JPS6092409A - Manufacture of fe-cr-co alloy powder - Google Patents
Manufacture of fe-cr-co alloy powderInfo
- Publication number
- JPS6092409A JPS6092409A JP20000083A JP20000083A JPS6092409A JP S6092409 A JPS6092409 A JP S6092409A JP 20000083 A JP20000083 A JP 20000083A JP 20000083 A JP20000083 A JP 20000083A JP S6092409 A JPS6092409 A JP S6092409A
- Authority
- JP
- Japan
- Prior art keywords
- alloy
- alloy powder
- powder
- sintering
- maximum energy
- 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
- 239000000843 powder Substances 0.000 title claims abstract description 35
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 13
- 229910000531 Co alloy Inorganic materials 0.000 title description 2
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 41
- 239000000956 alloy Substances 0.000 claims abstract description 41
- 229910017110 Fe—Cr—Co Inorganic materials 0.000 claims abstract description 12
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 6
- 229910052742 iron Inorganic materials 0.000 claims abstract description 6
- 238000000227 grinding Methods 0.000 claims abstract description 4
- 238000000889 atomisation Methods 0.000 claims description 4
- 229910018663 Mn O Inorganic materials 0.000 claims 1
- 238000000034 method Methods 0.000 abstract description 24
- 238000005245 sintering Methods 0.000 abstract description 13
- 229910052748 manganese Inorganic materials 0.000 abstract description 7
- 239000000203 mixture Substances 0.000 abstract description 4
- 229910001004 magnetic alloy Inorganic materials 0.000 description 5
- 239000002184 metal Substances 0.000 description 4
- 229910052751 metal Inorganic materials 0.000 description 4
- 238000000465 moulding Methods 0.000 description 4
- 230000000694 effects Effects 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- 239000002245 particle Substances 0.000 description 3
- 238000010298 pulverizing process Methods 0.000 description 3
- 238000005096 rolling process Methods 0.000 description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- 229910017060 Fe Cr Inorganic materials 0.000 description 2
- 229910002544 Fe-Cr Inorganic materials 0.000 description 2
- 229910017112 Fe—C Inorganic materials 0.000 description 2
- 230000032683 aging Effects 0.000 description 2
- UPHIPHFJVNKLMR-UHFFFAOYSA-N chromium iron Chemical compound [Cr].[Fe] UPHIPHFJVNKLMR-UHFFFAOYSA-N 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 230000004907 flux Effects 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 2
- 238000009692 water atomization Methods 0.000 description 2
- 229910000808 amorphous metal alloy Inorganic materials 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
- 238000009833 condensation Methods 0.000 description 1
- 230000005494 condensation Effects 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000004090 dissolution Methods 0.000 description 1
- 238000005868 electrolysis reaction Methods 0.000 description 1
- 238000005242 forging Methods 0.000 description 1
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 1
- 239000010931 gold Substances 0.000 description 1
- 229910052737 gold Inorganic materials 0.000 description 1
- 238000001000 micrograph Methods 0.000 description 1
- 238000002156 mixing Methods 0.000 description 1
- 229910052757 nitrogen Inorganic materials 0.000 description 1
- 230000001590 oxidative effect Effects 0.000 description 1
- 238000004080 punching Methods 0.000 description 1
- 238000001330 spinodal decomposition reaction Methods 0.000 description 1
- 239000004575 stone Substances 0.000 description 1
- 238000005491 wire drawing Methods 0.000 description 1
Landscapes
- Manufacture Of Metal Powder And Suspensions Thereof (AREA)
Abstract
Description
【発明の詳細な説明】
本発明はスピノータ匂解型Ｆｅ −Ｃｒ −Ｃｏ系磁石
合金を焼結法により得るのに使用されるＦｅ−Ｃｒ−Ｃ
ｏ系合金粉末の製造方法に関するものである。DETAILED DESCRIPTION OF THE INVENTION The present invention relates to a Fe-Cr-C magnet alloy used to obtain a spinotatically decomposed type Fe-Cr-Co magnet alloy by a sintering method.
