待できなくなるので留意す
る。The compounding amount and particle size of the dispersing particles in the MA alloy powder may be the amount and particle size that are adopted in the ordinary MA method. For example, the mother alloy powder has a particle size of 100 mesh ( The particle size is about 150 μm or less, and the average particle size is about 20 nm. The particle size of the non-MA powder may be the same as the particle size of the master alloy. Further, the mixing amount of the non-MA powder and the MA alloy powder can be appropriately determined,
At that time, if the mixing amount of the MA alloy powder is too small, MA
Note that the effect of dispersed particles by the method cannot be expected.
【００３６】次に本発明の実施例を示す。Next, examples of the present invention will be shown.
【００３７】[0037]
【実施例１】母合金粉末Ａとして、Ｎiをベースとした
Ｎi−２０％Ｃr−３％Ｍo−４％Ｎb(wt％)合金粉末を用
意し、これに分散用粉末してＹ2Ｏ3を３wt％添加し、Ｍ
Ａ処理を実施した。一部は、そのまま軟鋼カプセルに充
填し、１１５０℃での熱間押出しによって固化し、１方
向再結晶装置に供してアスペクト比の高い伸長結晶粒組
織を作った(比較材)。なお、１方向再結晶装置は誘導コ
イルによる局所的な加熱帯と、材料を一定の速度で誘導
コイル内を通過させることのできる引き抜き装置で構成
される装置である。As Example 1 master alloy powder A, Ni-20% was based on Ni Cr-3% Mo-4 % Nb (wt%) prepared alloy powder was dispersed powders to Y 2 O 3 3 wt% is added, M
Process A was carried out. A part of the composition was filled in a mild steel capsule as it was, solidified by hot extrusion at 1150 ° C., and subjected to a unidirectional recrystallization apparatus to form an elongated crystal grain structure having a high aspect ratio (comparative material). The one-way recrystallization device is a device including a local heating zone by an induction coil and a drawing device capable of passing a material through the induction coil at a constant speed.
【００３８】また、他の一部は、軟鋼カプセルに充填す
るときに、上記ＭＡ合金粉末に対して、上記母合金粉末
Ａと同じ組成の合金粉末を１０wt％混合し、以下同じ方
法で固化し、１方向再結晶装置に供した(本発明材)。Another part is that when filling a mild steel capsule, 10 wt% of an alloy powder having the same composition as the mother alloy powder A is mixed with the MA alloy powder and then solidified by the same method. It was subjected to a one-way recrystallization apparatus (material of the present invention).
【００３９】得られた両合金を室温で冷間圧延したとき
の加工性を図１及び図２に示す。本発明材は、圧延加工
による割れ発生までのパス回数が多く、室温での加工性
に優れていると共に、延性も優れていることがわかる。
一方、比較材は、僅か数パスにて割れが発生し、また延
性に劣っている。比較材では高温強度を得るために添加
した分散用粒子が合金全体中に分散しているため、加工
性を悪くしているが、これは、圧延による形状変化に対
し、分散用粒子(Ｙ2Ｏ3)の含まれない領域で、変形が進
み、加工割れを起こしたためと考えられる。The workability of both the obtained alloys when cold-rolled at room temperature is shown in FIGS. 1 and 2. It can be seen that the material of the present invention has a large number of passes until cracking due to rolling, has excellent workability at room temperature, and has excellent ductility.
On the other hand, the comparative material had cracks in only a few passes and was inferior in ductility. In the comparative material, the dispersing particles added to obtain the high temperature strength are dispersed in the entire alloy, which deteriorates the workability. This is because the dispersing particles (Y 2 It is considered that the deformation proceeded in the region not containing O 3 ) to cause work cracking.
【００４０】[0040]
【実施例２】実施例１の本発明材において、母合金粉末
中のＣr量を１０〜３０wt％、Ｍo量を１〜５wt％、Ｎb
量を１〜５wt％の範囲で変化させた場合、分散用粒子
(Ｙ2Ｏ3)の添加量を１〜５wt％の範囲で変化させた場
合、或いは非ＭＡ粉末の混合割合を３〜２０wt％の範囲
で変化させた場合、いずれも実施例１の本発明材と同様
の優れた加工性が得られた。Example 2 In the material of the present invention of Example 1, the amount of Cr in the mother alloy powder is 10 to 30 wt%, the amount of Mo is 1 to 5 wt%, and Nb is
Particles for dispersion when the amount is changed in the range of 1 to 5 wt%
When the addition amount of (Y 2 O 3 ) was changed in the range of 1 to 5 wt%, or when the mixing ratio of the non-MA powder was changed in the range of 3 to 20 wt%, the present invention of Example 1 was used. The same excellent workability as the material was obtained.
