JPH0480302A - Ni alloy powder and manufacture thereof - Google Patents
Ni alloy powder and manufacture thereofInfo
- Publication number
- JPH0480302A JPH0480302A JP2192089A JP19208990A JPH0480302A JP H0480302 A JPH0480302 A JP H0480302A JP 2192089 A JP2192089 A JP 2192089A JP 19208990 A JP19208990 A JP 19208990A JP H0480302 A JPH0480302 A JP H0480302A
- Authority
- JP
- Japan
- Prior art keywords
- powder
- alloy
- oxide
- fine
- phase
- 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
- 239000000843 powder Substances 0.000 title claims abstract description 84
- 229910000990 Ni alloy Inorganic materials 0.000 title claims abstract description 30
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 13
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 15
- 239000000956 alloy Substances 0.000 claims abstract description 15
- 239000002994 raw material Substances 0.000 claims abstract description 14
- 229910003310 Ni-Al Inorganic materials 0.000 claims abstract description 9
- 239000000463 material Substances 0.000 claims abstract description 8
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 7
- 230000001590 oxidative effect Effects 0.000 claims abstract description 4
- 230000002093 peripheral effect Effects 0.000 claims abstract 2
- 230000003647 oxidation Effects 0.000 claims description 10
- 238000007254 oxidation reaction Methods 0.000 claims description 10
- 239000002131 composite material Substances 0.000 claims description 9
- 125000004122 cyclic group Chemical group 0.000 claims description 9
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 claims description 7
- 229910052760 oxygen Inorganic materials 0.000 claims description 7
- 239000001301 oxygen Substances 0.000 claims description 7
- 239000012535 impurity Substances 0.000 claims description 4
- 238000010438 heat treatment Methods 0.000 claims description 3
- TWNQGVIAIRXVLR-UHFFFAOYSA-N oxo(oxoalumanyloxy)alumane Chemical compound O=[Al]O[Al]=O TWNQGVIAIRXVLR-UHFFFAOYSA-N 0.000 claims description 3
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 abstract description 11
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 abstract description 3
- 229910052593 corundum Inorganic materials 0.000 abstract description 3
- 239000011159 matrix material Substances 0.000 abstract description 3
- 229910001845 yogo sapphire Inorganic materials 0.000 abstract description 3
- 229910000480 nickel oxide Inorganic materials 0.000 abstract description 2
- GNRSAWUEBMWBQH-UHFFFAOYSA-N oxonickel Chemical compound [Ni]=O GNRSAWUEBMWBQH-UHFFFAOYSA-N 0.000 abstract description 2
- 238000000034 method Methods 0.000 description 10
- 238000005054 agglomeration Methods 0.000 description 4
- 230000002776 aggregation Effects 0.000 description 4
- 238000007796 conventional method Methods 0.000 description 4
- 239000000203 mixture Substances 0.000 description 4
- 230000000694 effects Effects 0.000 description 3
- 230000015572 biosynthetic process Effects 0.000 description 2
- 230000013011 mating Effects 0.000 description 2
- 238000005551 mechanical alloying Methods 0.000 description 2
- 239000002245 particle Substances 0.000 description 2
- 238000011946 reduction process Methods 0.000 description 2
- 238000010301 surface-oxidation reaction Methods 0.000 description 2
- 229910001018 Cast iron Inorganic materials 0.000 description 1
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- 229910000846 In alloy Inorganic materials 0.000 description 1
- 241000190020 Zelkova serrata Species 0.000 description 1
- 238000005299 abrasion Methods 0.000 description 1
- 238000009825 accumulation Methods 0.000 description 1
- 239000002253 acid Substances 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 229910052739 hydrogen Inorganic materials 0.000 description 1
- 239000001257 hydrogen Substances 0.000 description 1
- 238000004663 powder metallurgy Methods 0.000 description 1
- 238000005245 sintering Methods 0.000 description 1
Abstract
Description
【発明の詳細な説明】
〔産業上の利用分野〕
この発明は、特にすぐれた耐摩耗性を有する焼結体の製
造に用いるのに適したＮｉ合金粉末、並びにその製造法
に関するものである。DETAILED DESCRIPTION OF THE INVENTION [Field of Industrial Application] The present invention relates to a Ni alloy powder suitable for use in producing a sintered body having particularly excellent wear resistance, and a method for producing the same.