The present invention relates to a method for producing o-based alloy powder.
従来から、この種のスピノーダル分解型Ｆｅ −Ｃｒ
−Ｃｏ系磁石合金の製造方法として、Ｖ−！造法、圧延
法および焼結法が知られている。釣造法では容易に所望
形状の合金を得ることができる反面、小物製品をに造す
る場合は総合歩留が低く、また鋳物欠陥が生じ易く、複
雑形状製品では、多くの加工工程を必要とする欠点があ
る。Conventionally, this type of spinodal decomposition type Fe-Cr
- As a method for producing a Co-based magnetic alloy, V-! Manufacturing methods, rolling methods and sintering methods are known. While the fishing method can easily obtain alloys with desired shapes, when manufacturing small products, the overall yield is low and casting defects are likely to occur, and products with complex shapes require many processing steps. There are drawbacks to doing so.
また圧延法は、Ｆｅ −Ｃｒ −Ｃｏ系磁石合金（？！
Ｉえは特公昭５８−９８２７号公報参照）等の処性をも
つ材料にのみ適用できる方法であシ、打抜加工や線引加
工による小物、複雑形状製品あるいは板材、細丸棒等の
製造に優れる。しかし、反面鍛造、焼鈍、圧延等信の製
造方法にない複雑なプロセスが必要となる。これに対し
、焼結法（例えは特開昭５４−３３２０５号、同５６−
１３９６５７号、同５７−１６１５０号の各公報参照）
は総合歩留が高く小物、複雑形状製品の加工工程を大幅
に省略できる可能性があシ小物、複雑形状製品には適し
ている。In addition, the rolling method uses a Fe-Cr-Co magnetic alloy (?!
This method can only be applied to materials with processing properties such as Japanese Patent Publication No. 58-9827 (see Japanese Patent Publication No. 58-9827), and manufactures small items, complex-shaped products, plate materials, thin round bars, etc. by punching or wire drawing. Excellent in However, on the other hand, it requires complicated processes that are not available in other manufacturing methods such as forging, annealing, and rolling. On the other hand, sintering method (for example, JP-A-54-33205, JP-A-56-
(Refer to publications No. 139657 and No. 57-16150)
It has a high overall yield and has the potential to significantly omit processing steps for small and complex-shaped products, making it suitable for small and complex-shaped products.
焼結法を用いるためには、所望成分の金Ｉｊ４粉末を製
造する必要がち９、一般に金属粉末を製造する方法とし
ては、（１）機械的粉砕法、（２）還元による方法、（
ａ）電解による方法、（４）溶湯粉化による方法等があ
る。In order to use the sintering method, it is necessary to produce gold Ij4 powder with the desired components.9 Generally, methods for producing metal powder include (1) mechanical pulverization, (2) reduction method, (
There are a) a method by electrolysis, and (4) a method by pulverization of molten metal.
上述した延性を有するＦｅ −Ｃｒ −Ｃｏ系磁石合金
は磁気特性は良好であるが、機械的粉砕法では多大な時
…」と労力を要し粉末の製造が困難である１Ｆｅ −Ｃ
ｒ合金としてはｄ粉とし機械的粉砕を可能にする方法が
あるがその際のＣｒ量は４５チ以上と非常に高くする必
をがある。また還元による方法および電解による方法は
上記Ｆｅ −Ｃｒ −Ｃｏ 系合金のように多元系であ
る場合は不適である。The ductile Fe-Cr-Co magnetic alloy mentioned above has good magnetic properties, but mechanical crushing requires a lot of time and labor, making it difficult to produce powder.
There is a method of using d powder as the r alloy to enable mechanical pulverization, but in this case the Cr content must be very high, 45 or more. Further, the reduction method and the electrolytic method are unsuitable in the case of a multi-component system such as the above-mentioned Fe-Cr-Co alloy.