【００４１】[0041]
【実施例３】ＮiをベースとしたＮi−３０％Ｃr−３％
Ｓi−１％Ｂに少量のＭo、Ｃu、Ｗ及びＮb(wt％)を添加
した合金粉末を母合金粉末とし、これに７wt％のＶＣを
添加してＭＡ処理を実施し、１０００℃でＨＩＰ処理し
た(比較材)。この比較材を調べたところ、ＶＣが消失
し、ＮbＣ、ＶＢ2が析出していた。これは、分散させた
粒子ＶＣが製造中に熱的に安定でなく、ＶがＮbと置換
してＮbＣが析出し、そのために分離させられたＶがＢ
と結合してＶＢ2が析出したため、ＶＣが消失したもの
と考えられる。[Embodiment 3] Ni-based Ni-30% Cr-3%
An alloy powder obtained by adding a small amount of Mo, Cu, W and Nb (wt%) to Si-1% B was used as a master alloy powder, and 7wt% VC was added to this to perform MA treatment, and HIP at 1000 ° C. Treated (comparative material). When this comparative material was examined, VC disappeared and NbC and VB 2 were deposited. This is because the dispersed particles VC are not thermally stable during the production and V is replaced with Nb to precipitate NbC, and thus the separated V is B
It is considered that VC disappeared because VB 2 was precipitated in combination with
【００４２】そこで、母合金粉末Ａとして、Ｎiをベー
スとしたＮi−３０％Ｃr−３％Ｓi−１％Ｂの組成に各
２％のＭo、Ｃu及びＷ(wt％)を添加した合金粉末を作成
し、この母合金粉末に１０wt％のＶＣをＭＡ処理で分散
させた。得られたＭＡ合金粉末に対して、非ＭＡ合金粉
末として、ＮiをベースとしたＮi−３０％Ｃr−３％Ｓi
−１％Ｂに各２％のＭo、Ｃu、Ｗ及びＮb(wt％)を添加
した粉末を４０wt％の割合で混合し、ＨＩＰで固化した
(本発明材)。その結果、ＶＣの分散した粒子分散型合金
を得ることができた。これは、ＶＣがＮbの存在のもと
では熱的に安定でないため、母合金としてＮbを含まな
い粉末を用いたことにより、分散用ＶＣが製品中でも分
散したものと考えられる。Therefore, as the mother alloy powder A, an alloy powder in which 2% Mo, Cu and W (wt%) are added to the composition of Ni-30% Cr-3% Si-1% B based on Ni is used. Was prepared, and 10 wt% of VC was dispersed in the mother alloy powder by MA treatment. Based on the obtained MA alloy powder, as a non-MA alloy powder, Ni based Ni-30% Cr-3% Si
Powders obtained by adding 2% Mo, Cu, W and Nb (wt%) to -1% B were mixed at a ratio of 40 wt% and solidified by HIP.
(Inventive material). As a result, a particle-dispersed alloy in which VC was dispersed could be obtained. It is considered that this is because VC is not thermally stable in the presence of Nb, and thus the VC for dispersion was dispersed in the product by using the powder containing no Nb as the mother alloy.
【００４３】得られた両合金についての腐食試験の結果
を図３に、摩耗試験の結果を図４に示す。摩耗試験は、
大越式摩耗試験機を使用し、相手材：ＳＵＪ-２(ＨＲＣ
４５)、摩耗距離：４００m、摩耗速度：０.５m／s、最
終荷重：３.３kg、雰囲気：室温乾燥状態の条件で行っ
た。腐食試験では各種腐食液に５０℃×２４hr浸漬し
た。図より、本発明材は、比較材と比べ、耐食性を劣化
させることなく、耐摩耗性が向上していることがわか
る。FIG. 3 shows the results of the corrosion test for the obtained alloys, and FIG. 4 shows the results of the wear test. The wear test is
Using Ogoshi type abrasion tester, mating material: SUJ-2 (HRC
45), wear distance: 400 m, wear rate: 0.5 m / s, final load: 3.3 kg, atmosphere: dry at room temperature. In the corrosion test, it was immersed in various corrosive liquids at 50 ° C. for 24 hours. From the figure, it is understood that the material of the present invention has improved wear resistance without deteriorating the corrosion resistance as compared with the comparative material.