従来、例えば特開昭５８−２０７３４０号公報に記載さ
れるように、一般に、
重量％で（以Ｆ％は重−％を示す）、
Ａ１１：０．１〜１％、
を含有し、残りが実質的にＮｉからなる組成を有するＮ
ｉ−ＡΩ合金原料粉末に、
大気中、４５０〜６００℃の温度に加熱保持、の条件で
表面酸化処理を施した後、
ボールミル中で、メカニカルアロイング処理を施して、
粉末表面部に形成された酸化物を粉末全体に均一に分布
させ、
引続いて余剰の酸累を除去する目的で、還元性雰囲気中
、４００〜８００℃の温度に加熱保持、
の条件で還元処理を施して、上記の表面酸化によって生
成した微細な酸化アルミニウム（以下Ａｇ２Ｏ３で示す
）がＮＩまたはＮｉ−Ａｌ合金の素地に均一に分散した
組織を有するＮｉ合金粉末を製造する方法が知られてい
る。Conventionally, for example, as described in JP-A-58-207340, A11: 0.1 to 1% is contained in weight% (hereinafter F% indicates weight%), and the remainder is N having a composition consisting essentially of Ni
The i-AΩ alloy raw material powder was subjected to surface oxidation treatment under the conditions of heating and holding at a temperature of 450 to 600°C in the atmosphere, and then mechanical alloying treatment was performed in a ball mill.
In order to uniformly distribute the oxides formed on the powder surface throughout the powder, and subsequently to remove excess acid accumulation, the powder is heated and maintained at a temperature of 400 to 800°C in a reducing atmosphere. There is a known method for producing Ni alloy powder having a structure in which fine aluminum oxide (hereinafter referred to as Ag2O3) generated by the above-mentioned surface oxidation is uniformly dispersed in the base of NI or Ni-Al alloy. There is.
また、この方法で製造されたＮｉ合金粉末が、含油軸受
やガイドブツシュ、さらにバルブシートなどの各種駆動
装置の構造部材を通常の粉末冶金法により製造するに際
して、原料粉末として用いられていることも良く知られ
るところである。In addition, the Ni alloy powder produced by this method is used as a raw material powder when manufacturing structural members of various drive devices such as oil-impregnated bearings, guide bushes, and valve seats by ordinary powder metallurgy. It is also well known.
一方、近年の各種駆動装置の高性能化および高速化はめ
ざましく、これに伴ない、これの構造部材の使用環境も
一段と苛酷さを増し、このため構造部材には一層の耐摩
耗性が要求されているが、上記の従来轟欅鰺牟細おり方
法で製造されたＮｉ合金粉末を用いて製造された焼結体
製構造部材では耐摩耗性が十分でなく、これらの要求に
満足して対応することができないのが現状である。On the other hand, in recent years, the performance and speed of various drive devices have increased dramatically, and as a result, the environments in which these structural members are used have become even more severe, and as a result, structural members are required to have even higher wear resistance. However, the wear resistance of structural members made of sintered bodies manufactured using Ni alloy powder manufactured by the conventional Todoroki Keyaki Ajimu thin-ori method described above is insufficient, and these requirements have been met satisfactorily. The current situation is that this is not possible.
なお、この場合上記従来方法により製造された従来Ｎｉ
合金粉末において、素地に均一に分散するＡｌ２０３の
含有割合を多くして耐摩耗性の向上をはかる試みもなさ
れたか、粉末表面に露出するＡｌ ０ 粒の割合が増す
と、Ａ Ｉ ２０ ａ粒か粗大化し易く′なることと含
まって、焼結性が著しく低下し、この結果焼結体の強度
低下を招き、強度の而で実用に供することができないも
のである。In this case, the conventional Ni manufactured by the above conventional method
In alloy powder, attempts have been made to increase the content of Al203, which is uniformly dispersed in the base material, to improve wear resistance. The sinterability is significantly lowered due to the tendency to coarsen the sintered body, which results in a decrease in the strength of the sintered body, making it impossible to put it to practical use due to its strength.