これに対し、ｍｈ粉化の方法によれば、比較的容易に所
望の金踊粉末が得られ、上記Ｆｅ −Ｃｒ −Ｃｏ系合
金粉末の製造に適する。On the other hand, according to the mh powdering method, the desired Konodori powder can be obtained relatively easily and is suitable for producing the Fe-Cr-Co alloy powder.
しかして、Ｆｅ −Ｃｒ −Ｃｏ系磁石合金の必須成分
であるＦｅ−、Ｃｒ、Ｇｏ、５ｔＳＴｉのみでアトマイ
ズ法によシ得られる合金粉末の形状は丸味を帯びた不定
形のものが大半であシ、そのため成形、焼結後の試料は
高密度になシに＜＜、その結果高特性化には難かしい面
を有していた。However, the shape of the alloy powder obtained by the atomization method using only Fe-, Cr, Go, and 5tSTi, which are the essential components of the Fe-Cr-Co magnetic alloy, is mostly rounded and amorphous. Therefore, the sample after molding and sintering had a high density, which made it difficult to improve the properties.
本発明の目的は、上記従来技術の欠点を解消し、焼結後
の密度を向上させることによシ、高特性のＦｅ −Ｃｒ
−Ｃｏ系焼結磁石が得られるＦｅ −Ｃｒ −Ｃ。The purpose of the present invention is to eliminate the drawbacks of the above-mentioned prior art and to improve the density after sintering, thereby achieving high properties of Fe-Cr.
-Fe-Cr-C from which a Co-based sintered magnet can be obtained.
系合金粉末の製造方法を提供することである。It is an object of the present invention to provide a method for manufacturing alloy powder.
本発明のＦｅ −Ｃｒ −Ｃｏ系合金粉末の製造方法は
、Ｆｅ、 Ｃｒ、 Ｃｏを主成分としかつＳｉ、Ｔｉの
他にＩＶｌｎおよび／またはＢを添加した合金の溶湯な
アトマイズ法によシ粉末化することを特徴としている。The method for producing the Fe-Cr-Co alloy powder of the present invention is to produce powder using a molten atomization method of an alloy containing Fe, Cr, and Co as main components and containing IVln and/or B in addition to Si and Ti. It is characterized by becoming
すなわち本発明者等が種々検討した結果、胤およびＢを
添加したＦｅ −Ｃｒ −Ｃｏ系合金を用いることによ
り、丸味を帯びた不定形合金粉末よシ球形に近い合金粉
末にすることが可能となり、この球状化したＦｅ −Ｃ
ｒ −Ｃｏ系合金粉末を用いて常法によシ焼結磁石を製
造すると焼結後のＭ［が向上し、理論密度比９６％以上
かつ最大エネルギー積３、５ Ｍ Ｇ Ｏｅ以上の焼結
磁石合金が得られることを見出した。In other words, as a result of various studies by the present inventors, by using a Fe-Cr-Co alloy to which Seed and B are added, it is possible to create an alloy powder that is closer to a spherical shape than a rounded amorphous alloy powder. , this spheroidized Fe-C
When a sintered magnet is manufactured by a conventional method using r-Co alloy powder, the M after sintering is improved, and the sintering has a theoretical density ratio of 96% or more and a maximum energy product of 3.5 M G Oe or more. It has been found that a magnetic alloy can be obtained.
また本発明においては、Ｆｅ−Ｃｒ−Ｃｏ系合金粉末と
して重重比でＣｒ １７〜４５チ、Ｃｏ ５〜３０チ、
ＳｉＯ，１〜５％、’Ｉ’ｉ ０．１〜５％、Ｍｎ ０
．１〜５％、Ｂｏ、１〜５％、残部実質的にＦｅからな
る組成のものが好ましい。その理由は次の通シである。In addition, in the present invention, the Fe-Cr-Co alloy powder has a weight ratio of Cr 17 to 45 inches, Co 5 to 30 inches,
SiO, 1-5%, 'I'i 0.1-5%, Mn 0
．． A preferred composition is 1 to 5% Bo, 1 to 5% Fe, and the remainder substantially Fe. The reason is as follows.