【００４４】[0044]
【実施例４】実施例３の本発明材において、母合金粉末
中のＣr量を１０〜４０wt％、Ｓi量を１〜５wt％、Ｂ量
を０.５〜３wt％、Ｍo、Ｃu、Ｗ量をそれぞ１〜５wt％
の範囲で変化させた場合、分散用粒子(ＶＣ)の添加量を
３〜３０wt％の範囲で変化させた場合、或いは混合させ
る非ＭＡ粉末中のＮb量を１〜５wt％で変化させた場
合、非ＭＡ合金粉末の混合割合を２０〜５０wt％の範囲
で変化させた場合、いずれも実施例３の本発明材と同様
に優れた耐摩耗性が得られた。Example 4 In the material of the present invention of Example 3, the amount of Cr in the mother alloy powder is 10 to 40 wt%, the amount of Si is 1 to 5 wt%, the amount of B is 0.5 to 3 wt%, Mo, Cu and W. 1 to 5 wt% each
When the amount of dispersion particles (VC) added is changed within the range of 3 to 30 wt%, or when the amount of Nb in the non-MA powder to be mixed is changed within the range of 1 to 5 wt%. When the mixing ratio of the non-MA alloy powder was changed within the range of 20 to 50 wt%, excellent wear resistance was obtained as in the case of the inventive material of Example 3.
【００４５】[0045]
【実施例５】ＡlをベースとしたＡl−３％Ｃu−１.５％
Ｍgに５μm径のＳiＣ粒子を３０体積％添加し潤滑溶剤
としてエタノールを３wt％添加してＭＡ処理して分散さ
せた粉末を、４８０℃でＨＩＰ処理で固化した(比較
材)。同様にＳiＣ粒子を添加、ＭＡ処理を行わずＨＩＰ
処理で固化した材料も用意した。その結果、Ｔ６処理後
の引張強さは６０５Ｎ／mm2になった。ＳiＣ粒子を添加
しなかったものは４８０Ｎ／mm2程度であり、分散強化
が効果を発揮した。これは添加したＳiＣ粒子だけでな
く、添加したエタノール中の酸素、炭素とベースメタル
のＡlが反応して生成するアルミナ及びＡl4Ｃ3の分散に
寄与するものである。しかし、分散強化合金は加工性が
劣る。同材料を加熱温度４５０℃で、実施したところ、
圧下率が１０％に達する前に破壊した。Example 5 Al-3% Cu-1.5% based on Al
A powder obtained by adding 30% by volume of 5 μm-diameter SiC particles to Mg and adding 3 wt% of ethanol as a lubricating solvent and MA-dispersed the powder was solidified by HIP treatment at 480 ° C. (comparative material). Similarly, SiC particles were added and HIP was performed without MA treatment.
A material solidified by the treatment was also prepared. As a result, the tensile strength after T6 treatment was 605 N / mm 2 . The amount without addition of SiC particles was about 480 N / mm 2 , and dispersion strengthening was effective. This contributes not only to the added SiC particles but also to the dispersion of alumina and Al 4 C 3 produced by the reaction of oxygen and carbon in the added ethanol with Al of the base metal. However, the dispersion strengthened alloy has poor workability. When the same material was heated at a heating temperature of 450 ° C.,
It fractured before the rolling reduction reached 10%.
【００４６】そこで、母合金粉末として、Ａlをベース
としたＡl−３％Ｃu−１.５％Ｍgに５μm径のＳiＣ粒子
を３０体積％添加し、潤滑溶剤としてエタノールを３wt
％添加従ってＭＡ処理して分散させた粉末を用意した。
得られたＭＡ処理合金粉末に対して、非ＭＡ処理粉末と
して、ＡlをベースとしたＡl−３％Ｃu−１.５％Ｍg−
１５％Ｓi粉末を５０％の割合で混合し、ＨＩＰで固化
した(本発明材)。Therefore, 30% by volume of 5 μm diameter SiC particles was added to Al-3% Cu-1.5% Mg based on Al as a mother alloy powder, and 3 wt% of ethanol was used as a lubricating solvent.