そこで、本発明者等は、上述のような観点から、各種駆
動装置の構造部材として用いた場合に、すぐれた耐摩耗
性を発揮する焼結体を製造すべく、上記従来Ｎｉ合金粉
末に着目し研究を行なった結果、
まず、上記の従来方法によるＮｉ合金粉末の製造に用い
られているＮｉ−Ａｌ１合金原料粉末における０、１〜
１％のＡｐ含有量に比して相対的に多い割合の１．５〜
１０％のＡｌｌを含有したＮｉ−Ａｌ１合金粉末を用い
、
このＮｊ−Ａ、Ｑ合金原料粉末に、上記の従来方法＝昧
−４白白法における４５０〜６００℃の酸化温度より一
段と高い１０００〜１３００℃の温度で、望ましくは粉
末流動化状態で、酸化処理を施すと、形成された酸化物
粉末は、主体が酸化ニッケル（以下ＮｉＯで示す）から
なる素地に、粉末中心部を通るあらゆる断面において、
粉末、中心部と粉末周辺部との間に、微細なＮｉ−１複
合酸化物〔以下、（Ｎｉ、、’ｌ ）０で示す〕が環状
に凝集してなる環状複合酸化物相、いいかえれば粉末内
部に層をなしてシェル状に凝集分布する微細な（Ｎｉ、
ｌ ）Ｏで構成された環状複合酸化物相が存在する組織
をもつようになり、
さらに、この酸化物粉末に、メカニカルアロイング処理
を施すことなく、直ちに、上記の従来方法における４０
０〜８００℃の還元温度に比して相対的に低い２００〜
５００℃の温度で還元処理を施すと、
上記酸化物粉末の素地を形成していた主体のＮｉＯがＮ
ｉに還元され、かつ上記環状複合酸化物相が微細なＡｇ
２Ｏ３を主体とする環状硬質相に変化するようになり、
この結果得られたＮｉ合金粉末は、相対的にＡｇ２Ｏ３
の含有割合が高いので、これから焼結体を製造した場合
、耐摩耗性が飛躍的に向上するようになり、さらに上記
の通りＡｇ２Ｏ３粒が粉末表面に存在せず、内部に層を
なしてシェル状に分布するので、焼結性がｊＭなわれる
ことがなく、Ａ １１２０ ａの含有割合が高いにもか
かわらず、高強度の焼結体を製造することができるよう
になるという研究結果を得たのである。Therefore, from the above-mentioned viewpoint, the present inventors focused on the conventional Ni alloy powder described above in order to produce a sintered body that exhibits excellent wear resistance when used as a structural member of various drive devices. As a result of our research, we found that the Ni-Al1 alloy raw material powder used in the production of Ni alloy powder by the conventional method described above has
1.5~, which is a relatively large proportion compared to 1% Ap content
Using Ni-Al1 alloy powder containing 10% All, this Nj-A, Q alloy raw material powder was heated to an oxidation temperature of 1000 to 1300°C, which is much higher than the oxidation temperature of 450 to 600°C in the conventional method (Mai-4 Hakuhaku method). When the oxidation treatment is carried out at a temperature of °C, preferably in a powder fluidized state, the formed oxide powder is applied to a matrix mainly composed of nickel oxide (hereinafter referred to as NiO) in all cross sections passing through the center of the powder. ,
Between the center of the powder and the periphery of the powder, there is a cyclic composite oxide phase, in which fine Ni-1 composite oxide [hereinafter referred to as (Ni,,'l)0] aggregates in a ring shape. Fine (Ni, Ni,
l) It has a structure in which a cyclic composite oxide phase composed of O exists, and furthermore, this oxide powder is immediately treated with
Relatively low reduction temperature of 200 to 800℃
When the reduction treatment is performed at a temperature of 500°C, the main NiO that formed the base of the above oxide powder becomes N.
i, and the cyclic composite oxide phase is fine Ag
The Ni alloy powder obtained as a result of this changes into an annular hard phase mainly composed of 2O3.
Since the content ratio of Ag2O3 is high, when a sintered body is manufactured from this, the wear resistance will be dramatically improved.Furthermore, as mentioned above, Ag2O3 grains do not exist on the powder surface, and form a layer inside to form a shell. As the A 1120 a content is high, the sinterability does not deteriorate due to the distribution of A 1120 a, and the research results show that it is possible to produce a high-strength sintered body despite the high content of A 1120 a. It was.
