JPH01215944A - Valve seat made of ni-al sintered alloy and its manufacture - Google Patents
Valve seat made of ni-al sintered alloy and its manufactureInfo
- Publication number
- JPH01215944A JPH01215944A JP3924688A JP3924688A JPH01215944A JP H01215944 A JPH01215944 A JP H01215944A JP 3924688 A JP3924688 A JP 3924688A JP 3924688 A JP3924688 A JP 3924688A JP H01215944 A JPH01215944 A JP H01215944A
- Authority
- JP
- Japan
- Prior art keywords
- powder
- valve seat
- weight
- alloy
- sintered alloy
- 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
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 4
- 229910045601 alloy Inorganic materials 0.000 title claims description 19
- 239000000956 alloy Substances 0.000 title claims description 19
- 239000000843 powder Substances 0.000 claims abstract description 26
- 229910000990 Ni alloy Inorganic materials 0.000 claims abstract description 10
- 239000011812 mixed powder Substances 0.000 claims abstract description 7
- 239000000203 mixture Substances 0.000 claims abstract description 7
- 238000000034 method Methods 0.000 claims abstract description 6
- 239000002245 particle Substances 0.000 claims description 12
- 229910003310 Ni-Al Inorganic materials 0.000 claims description 3
- 230000001590 oxidative effect Effects 0.000 claims description 3
- 238000007711 solidification Methods 0.000 claims 1
- 230000008023 solidification Effects 0.000 claims 1
- 229910052742 iron Inorganic materials 0.000 abstract description 11
- 239000000463 material Substances 0.000 abstract description 10
- 238000005245 sintering Methods 0.000 abstract description 7
- 238000002156 mixing Methods 0.000 abstract description 2
- 238000000465 moulding Methods 0.000 abstract 3
- 230000001105 regulatory effect Effects 0.000 abstract 2
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 27
- 229910000765 intermetallic Inorganic materials 0.000 description 8
- 238000002485 combustion reaction Methods 0.000 description 7
- 230000000694 effects Effects 0.000 description 7
- 238000004663 powder metallurgy Methods 0.000 description 4
- 239000012188 paraffin wax Substances 0.000 description 3
- 239000011230 binding agent Substances 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 239000002994 raw material Substances 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- DSSYKIVIOFKYAU-XCBNKYQSSA-N (R)-camphor Chemical compound C1C[C@@]2(C)C(=O)C[C@@H]1C2(C)C DSSYKIVIOFKYAU-XCBNKYQSSA-N 0.000 description 1
- 229910018507 Al—Ni Inorganic materials 0.000 description 1
- 241000723346 Cinnamomum camphora Species 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- 229910001347 Stellite Inorganic materials 0.000 description 1
- 229960000846 camphor Drugs 0.000 description 1
- 229930008380 camphor Natural products 0.000 description 1
- AHICWQREWHDHHF-UHFFFAOYSA-N chromium;cobalt;iron;manganese;methane;molybdenum;nickel;silicon;tungsten Chemical compound C.[Si].[Cr].[Mn].[Fe].[Co].[Ni].[Mo].[W] AHICWQREWHDHHF-UHFFFAOYSA-N 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 239000010949 copper Substances 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000001125 extrusion Methods 0.000 description 1
- 238000005242 forging Methods 0.000 description 1
- 238000001192 hot extrusion Methods 0.000 description 1
- 229910052739 hydrogen Inorganic materials 0.000 description 1
- 239000001257 hydrogen Substances 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 230000007774 longterm Effects 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 238000007665 sagging Methods 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
Landscapes
- Powder Metallurgy (AREA)
Abstract
Description
【発明の詳細な説明】 〔産業上の利用分野〕 本発明は内燃機関に使用されるバルブシートに関する。[Detailed description of the invention] [Industrial application field] The present invention relates to a valve seat used in an internal combustion engine.