%, And then MA treatment was performed to prepare a dispersed powder.
Based on the obtained MA-treated alloy powder, Al-based Al-3% Cu-1.5% Mg-as non-MA-treated powder.
15% Si powder was mixed at a ratio of 50% and solidified by HIP (material of the present invention).
【００４７】得られた合金について、機械的性質、加工
性について調査した結果を図５に示す。本発明材は、比
較材と比べ、機械的性質を劣化させることなく、加工性
が向上していることがわかる。The results of investigations on the mechanical properties and workability of the obtained alloy are shown in FIG. It can be seen that the material of the present invention has improved workability as compared with the comparative material without deteriorating the mechanical properties.
【００４８】[0048]
【実施例６】実施例５の本発明材において、母合金粉末
中のＣu量を０.１〜３.０wt％に、Ｍg量を０.１〜１.５
wt％にそれぞれ変化させた場合、分散させるＳiＣ粒子
の粒子径を０.２〜１０μmの範囲で、体積率を５〜３０
体積％の範囲で変化させた場合、エタノール添加量を１
〜８wt％の範囲で変化させた場合、或いは混合する非Ｍ
Ａ処理粉末の割合を２０〜５０wt％の範囲で変化させた
場合、いずれも実施例５と同様に優れた加工性が得られ
た。Example 6 In the material of the present invention of Example 5, the amount of Cu in the mother alloy powder is 0.1 to 3.0 wt% and the amount of Mg is 0.1 to 1.5.
When each is changed to wt%, the particle size of the SiC particles to be dispersed is in the range of 0.2 to 10 μm and the volume ratio is 5 to 30.
When changing in the range of volume%, the amount of ethanol added is 1
When changing in the range of ~ 8wt%, or mixing non-M
When the ratio of the A-treated powder was changed in the range of 20 to 50 wt%, excellent workability was obtained in all cases as in Example 5.
【００４９】[0049]
【発明の効果】以上説明したように、本発明によれば、
粒子分散型合金の製造において分散用粒子をその特性を
損うことなく製品中に分散させることが可能となり、酸
化物分散型合金の難点とされている加工性の劣化を改善
でき、また耐摩耗性のために分散用粒子として添加する
炭化物やホウ化物の製造中の変化を防止できるので、優
れた加工性と高温強度、耐クリープ特性を有する粒子分
散型Ｆe基、Ｎi基、Ａl基合金や、耐食性、耐摩耗性に
優れる粒子分散型Ｎi基合金を製造できる。As described above, according to the present invention,
In the production of particle-dispersed alloys, it is possible to disperse the particles for dispersion in the product without impairing the characteristics, and it is possible to improve the deterioration of workability, which is the difficulty of oxide-dispersed alloys, and to improve wear resistance. Since it can prevent changes in the production of carbides and borides that are added as dispersion particles due to its excellent properties, it has excellent workability, high temperature strength, and creep resistance. A particle-dispersed Ni-based alloy having excellent corrosion resistance and wear resistance can be manufactured.
【図１】実施例１で得られた合金の冷間圧延における割
れ発生までのパス回数を示す図である。FIG. 1 is a diagram showing the number of passes until cracking occurs in cold rolling of the alloy obtained in Example 1.
【図２】実施例１で得られた合金の引張り試験での破断
伸びを示す図である。FIG. 2 is a diagram showing elongation at break in a tensile test of the alloy obtained in Example 1.
【図３】実施例３で得られた合金の耐摩耗性(比摩耗量)
を示す図である。FIG. 3 Abrasion resistance (specific wear amount) of the alloy obtained in Example 3
FIG.
【図４】実施例３で得られた合金の各種腐食液中での腐
食減量を示す図である。FIG. 4 is a diagram showing the corrosion weight loss of the alloy obtained in Example 3 in various corrosive liquids.
【図５】実施例５で得られた合金の機械的性質と加工性
(割れ発生までの圧下率)を示す図である。FIG. 5 Mechanical properties and workability of the alloy obtained in Example 5
It is a figure which shows (the rolling reduction until the crack generation).