この発明は、上記研究結果にもとづいてなされたもので
あって、
ＡＮ ： １．５〜】０％、
を含有し、残りがＮｉと不可避不純物からなるＮｉ −
Ａ１合金原料粉末に、
酸化性雰囲気中、１０００〜１３００℃の温度に、望ま
しくは流動化状態で加熱保持、
の条件で酸化処理を施して、主体がＮｉＯからなる素地
に、粉末中心部を通るあらゆる断面において、粉末中心
部と粉末周辺部との間に、微細な（Ｎｉ−Ａｌ２）０が
環状に凝集してなる環状複合酸化物相が存在する組織を
もった酸化物粉末を形成し、
引続いて、上記酸化物粉末に、
還元性雰囲気中、２００〜５００℃の温度に加熱保持、
の条件で還元処理を施して、上記酸化物粉末の素地をＮ
ｉ またはＮニーＡ１合金とすると共に、上記環状複合
酸化物相を微細な八１２０３を主体とする環状硬質相と
する、主要工程によってＮｉ合金粉末を製造する方法、
並びに、この方法で製造された、
１１： １．５〜９．２％、
酸素：１．３〜８．２％、
を含有し、残りがＮｉと不可避不純物からなる組成、並
びにＮｉまたはＮｉ−Ａｌ合金からなる素地に、粉末中
心部を通るあらゆる断面において、粉末中心部と粉末周
辺部との間に、環状に凝集した微細なＡ Ｉ ２０ ａ
を主体とする環状硬質相が存在する組織を有するＮｉ合
金粉末に特徴を有するものである。This invention was made based on the above research results, and includes AN: 1.5~]0%, with the remainder consisting of Ni and unavoidable impurities.
A1 alloy raw material powder is oxidized in an oxidizing atmosphere at a temperature of 1000 to 1300°C, preferably kept in a fluidized state, and passed through the center of the powder to a base mainly composed of NiO. Forming an oxide powder with a structure in which a cyclic composite oxide phase formed by agglomeration of fine (Ni-Al2)0 in a ring shape exists between the powder center and the powder periphery in every cross section, Subsequently, the oxide powder was subjected to a reduction treatment under the conditions of heating and holding at a temperature of 200 to 500°C in a reducing atmosphere to convert the base material of the oxide powder into N.
i or N Ni A1 alloy, and a method for producing Ni alloy powder by the main process, in which the above-mentioned cyclic composite oxide phase is a cyclic hard phase mainly composed of fine 81203, and the method produced by this method. , 11: 1.5 to 9.2%, oxygen: 1.3 to 8.2%, and the remainder is Ni and unavoidable impurities, and a powder is applied to the base consisting of Ni or Ni-Al alloy. In every cross section passing through the center, between the powder center and the powder periphery, fine A I 20 a aggregated in an annular shape
It is characterized by a Ni alloy powder having a structure in which an annular hard phase mainly composed of .
つぎに、この発明のＮｉ合金粉末およびこれの製造法に
おいて、成分組成および製造条件を上記の通りに限定し
た理由を説明する。Next, in the Ni alloy powder of the present invention and the method for producing the same, the reason why the component composition and production conditions are limited as described above will be explained.
（ａ）Ｎｉ合金粉末の成分組成
ＡＩＩは酸素と結合して粉末内部で層をなしてシェル状
に凝集分布する微細なＡｊｌ１２０３を形成し、粉末の
焼結性を損なうことなく、かつこれを原料粉末として用
いて製造された焼結体の耐摩耗性を著しく向上させる作
用があり、この場合Ａ、Ｉｌｌ含有量がきまれば必然的
に酸化処理で酸素含有ｍもきまるものであり、したがっ
てＡＮ８有量が１．５％未満になると酸素含有量も１．
３％未満となり、八１２０３の形成割合が不十分で所望
のすぐれた耐摩耗性を確保することができず、一方１）
含有量が９．２％を越えると、酸素含有量も８．２％を
越えて多くなり、この結果多量のＡ Ｉ ２０ ａが形
成されることになるので、Ａ Ｉ？ ２０ ａ粒の粗大
化が避けられず、相手攻撃性が現われるようになること
から、Ａｎ）含有量を１．５〜９．２％、酸素含有量を
１．３〜８．２％と定めた。(a) Component composition AII of the Ni alloy powder combines with oxygen to form fine Ajl1203 that forms a layer inside the powder and is aggregated and distributed in a shell shape, and can be used as a raw material without impairing the sinterability of the powder. It has the effect of significantly improving the wear resistance of the sintered compact produced as a powder, and in this case, if the A and Ill contents are determined, the oxygen content m will also be determined by the oxidation treatment. When the amount is less than 1.5%, the oxygen content is also 1.5%.