従来から内燃機関に使用されているバルブシート（弁座
）の材料としては、５ＵＨ−４等の耐熱鋼を代表とする
鉄系合金が大部分であった。Conventionally, most of the materials for valve seats used in internal combustion engines have been iron-based alloys, typified by heat-resistant steel such as 5UH-4.
又、鉄系合金を用いて各種の改良を加えた内燃機関用バ
ルブシートも知られている。例えば、特開昭６０−１３
０５５号公報及び特開昭６０−１３０６２号公報には、
２層構造にすることにより耐熱性を高めたバルブシート
が開示されている。特開昭６１−５０５号公報及び特開
昭６１−５６１号公報には、２層構造のバルブシートに
銅を溶浸して熱伝導性を改善したものが記載されている
。更に、特開昭６１−１６５２３０号公報及び特開昭６
２−５２６５０号公報には、Ｏｒの含有量が多く且つそ
の一部が炭化物等の硬質粒子として分散した鉄系合金か
らなるバルブシートが開示されている。In addition, valve seats for internal combustion engines that use iron-based alloys and have various improvements are also known. For example, JP-A-60-13
No. 055 and JP-A-60-13062,
A valve seat with improved heat resistance by having a two-layer structure is disclosed. JP-A-61-505 and JP-A-61-561 disclose a valve seat having a two-layer structure in which copper is infiltrated to improve thermal conductivity. Furthermore, JP-A-61-165230 and JP-A-6
Japanese Patent No. 2-52650 discloses a valve seat made of an iron-based alloy containing a large amount of Or, some of which is dispersed as hard particles such as carbide.
しかし、従来のバルブシートに用いていた鉄系合金は温
度が５００Ｃを超えると急激に強度が低下するため、長
期間の使用に耐えられなかった。However, the iron-based alloys used in conventional valve seats suddenly lose their strength when the temperature exceeds 500C, so they cannot withstand long-term use.
即ち、高出力・高負荷エンジンのように高性能な内燃機
関でバルブシートが５００Ｃ以上の温度に曝されると「
へたり」が生じる等の問題があった。In other words, when a valve seat is exposed to a temperature of 500C or higher in a high-performance internal combustion engine such as a high-output, high-load engine,
There were problems such as "sagging".
従来の鉄系合金からなるバルブシートは、上記の如く高
温強度に制約があるため、最近の高温で作動する高性能
な内燃機関においては耐熱性が不足してきている現状で
ある。Conventional valve seats made of iron-based alloys are limited in their high-temperature strength as described above, and therefore their heat resistance is currently insufficient in recent high-performance internal combustion engines that operate at high temperatures.
鉄系合金以外でバルブシートに使用される材料としてＣ
ｏをベースにしたステライトがあるが、ベースとなるＧ
ｏが高価であるためバルブシート自体が非常に高価格に
なる欠点がある。C as a material other than iron-based alloys used for valve seats
There is a stellite based on o, but the base is G
Since o is expensive, there is a drawback that the valve seat itself is very expensive.
本発明はこのような現状に鑑み、バルブシートが５００
１？以上の高温に曝される高性能な内燃機関においても
長期間に亘って使用できるような優れた高温強度を有す
るバルブシートを安価に提供することを目的とするもの
である。In view of the current situation, the present invention has been developed to reduce the number of valve seats to 500
1? The object of the present invention is to provide a valve seat at a low cost that has excellent high-temperature strength and can be used for a long period of time even in high-performance internal combustion engines exposed to high temperatures.
本発明のバルブシートはＮｉ−Ａｌ系焼結合金からなる
ものであって、９〜１３重量％のＡｌと、６〜１６重量
％のＦｅと、０．０１〜０．１重量％のＢと、残部のＮ
ｉとからなり、真密度比が９５％以上であって、５００
′Ｃでの降伏応力が４００ ＭＰａ以上であることを特
徴としている。The valve seat of the present invention is made of a Ni-Al based sintered alloy, and contains 9 to 13% by weight of Al, 6 to 16% by weight of Fe, and 0.01 to 0.1% by weight of B. , remainder N
i, the true density ratio is 95% or more, and 500
It is characterized by a yield stress of 400 MPa or more at 'C.