合金成分において、Ｃｒは保磁力に大きく影響し、１７
％未満では充分な保磁力が得られず、また４５％を越え
ると飽和磁束密度が低下して実用的でなくなる。Among alloy components, Cr has a large effect on coercive force, and 17
If it is less than 45%, a sufficient coercive force cannot be obtained, and if it exceeds 45%, the saturation magnetic flux density decreases, making it impractical.
ＣｏはＣｒと共に保磁力を増大させるものであるが、５
％未満では所望磁気特性が得られず、また３０％を越す
と熱処理条件が困難となる。Co increases the coercive force together with Cr, but 5
If it is less than 30%, the desired magnetic properties cannot be obtained, and if it exceeds 30%, the heat treatment conditions become difficult.
Ｓｉは湯の流動性を改善し、またＴｉは大気溶解時ある
いは焼結過程において真空中あるいは非酸化性芥囲気中
の倣瀘の窒素を固定させるため、各々０．１〜５％の添
加が有効である。Si improves the fluidity of hot water, and Ti fixes nitrogen in a vacuum or non-oxidizing atmosphere during atmospheric dissolution or during the sintering process, so it is recommended to add 0.1 to 5% of each. It is valid.
胤お・よびＢの重加は上記のＦｅ５ＣｒＳＣｏ、５ｉｓ
Ｔｉ元索と相互に反応して溶湯の表面張力を高める働き
を有し、そのためアトマイズ後得られる合金粉末を球状
化せしめるものであるが、その含有量が０．１％未満で
は添加による効呆は望めない。The weight of Tane and B is the above Fe5CrSCo, 5is
It has the effect of increasing the surface tension of the molten metal by interacting with the Ti base, and therefore makes the alloy powder obtained after atomization spheroidized, but if its content is less than 0.1%, the effect of its addition is low. I can't hope for that.
また５％を越えると磁気特性の劣化を引き匙こすことか
ら０．１〜５％の軛囲が良い。Moreover, if it exceeds 5%, the magnetic properties may deteriorate, so a range of 0.1 to 5% is preferable.
実施例ｌ
Ｃｏ１０％、Ｃｒ ２７％、Ｓｉ０．５％、Ｔｉ Ｏ，
５％、残部実質的にＦｅからなる組成になるように配合
した後、Ｍｎを０％（無添加）、０．１％、０．５％、
１チ、２％、３％、５％添加し、溶湯温厩 １７００〜
１８００℃においてＮ２中水アトマイズ法にて粒［１０
０ｍｅｓｈ以下の合金粉末を作製した。Example 1 Co10%, Cr27%, Si0.5%, TiO,
5%, and the remainder was blended so as to have a composition consisting essentially of Fe, and then Mn was added to 0% (no addition), 0.1%, 0.5%,
Add 1 g, 2%, 3%, 5%, warm molten metal 1700~
Particles [10
An alloy powder of 0 mesh or less was produced.
第１図（ａ）、（ｂ）にＭｎ無添加およびＭｎを０．５
％添加した場合に得られた合金粉末の顕微鏡写真を示す
。Figure 1 (a) and (b) show no Mn addition and Mn addition of 0.5
% of the alloy powder is shown.
この粉末を５ｔ／ｃＩ／ｌの成形圧で外径１３ ｇ 、
高さ１０Ｍの円柱状に成形し、この成形体を１０ Ｔｏ
ｒｒ以下の真号中で１４００℃の温度で９０分間涜結上
行った。その後９００℃で３０分間保持する俗体化処理
後、さらに６３０℃近坊で６０分間保持する等温磁場処
理を行い、続いて６１０℃から４７０℃まで４℃／ｈの
遠戚で冷却する時効処理を施した。This powder was molded under a molding pressure of 5t/cI/l to an outer diameter of 13g,
The molded body was molded into a cylindrical shape with a height of 10M, and the molded body was
Condensation was carried out at a temperature of 1400° C. for 90 minutes in a vacuum chamber with a temperature below rr. After that, after a secularization treatment held at 900°C for 30 minutes, an isothermal magnetic field treatment held at 630°C for 60 minutes, followed by an aging treatment where the temperature is cooled from 610°C to 470°C at a rate of 4°C/h. was applied.