3%, the formation ratio of 81203 was insufficient and the desired excellent wear resistance could not be secured; on the other hand, 1)
When the content exceeds 9.2%, the oxygen content also increases beyond 8.2%, resulting in the formation of a large amount of A I 20 a, so that A I? 20 Since the coarsening of the a grains is unavoidable and the aggressiveness of the opponent appears, the An) content is set at 1.5 to 9.2% and the oxygen content is set at 1.3 to 8.2%. Ta.
（ｂ）Ｎｉ合金原料粉末の１含有量
Ａｌ含有量が１．５％未満では、酸化処理で形成される
（Ｎｉ．Ａｉｌ ） Ｏの粉末内部での環状凝集が十分
に行なわれず、この結果還元処理後の粉末表面に比較的
多量のＡ ＩＩ２０３が存在するようになって焼結性が
低下し、焼結体の強度低下の原因となり、一方Ａｇ含有
量が１０％を越えると、酸化処理で形成される（Ｎｊ、
Ａ、ｌｉｔ ） Ｏ並びに還元処理で形成されるＡ Ｉ
２０ ａの組径が粗大化し、これを焼結体とした場合
相手攻撃性が増すようになることから、Ａｌｌ含有量を
１．５〜ｌＯ％と定めた。(b) If the Al content of the Ni alloy raw material powder is less than 1.5%, the annular agglomeration of (Ni.Ail)O formed in the oxidation treatment within the powder will not occur sufficiently, resulting in reduction. A relatively large amount of A II203 is present on the powder surface after treatment, which reduces sinterability and causes a decrease in the strength of the sintered body.On the other hand, if the Ag content exceeds 10%, the oxidation treatment formed (Nj,
A, lit ) O and A I formed in the reduction process
Since the set diameter of 20a becomes coarse and if it is made into a sintered body, the aggressiveness against others increases, so the All content was determined to be 1.5 to 10%.
（ｃ） 酸化処理温度
その温度力筒０００℃未満では、（ＮＬＡＮ ）Ｏの環
状凝集が不十分であり、一方その温度力筒３００℃を越
えると、粉末を流動化しても粉末同志に融着が起り易く
なることから、その温度を１０００〜１３００℃と定め
た。(c) Oxidation treatment temperature If the temperature is less than 000°C, the annular agglomeration of (NLAN)O is insufficient, while if the temperature exceeds 300°C, the powders will fuse together even if they are fluidized. Since this tends to occur, the temperature was set at 1000 to 1300°C.
（ｄ）還元温度
その温度が２００℃未満では、酸化物粉末の還元に長時
間を要し、実用的でなく、一方その温度が５００℃を越
えると、還元処理で形成されるＡｇ２Ｏ３が粗大化する
ようになり、この結果焼結体の相手攻撃性が増すように
なることから、その温度を２００〜５００℃と定めた。(d) Reduction temperature If the temperature is less than 200°C, it takes a long time to reduce the oxide powder, making it impractical. On the other hand, if the temperature exceeds 500°C, Ag2O3 formed in the reduction process becomes coarse. As a result, the aggressiveness of the sintered body toward others increases, so the temperature was set at 200 to 500°C.
つぎに、この発明のＮｉ合金粉末およびその製造法を実
施例により具体的に説明する。Next, the Ni alloy powder of the present invention and its manufacturing method will be specifically explained using Examples.