又、本発明のＮｉ−Ａ／！系焼結合金からなるバルブシ
ートの製造方法は粉末冶金法によるものであり、粒径が
１００メツシュ以下のｌ！−Ｂ−Ｎｉ合金粉末と粒径が
２００メツシュ以下のＦｅ粉末とを、最終組成が９〜１
３重量％のＡｌと、６〜１６重量％のＦｅと、０．０１
〜０．１重量％のＢと、残部のＮｉとになるように混合
し、この混合粉末の成形体を真空中又は非酸化性雰囲気
中（こおいて１１００〜１３００ Ｃの温度で焼結した
後、真密度比９５％以上に再圧縮することを特徴として
いる。Moreover, Ni-A/! of the present invention! The manufacturing method of the valve seat made of the sintered alloy is based on the powder metallurgy method, and the particle size is 100 mesh or less. -B-Ni alloy powder and Fe powder with a particle size of 200 mesh or less are combined to have a final composition of 9 to 1
3 wt% Al, 6-16 wt% Fe, 0.01
~0.1% by weight of B and the remainder of Ni were mixed, and a molded body of this mixed powder was sintered in a vacuum or in a non-oxidizing atmosphere (here, at a temperature of 1100 to 1300 C). After that, it is characterized by being recompressed to a true density ratio of 95% or more.
混合粉末の成形体を形成するためには、通常の如く混合
粉末にパラフィン、カンファー等の結合剤を２〜５重量
％添加して加圧成形する。この結合剤は焼結前に５００
〜９００Ｃで加熱することにより除去できる。In order to form a molded body of the mixed powder, 2 to 5% by weight of a binder such as paraffin or camphor is added to the mixed powder and then pressure molded. This binder is 500%
It can be removed by heating at ~900C.
又、混合粉末を上記最終組成に調製するためには、Ａ／
ニーＥ−Ｎｉ合金粉末の組成をＡ１９．１〜１５．５重
量％、Ｂｏ、０１〜０．１２重量％及び残部Ｎｉとする
ことが望ましい。In addition, in order to prepare the mixed powder to the above final composition, A/
It is desirable that the composition of the Ni E-Ni alloy powder be A19.1 to 15.5% by weight, Bo 01 to 0.12% by weight, and the balance Ni.
なお、本発明に係るＡ４−Ｎｉ系焼結合金は、その性質
Ｇこ影響を与えない範囲で不可避不純物を含み得ること
は云うまでもない。It goes without saying that the A4-Ni based sintered alloy according to the present invention may contain unavoidable impurities within a range that does not affect its properties.
本発明のバルブシートは、Ａ４−Ｎｉ系金属間化合物を
ベースとするＡ／！−Ｎｉ系焼結合金からなる。このｊ
ｋ４−Ｎｉ系金属間化合物は非常に高硬度であり、従来
は粉末冶金材料の分散粒子として使用されていた。然る
に本発明においては、この１−Ｎｉ系金属間化合物は耐
熱性が高いうえに耐摩耗性にも優れている点に着目し、
Ｈ工Ｐや熱間押出などの粉末冶金技術を利用して、ｌ！
−Ｎｉ系金属間化合物自体ヲベースとしてバルブシート
を構成したものである。The valve seat of the present invention is an A/! valve seat based on an A4-Ni intermetallic compound. - Made of Ni-based sintered alloy. This j
K4-Ni intermetallic compounds have extremely high hardness and have conventionally been used as dispersed particles in powder metallurgy materials. However, in the present invention, we focused on the fact that this 1-Ni-based intermetallic compound has high heat resistance and excellent wear resistance.
Using powder metallurgy techniques such as H-P and hot extrusion, l!
-The valve seat is constructed using the Ni-based intermetallic compound itself as a base.