第２図にこのようにして侍られたＦｅ −Ｃｒ −Ｃ。Fig. 2 shows Fe-Cr-C served in this way.
磁石の理論密度比と最大エネルギー積値とＭｎ添加量の
関係を示す。第２図から明らかなようにＭｎを添加する
ことにより理論履度比は９６チ以上に向上し、約０．５
〜５％間で飽和の傾向を示す。一方磁気特性はＭｎ１％
近傍で最大値を有することがわかった。The relationship between the theoretical density ratio of the magnet, the maximum energy product value, and the amount of Mn added is shown. As is clear from Fig. 2, by adding Mn, the theoretical wear ratio increases to more than 96 inches, which is about 0.5
It shows a tendency of saturation between ~5%. On the other hand, the magnetic properties are Mn1%
It was found that it has a maximum value in the vicinity.
実施例２
目標成分が００１０％、Ｃｒ ２７ ％、Ｓｔ Ｏ，５
％、Ｔｉ０１５チ、Ｍｎ １チ、へ部実負的にＦｅの組
成になるように配合した後、添加量を変化させてＢを添
加し、水７トマイズ法にて粒度１００ｍｅａｈ 以下の
合金粉末を作製しだ０この合金粉末を用いて実施例１と
同様の条件で成形、焼結および熱処理を行ってＦｅ −
Ｃｒ −Ｃｏ系焼結磁石を得た０第３図にＢ添加量とそ
の時得られたこの磁石の理論密度比および最大エネルギ
ー積の関係を示す。Example 2 Target components are 0010%, Cr 27%, St O,5
%, 15% Ti, 1% Mn, and 1% Ti, 1% Mn, and 1% Fe. After blending so as to have a negative composition of Fe, B was added by varying the amount added, and an alloy powder with a particle size of 100mah or less was produced using the water totomization method. Production: Using this alloy powder, molding, sintering and heat treatment were performed under the same conditions as in Example 1 to obtain Fe-
A Cr--Co based sintered magnet was obtained. Figure 3 shows the relationship between the amount of B added and the theoretical density ratio and maximum energy product of this magnet obtained at that time.
第３図から明らかなように、Ｂ添加量が０．１〜５チの
範囲で理論密度比９６チ以上、最大エネルギー積３．５
Ｍ Ｇ Ｏｅ以上が得られた０実施例３
Ｃｏ １２％、Ｃｒ２５％、Ｓｔ Ｏ，５％、Ｔｉ ０
．５ ％、残部実質的にＦｅの組成になるように配合し
た後、ＭｎおよびＢを第１表に示すように複合添加し、
水アトマイズ法にて粒度１００ｍｅｓｈ以下の８ａｉ＃
４の合金粉末を作製した。As is clear from Figure 3, when the amount of B added is in the range of 0.1 to 5 inches, the theoretical density ratio is 96 inches or more, and the maximum energy product is 3.5 inches.
M G Oe or higher was obtained Example 3 Co 12%, Cr 25%, St O, 5%, Ti 0
．． 5%, the remainder being essentially Fe, and then Mn and B were added in combination as shown in Table 1.
8ai# with a particle size of 100 mesh or less using the water atomization method
An alloy powder of No. 4 was prepared.