それぞれ第１表に示される平均粒径およびＡΩ含有量の
Ｎｉ−Ａρ合金原料粉末を用意し、これらＮｉ−Ａｌ合
金原料粉末に、同じく第１表に示される条件で、酸化処
理、必要に応じてボールミル中での３時間のメカニカル
アロイング処理、および還元処理を施すことにより本発
明法１〜７および従来法１〜３を実施し、それぞれ本発
明Ｎｉ合金粉末１〜７および従来Ｎｉ合金粉末１〜３を
製造した。Ni-Aρ alloy raw material powders having the average particle diameter and AΩ content shown in Table 1 are prepared, and these Ni-Al alloy raw material powders are subjected to oxidation treatment and optionally under the conditions also shown in Table 1. Methods 1 to 7 of the present invention and conventional methods 1 to 3 were carried out by mechanical alloying treatment for 3 hours in a ball mill and reduction treatment to obtain Ni alloy powders of the present invention 1 to 7 and conventional Ni alloy powders, respectively. 1 to 3 were manufactured.
ついで、この結果得られた各種Ｎｉ合金粉末について、
成分組成を７１ｐｊ定すると共に、その断面組織を金属
顕微鏡（化率： １０００倍）を用いて観察し、さらに
本発明Ｎｉ合金粉末１〜７については、３０個の粉末の
それぞれの断面の中心部を通る任意直線上における粒径
、並びに環状硬質相の外径および内径を測定し、これら
の平均値を算出した。これらの結果を第２表に示した。Next, regarding the various Ni alloy powders obtained as a result,
In addition to determining the component composition of 71 pj, the cross-sectional structure was observed using a metallurgical microscope (magnification ratio: 1000 times), and for the Ni alloy powders 1 to 7 of the present invention, the central part of the cross section of each of the 30 powders was determined. The particle size on an arbitrary straight line passing through , and the outer diameter and inner diameter of the annular hard phase were measured, and the average value thereof was calculated. These results are shown in Table 2.
さらにこれらの各種のＮｉ合金粉末を原料粉末として用
い、これより５１ｏｎ／ｃ−の圧力で圧粉体にプレス成
形し、この圧粉体を、水素中、１３５０℃に３０分間保
持の条件で焼結して、断面＝ｌＯ關ＸＩＯ能、長さ：
５５ｍｍの寸法をもった焼結体を製造し、この焼結体に
ついて、強度を評価する目的て引張強さを測定すると共
に、摩耗試験を行なった。Furthermore, using these various Ni alloy powders as raw material powders, they were press-formed into a compact at a pressure of 51 on/c-, and this compact was sintered in hydrogen at 1350°C for 30 minutes. Therefore, cross section = lO xIO function, length:
A sintered body having a size of 55 mm was manufactured, and the tensile strength of this sintered body was measured for the purpose of evaluating the strength, and an abrasion test was conducted on the sintered body.
なお、摩耗試験は、回転軸を水平とした外径＝４０ｍｍ
Ｘ内径：３０ｍｍＸ長さ二１５ｍの鋳鉄（Ｆｅ１２）製
熱処理リング（硬さ： ＨＲＣ５０）の上方から、上記
焼結体から８＋＋＋ｍＸ８ｍｍＸ３５關の寸法に切出し
た試験片を水平に当接させ、この状態で上記試験片に５
ｋｇの荷重を垂直にかけ、前記リングを１．２ｍ／秒の
周速で回転させ、１０分後の試験片の最大摩耗深さを測
定することにより行なった。これらの結果も第２表に示
した。In addition, the wear test was performed using an outer diameter of 40 mm with the rotation axis horizontal.
A test piece cut out from the above sintered body into a size of 8+++ m x 8 mm x 35 m was horizontally brought into contact with a heat-treated ring made of cast iron (Fe12) (hardness: HRC50) with an inner diameter of 30 mm and a length of 215 m. 5 on the above test piece
The test was carried out by vertically applying a load of kg, rotating the ring at a circumferential speed of 1.2 m/sec, and measuring the maximum wear depth of the test piece after 10 minutes. These results are also shown in Table 2.