しかも、高出力・高負荷エンジンのように高性能な内燃
機関でバルブシートが５００Ｃ以上の温度に曝されても
「へたり」が生じないためには、５００Ｃでの降伏応力
が４００ ＭＰａ以上である必要があることが判明した
が、本発明のバルブシートはこの条件を充たすものであ
る。Furthermore, in order for the valve seat to not "sag" even when exposed to temperatures of 500C or higher in a high-performance internal combustion engine such as a high-output, high-load engine, the yield stress at 500C must be 400 MPa or higher. The valve seat of the present invention satisfies this condition.
構成元素のうちＡｌはＮｉと共に金属間化合物を形成す
るが、Ａｌが９重量％未満では金属間化合物の形成に不
足であり、１３重量％を超えると金属間化合物を形成し
ないＡ’７が増加するので、合金の特性が劣化する。Ｆ
ｅはＡｌ−Ｎｉ系金属間化合物のＡｌ又はＮｉと置換す
る形で固溶し、延性を改善する効果を有する。しかし、
Ｆｅが６重量％未満では延性改善の効果が現われず、１
６重量％を超えると加工性の低下が大さくなる。ＢもＦ
ｅと同様に延性を改善するが、０゜０１重量％未満では
その効果がなく、０．１重量％を超えても効果がもはや
大きくならない。Among the constituent elements, Al forms an intermetallic compound together with Ni, but if Al is less than 9% by weight, it is insufficient to form an intermetallic compound, and if it exceeds 13% by weight, A'7, which does not form an intermetallic compound, increases. As a result, the properties of the alloy deteriorate. F
e forms a solid solution by replacing Al or Ni in the Al-Ni intermetallic compound, and has the effect of improving ductility. but,
If Fe is less than 6% by weight, the effect of improving ductility does not appear, and 1
If it exceeds 6% by weight, the deterioration in processability will be significant. B and F
Like e, it improves ductility, but if it is less than 0.01% by weight, it has no effect, and if it exceeds 0.1% by weight, the effect is no longer significant.
本発明のバルブシートは粉末冶金法により製造する。Ｎ
ｉ、Ａｌ及びＢについてはＡｌ−Ｂ−Ｎｉ合金粉末を用
い、Ｆｅは単独の粉末として添加する。単独とは合金化
していないという意味であり、原料粉末として１−Ｂ−
Ｎｉ合金粉末の表面に微細なＦｅ粉末が付着した拡散結
合粉末を用いることもできる。Ｆｅ単独の粉末を用いる
ことで、焼結時にＦｅがＡｌ−Ｂ−Ｎｉ合金粉末中に拡
散し、これによって焼結が促進され粉末の結合が強化さ
れる。The valve seat of the present invention is manufactured by powder metallurgy. N
For i, Al and B, Al-B-Ni alloy powder is used, and Fe is added as a single powder. Single means that it is not alloyed, and 1-B- is used as a raw material powder.
Diffusion-bonded powder in which fine Fe powder is attached to the surface of Ni alloy powder can also be used. By using a powder containing only Fe, Fe diffuses into the Al-B-Ni alloy powder during sintering, thereby promoting sintering and strengthening the bond between the powders.
従ってＡ４−Ｂ−Ｎｉ合金粉末との接触界面を増加させ
、拡散焼結を促進させるために、Ｆｅ粉末の粒径は微細
であることが必要であり、この粒径が２００メツシュを
超えて大きくなると降伏応力などの所望の特性が得られ
ない。又、Ａｚ−Ｂ−４ｉ合金粉末の粒径も１００メツ
シュ以下とすべきであり、これより大さいと粉末の成形
性が低下すると共に、上記したＦｅの固溶が不充分とな
る。Therefore, in order to increase the contact interface with the A4-B-Ni alloy powder and promote diffusion sintering, the particle size of the Fe powder needs to be fine, and if the particle size exceeds 200 mesh, it is necessary to In this case, desired properties such as yield stress cannot be obtained. Further, the particle size of the Az-B-4i alloy powder should also be 100 mesh or less; if it is larger than this, the moldability of the powder will decrease and the solid solution of Fe described above will become insufficient.