Claims (3)
う)処理で粒子を分散させた合金粉末を使用し、該粉末
を高温で加圧し固化処理して粒子分散型合金を製造する
に際して、 純金属粉末又は合金粉末(非ＭＡ粉末)を準備する工程
と、 この純金属粉末又は合金粉末と同一の成分組成を有す
る粉末を母合金粉末とし、この母合金粉末中に、該母合
金粉末を構成する元素から製造中に生成する如何なる化
合物よりも熱的に安定な化合物からなる分散用粒子をメ
カニカルアロイング処理で分散させた合金粉末(ＭＡ合
金粉末)を製造する工程と、 上記の工程で準備した非ＭＡ粉末と、上記の工程
で製造したＭＡ合金粉末とを混合し、高温で加圧して固
化処理することを特徴とする粒子分散型合金の製造方
法。1. A pure metal powder is used when an alloy powder in which particles are dispersed by a mechanical alloying (hereinafter referred to as MA) treatment is used and the powder is pressed at a high temperature and solidified to produce a particle dispersion type alloy. Or, a step of preparing an alloy powder (non-MA powder), and a powder having the same composition as the pure metal powder or the alloy powder is used as a master alloy powder, and the elements constituting the master alloy powder are contained in the master alloy powder. A step of producing an alloy powder (MA alloy powder) in which dispersion particles made of a compound that is more thermally stable than any compound produced during the production are dispersed by mechanical alloying treatment; A method for producing a particle-dispersed alloy, which comprises mixing the MA powder and the MA alloy powder produced in the above step and pressurizing the mixture at a high temperature for solidification.
使用し、該粉末を高温で加圧し固化処理して粒子分散型
合金を製造するに際して、 純金属粉末又は合金粉末を母合金粉末とし、この母合
金粉末中に、該母合金粉末を構成する元素から製造中に
生成する如何なる化合物よりも熱的に安定な化合物から
なる分散用粒子をメカニカルアロイング処理で分散させ
た合金粉末(ＭＡ合金粉末)を製造する工程と、 上記の工程で用いた母合金粉末と同一の組成をベー
スとし、これに更に１種以上の合金元素を添加した成分
組成の合金粉末(非ＭＡ合金粉末)を準備する工程と、 上記の工程で製造したＭＡ合金粉末と、上記の工程
で準備した非ＭＡ合金粉末とを混合し、高温で加圧し
て固化処理することを特徴とする粒子分散型合金の製造
方法。2. When using an alloy powder in which particles are dispersed by MA treatment and pressurizing the powder at a high temperature to solidify it to produce a particle dispersion type alloy, pure metal powder or alloy powder is used as a mother alloy powder. An alloy powder (MA) in which dispersion particles made of a compound that is more thermally stable than any compound produced during the production from the elements constituting the mother alloy powder are dispersed in the mother alloy powder by mechanical alloying treatment (MA (Alloy powder) manufacturing process, and based on the same composition as the mother alloy powder used in the above process, an alloy powder (non-MA alloy powder) with a component composition in which one or more alloy elements are further added Manufacture of a particle-dispersed alloy characterized by mixing the preparing step, the MA alloy powder prepared in the above step, and the non-MA alloy powder prepared in the above step, and pressurizing at high temperature for solidification treatment. Method.
する１種以上の合金元素として、少なくとも、製造中に
ＭＡ合金粉末の成分と反応し易い元素を選択する請求項
３に記載の方法。3. The method according to claim 3, wherein at least an element which easily reacts with a component of the MA alloy powder during production is selected as the one or more alloy elements added in the step.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP6098173A JPH07278695A (en) | 1994-04-12 | 1994-04-12 | Production of particle dispersion type alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP6098173A JPH07278695A (en) | 1994-04-12 | 1994-04-12 | Production of particle dispersion type alloy |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH07278695A true JPH07278695A (en) | 1995-10-24 |
Family
ID=14212660
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP6098173A Withdrawn JPH07278695A (en) | 1994-04-12 | 1994-04-12 | Production of particle dispersion type alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH07278695A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101886213A (en) * | 2010-06-30 | 2010-11-17 | 北京航空航天大学 | Ultra-disperse structure complex phase alloy steel and preparation method thereof |
-
1994
- 1994-04-12 JP JP6098173A patent/JPH07278695A/en not_active Withdrawn
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101886213A (en) * | 2010-06-30 | 2010-11-17 | 北京航空航天大学 | Ultra-disperse structure complex phase alloy steel and preparation method thereof |
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