第１．２表に示される通り、本発明法１〜７によれば、
粉末内部に微細なＡｇ２Ｏ３が断面組織でみて環状に凝
集してなる環状硬質相が存在したＮｉ合金粉末（本発明
Ｎｉ合金粉末１〜７）を製造することができ、この本発
明Ｎｉ合金粉末１〜７は、上記の通りＡ、９含有量が高
いにもかかわらず、Ａ Ｉ ２０ ｓが粉末内部に封じ
込められた状態になっているので、これを原料粉末とし
て用いて焼結体を製造した場合、良好な焼結性が確保さ
れることから、高強度の焼結体を製造することができる
ばかりでなく、相対的に高含有量のＡ Ｉ？ ２０ ａ
によって、これより製造された焼結体は、相手材である
熱処理リングの損耗がきわめて少ない状態、すなわち相
手攻撃性が抑制された状態で、すぐれた耐摩耗性を示す
のに対して、従来法１〜３で製造されたＮｉ合金粉末（
従来Ｎｉ合金粉末１〜３）は、Ａ ｉｔ ２０ ａが粉
末全体に均一に分散分布した組織をもつので、Ａｆｉ含
有量が相対的に低いことと含まって、焼結性の低下はあ
まりなく、したがってほぼ同等の強度を有する焼結体を
製造することができるものの、耐摩耗性の面ではかなり
劣った結果しか示さないことが明らかである。As shown in Table 1.2, according to methods 1 to 7 of the present invention,
It is possible to produce Ni alloy powder (Ni alloy powders 1 to 7 of the present invention) in which there is a ring-shaped hard phase formed by agglomeration of fine Ag2O3 in a ring shape when viewed from the cross-sectional structure, and this Ni alloy powder 1 of the present invention can be produced. -7, despite the high A and 9 contents as described above, A I 20 s was confined inside the powder, so this was used as the raw material powder to produce the sintered body. In this case, since good sinterability is ensured, not only can a high-strength sintered body be manufactured, but also a relatively high content of AI? 20a
The sintered body produced by this method shows excellent wear resistance with extremely little wear on the heat-treated ring, which is the mating material, in other words, the aggressiveness to the mating material is suppressed. Ni alloy powder manufactured in 1 to 3 (
Conventional Ni alloy powders 1 to 3) have a structure in which A it 20 a is uniformly distributed throughout the powder, so the sinterability does not deteriorate much due to the relatively low Afi content. It is therefore clear that although it is possible to produce a sintered body with approximately the same strength, the results are considerably inferior in terms of wear resistance.
上述のように、この発明の方法によれば、相対的に多量
の微細なＡｇ２Ｏ３が粉末内部に層をなしてシェル状に
封じ込められたＮｉ合金粉末を製造することができ、し
たがってこの結果製造されたＮｉ合金粉末は焼結性がき
わめて良好で、これを用いて製造された焼結体は高強度
をもち、かつすぐれた耐摩耗性を示すようになるので、
これを用いて上記のほかに、ブロックリングやロッカー
アーム用チップ、ブレーキ用バット、さらにクラッチ板
などの各種駆動装置の構造部材を製造した場合、すぐれ
た性能を発揮するようになるなど工業上有用な効果がも
たらされるのである。As mentioned above, according to the method of the present invention, it is possible to produce a Ni alloy powder in which a relatively large amount of fine Ag2O3 forms a layer inside the powder and is confined in a shell shape, and thus the produced The Ni alloy powder has extremely good sintering properties, and the sintered bodies manufactured using it have high strength and excellent wear resistance.
In addition to the above, when this is used to manufacture structural members of various drive devices such as block rings, rocker arm tips, brake butts, and clutch plates, it exhibits excellent performance and is industrially useful. This brings about a great effect.
Claims (3)
びにＮｉまたはＮｉ−Ａｌ合金からなる素地に、粉末中
心部を通るあらゆる断面において、粉末中心部と粉末周
辺部との間に、環状に凝集した微細な酸化アルミニウム
を主体とする環状硬質相が存在する組織、を有すること
を特徴とするＮｉ合金粉末。(1) Contains Al: 1.5 to 9.2% by weight, Oxygen: 1.3 to 8.2% by weight, and the remainder is Ni and unavoidable impurities, and Ni or Ni-Al alloy. The base material is characterized by having a structure in which a ring-shaped hard phase mainly composed of fine aluminum oxide agglomerated in an annular shape exists between the powder center and the powder periphery in every cross section passing through the powder center. Ni alloy powder.