原料粉末の焼結は真空中又は非酸化性雰囲気中１１００
〜１３００ Ｃで行なう。１１００ Ｃ未満の温度では
焼結が不充分となり、１３００Ｃを超えても効果の改善
がなく不経済である。The raw material powder is sintered in a vacuum or in a non-oxidizing atmosphere.
Perform at ~1300C. If the temperature is less than 1100 C, sintering will be insufficient, and if the temperature exceeds 1300 C, the effect will not improve and it will be uneconomical.
又、焼結後に再圧縮を行ない真密度比を９５％以上店す
る。真密度比が９５％未満では高温強度が不足し、所望
の降伏応力などが得られない。再圧縮の手段は、鍛造、
押出、Ｈ工Ｐ等の通常の方法で良い。Further, after sintering, recompression is performed to increase the true density ratio to 95% or more. If the true density ratio is less than 95%, the high temperature strength will be insufficient and the desired yield stress etc. will not be obtained. The means of recompression is forging,
Conventional methods such as extrusion and H-processing may be used.
実施例１
粒径が１００メツシュ以下のＡ４−Ｂ−Ｎｉ合金粉末と
粒径が２００メツシュ以下のＦｅ粉末とを、最終組成が
１１重量％のＡｌ、１０重量％のＦｅ、０．０５重量％
のＢ及び残部のＮｉとになるように混合し、この混合粉
末に対して３重量％のパラフィンを添加混合した後、金
型で圧力Ｔｔｏｎ膚で成形した。Example 1 A4-B-Ni alloy powder with a particle size of 100 mesh or less and Fe powder with a particle size of 200 mesh or less were combined in a final composition of 11% by weight of Al, 10% by weight of Fe, and 0.05% by weight.
After adding and mixing 3% by weight of paraffin to this mixed powder, it was molded using a mold under a pressure of Tton.
この成形体を水素雰囲気中８００Ｃに加熱してパラフィ
ンを除去し、次に真空中において１２００ ｔｒの温度
で焼結した。得られた焼結体を金型で再圧縮して真密度
比９８％とし、更に真空中１０００ Ｃで２時間加熱し
て焼鈍した。The compact was heated to 800 C in a hydrogen atmosphere to remove paraffin, and then sintered in vacuum at a temperature of 1200 tr. The obtained sintered body was recompressed in a mold to a true density ratio of 98%, and further annealed by heating at 1000 C in vacuum for 2 hours.
比較のために、Ｆｅ粉末の粒径を２００メツシュよりも
粗くした以外は実施例１と同じ方法により、同一組成で
同一真密度比の素材を製造した。For comparison, materials with the same composition and true density ratio were manufactured by the same method as in Example 1 except that the particle size of the Fe powder was made coarser than 200 mesh.
これら２種類の素材からテストピースを切す出し、５０
０Ｃに保持した状態で圧縮降伏応力を測定したところ、
本発明の素材は４５０ ＭＰａであったのに対し、比較
例の素材は３９０ ＭＰａでしかなかった。Cut test pieces from these two types of materials, 50
When the compressive yield stress was measured while being held at 0C,
The material of the present invention had a strength of 450 MPa, while the material of the comparative example had a strength of only 390 MPa.
実施例２
実施例１と同様の方法であるが、焼結後の再圧縮の圧力
を変えることにより、真密度比を夫々９１％、９３％、
９５％及び９７％とした素材を製造した。Example 2 The same method as Example 1 was used, but by changing the recompression pressure after sintering, the true density ratio was changed to 91%, 93%, and 93%, respectively.
Materials with a concentration of 95% and 97% were produced.
各素材について５００Ｃでの圧縮降伏応力を測定し結果
を図面に示した。この図面から９５％未満の真密度比で
は４００ ＭＰａ以上の降伏応力が得られないことが判
る。The compressive yield stress at 500C was measured for each material, and the results are shown in the drawings. It can be seen from this drawing that a yield stress of 400 MPa or more cannot be obtained with a true density ratio of less than 95%.
本発明によれば、従来の鉄系合金製バルブシートに比べ
て高温強度に優れたＮｉ−Ａ４系焼結合金製バルブシー
トを提供することができる。従って、本発明はバルブシ
ートが従来にない５００Ｃ以上の高温に曝される高負荷
・高出力エンジン等に特に有効である。According to the present invention, it is possible to provide a Ni-A4-based sintered alloy valve seat that has superior high-temperature strength compared to conventional iron-based alloy valve seats. Therefore, the present invention is particularly effective in high-load, high-output engines where valve seats are exposed to unprecedented high temperatures of 500C or higher.
図面はバルブシートを構成するＮｉ−Ａｌ系焼結合金の
真密度比と５００Ｃでの降伏応力との関係を示すグラフ
である。
出願人 住友電気工業株式会社The drawing is a graph showing the relationship between the true density ratio of the Ni--Al based sintered alloy constituting the valve seat and the yield stress at 500C. Applicant: Sumitomo Electric Industries, Ltd.
Claims (2)
と、０．０１〜０．１重量％のＢと、残部のＮｉとから
なり、真密度比が９５％以上であつて、５００℃での降
伏応力が４００ＭＰａ以上であることを特徴とするＮｉ
−Ａｌ系焼結合金製バルブシート。(1) 9-13% by weight of Al and 6-16% by weight of Fe
, 0.01 to 0.1% by weight of B, and the balance of Ni, which has a true density ratio of 95% or more and a yield stress of 400 MPa or more at 500°C.
-Al-based sintered alloy valve seat.
粉末と粒径が２００メッシュ以下のＦｅ粉末とを、最終
組成が９〜１３重量％のＡｌと、６〜１６重量％のＦｅ
と、０．０１〜０．１重量％のＢと、残部のＮｉとにな
るように混合し、この混合粉末の成形体を真空中又は非
酸化性雰囲気中において１１００〜１３００℃の温度で
焼結した後、真密度比９５％以上に再圧縮することを特
徴とするＮｉ−Ａｌ系焼結合金製バルブシートの製造方
法。(2) Al-B-Ni alloy powder with a particle size of 100 mesh or less and Fe powder with a particle size of 200 mesh or less have a final composition of 9 to 13% by weight of Al and 6 to 16% by weight of Fe.
, 0.01 to 0.1% by weight of B, and the balance of Ni, and a compact of this mixed powder is sintered at a temperature of 1100 to 1300°C in vacuum or in a non-oxidizing atmosphere. A method for manufacturing a valve seat made of a Ni-Al based sintered alloy, which comprises recompressing the Ni-Al based sintered alloy to a true density ratio of 95% or more after solidification.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3924688A JPH01215944A (en) | 1988-02-22 | 1988-02-22 | Valve seat made of ni-al sintered alloy and its manufacture |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3924688A JPH01215944A (en) | 1988-02-22 | 1988-02-22 | Valve seat made of ni-al sintered alloy and its manufacture |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH01215944A true JPH01215944A (en) | 1989-08-29 |
Family
ID=12547775
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP3924688A Pending JPH01215944A (en) | 1988-02-22 | 1988-02-22 | Valve seat made of ni-al sintered alloy and its manufacture |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH01215944A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1295361C (en) * | 2005-11-09 | 2007-01-17 | 锦州市催化剂厂 | Production method of regenerating metal alloy from imperfect fine powder using nickel aluminium alloy catalyst |
-
1988
- 1988-02-22 JP JP3924688A patent/JPH01215944A/en active Pending
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1295361C (en) * | 2005-11-09 | 2007-01-17 | 锦州市催化剂厂 | Production method of regenerating metal alloy from imperfect fine powder using nickel aluminium alloy catalyst |
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