ｌ合金原料粉末に、 酸化性雰囲気中、１０００〜１３００℃の温度に加熱保
持、 の条件で酸化処理を施して、主体が酸化ニッケルからな
る素地に、粉末中心部を通るあらゆる断面において、粉
末中心部と粉末周辺部との間に、微細なＮｉ−Ａｌ複合
酸化物が環状に凝集してなる環状複合酸化物相が存在す
る組織をもった酸化物粉末を形成し、 ついで、上記酸化物粉末に、 還元性雰囲気中、２００〜５００℃の温度に加熱保持、 の条件で還元処理を施して、上記酸化物粉末の素地をＮ
ｉまたはＮｉ−Ａｌ合金とすると共に、上記環状複合酸
化物相を微細な酸化アルミニウムで構成された環状硬質
相とすることを特徴とするＮｉ合金粉末の製造法。(2) Al: Ni-A containing 1.5 to 10% by weight, with the remainder consisting of Ni and unavoidable impurities
l Alloy raw material powder is subjected to oxidation treatment under the conditions of heating and holding at a temperature of 1000 to 1300℃ in an oxidizing atmosphere, and the powder center is An oxide powder having a structure in which a cyclic composite oxide phase formed by agglomerating fine Ni-Al composite oxides in a ring shape is formed between the part and the peripheral part of the powder, and then the oxide powder is Then, in a reducing atmosphere, heat and hold at a temperature of 200 to 500 ° C. A reduction treatment was performed under the following conditions to transform the base of the oxide powder into N.
A method for producing a Ni alloy powder, characterized in that the cyclic composite oxide phase is a cyclic hard phase composed of fine aluminum oxide.
流動化させながら行なわれることを特徴とする上記特許
請求の範囲第（２）項記載のＮｉ合金粉末の製造法。(3) The method for producing Ni alloy powder according to claim (2), wherein the oxidation treatment is performed while fluidizing the Ni-Al alloy raw material powder.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2192089A JP2748667B2 (en) | 1990-07-20 | 1990-07-20 | Ni alloy powder and method for producing the same |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2192089A JP2748667B2 (en) | 1990-07-20 | 1990-07-20 | Ni alloy powder and method for producing the same |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH0480302A true JPH0480302A (en) | 1992-03-13 |
| JP2748667B2 JP2748667B2 (en) | 1998-05-13 |
Family
ID=16285469
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2192089A Expired - Lifetime JP2748667B2 (en) | 1990-07-20 | 1990-07-20 | Ni alloy powder and method for producing the same |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2748667B2 (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2008072957A (en) * | 2006-09-21 | 2008-04-03 | Kubota Corp | Support apparatus for farm equipment |
| JP5111601B2 (en) * | 2008-03-07 | 2013-01-09 | 株式会社日立メディコ | Ultrasonic imaging device |
| WO2017188088A1 (en) * | 2016-04-28 | 2017-11-02 | 住友電気工業株式会社 | Alloy powder, sintered body, method for producing alloy powder and method for producing sintered body |
| RU2686831C1 (en) * | 2018-03-22 | 2019-04-30 | Федеральное государственное унитарное предприятие "Всероссийский научно-исследовательский институт авиационных материалов" (ФГУП "ВИАМ") | Intermetallide matrix based metal-ceramic composite material and its production method |
-
1990
- 1990-07-20 JP JP2192089A patent/JP2748667B2/en not_active Expired - Lifetime
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2008072957A (en) * | 2006-09-21 | 2008-04-03 | Kubota Corp | Support apparatus for farm equipment |
| JP5111601B2 (en) * | 2008-03-07 | 2013-01-09 | 株式会社日立メディコ | Ultrasonic imaging device |
| WO2017188088A1 (en) * | 2016-04-28 | 2017-11-02 | 住友電気工業株式会社 | Alloy powder, sintered body, method for producing alloy powder and method for producing sintered body |
| CN109070207A (en) * | 2016-04-28 | 2018-12-21 | 住友电气工业株式会社 | Alloy powder, sintered body, the method for manufacturing alloy powder and the method for manufacturing sintered body |
| US11045872B2 (en) | 2016-04-28 | 2021-06-29 | Sumitomo Electric Industries, Ltd. | Alloy powder, sintered material, method for producing alloy powder, and method for producing sintered material |
| RU2686831C1 (en) * | 2018-03-22 | 2019-04-30 | Федеральное государственное унитарное предприятие "Всероссийский научно-исследовательский институт авиационных материалов" (ФГУП "ВИАМ") | Intermetallide matrix based metal-ceramic composite material and its production method |
Also Published As
| Publication number | Publication date |
|---|---|
| JP2748667B2 (en) | 1998-05-13 |
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