第 １ 表
各合金粉末を用いて実施例１と同様の条件で成形、焼結
を行った。しかるｅ、１２００℃で３０分間保持する溶
体化処理を行い、さらに６５０℃近傍で４０分間保持す
る等温ｉ場処理を行い、続いて４℃／ｈの速贋で６２５
℃から４７０℃まで冷却する時効処理を施して焼結研石
を得た。Table 1 Molding and sintering were performed under the same conditions as in Example 1 using each alloy powder. However, solution treatment was performed at 1200°C for 30 minutes, followed by isothermal i-field treatment at around 650°C for 40 minutes, followed by 625
A sintered grinding stone was obtained by performing an aging treatment of cooling from °C to 470 °C.
得られた焼結磁石の理論密度比と最大エネルギー積値は
第１表に示す通りである。第１表よシ明らかなようにＭ
ｎ５Ｂ無添加材（−１）に比べ、ＭｎとＢを複合添加し
た磁石（Ｎ［Ｌ２〜８）は理論密度比および最大エネル
ギー積がともに向上している。The theoretical density ratio and maximum energy product value of the obtained sintered magnet are shown in Table 1. From Table 1, it is clear that M
Compared to the n5B additive-free material (-1), the magnets (N [L2 to 8) with a composite addition of Mn and B have improved both the theoretical density ratio and the maximum energy product.
以上に記述の如く、本兄明の製造方法によれば、本系合
金を水アトマイズ法にて合金粉末にする際、Ｍｎおよび
／またはＢをふ加することによシ、合金粉末を球状化せ
しめたものであり、その結果焼結後の密度が向上して理
論密度比９６チ以上、最大エネルギー積３．５ Ｍ ０
０ｅ以上の優れた焼結磁石合金を提供することが可能と
なったものである。As described above, according to the manufacturing method of the present inventor, when the present alloy is made into alloy powder by the water atomization method, by adding Mn and/or B, the alloy powder is made spheroidal. As a result, the density after sintering is improved, the theoretical density ratio is 96 cm or more, and the maximum energy product is 3.5 M 0
This makes it possible to provide an excellent sintered magnet alloy with a magnetic flux of 0e or higher.
第１図（ａ）及び（ｂ）はそれぞれＭｎを無添加の合金
粉末およびＭｎを０．５チ添加した合金粉末の鵡微鋭写
真、第２図は合金粉末のＭｎの添加量とＦｅ −Ｃｒ−
Ｃｏ系磁石の理論密度比および最大エネルギー積の関係
を示す図、第３図は合金粉末のＢの添加量とＦｅ −Ｃ
ｒ −Ｃｏ系磁石合金の理論密度比および最大エネルギ
ー積の関係を示す図である。
代理人 弁理士 本 間 崇Figures 1 (a) and (b) are microphotographs of an alloy powder with no addition of Mn and an alloy powder with 0.5 mm of Mn added, respectively, and Figure 2 shows the amount of Mn added in the alloy powder and the Fe - Cr-
A diagram showing the relationship between the theoretical density ratio and the maximum energy product of Co-based magnets. Figure 3 shows the relationship between the amount of B added to the alloy powder and the Fe-C
FIG. 2 is a diagram showing the relationship between the theoretical density ratio and the maximum energy product of an r-Co-based magnet alloy. Agent Patent Attorney Takashi Honma
Claims (1)
てＳｔとＴｉを含む合金の溶湯なアトマイズ法により粉
末化するＦｅ −Ｃｒ −Ｃｏ系合金粉末の製造方法に
おいて、前記合金としてＦｅ、Ｃｒ及びＣｏとともにＭ
ｎおよび／またはＢを添加した合金を用いたことを特徴
とするＦｅ−Ｃｒ−Ｃｏ系合金粉末の製造方法。 ２、重量比でＣｒ１７〜４５％、６０５〜３０％、Ｓｔ
Ｏ，１〜５％、Ｔｉ００１〜５％、Ｍｎ Ｏ，１〜５
％、 ＢＯ０１〜５％、残部実質的にＦｅからなる合金
を用いたことを特徴とする特許請求の範囲第１項記載の
Ｆｅ −Ｃｒ −Ｃｏ系合金粉末の製造方法。[Claims] 1. A method for producing a Fe-Cr-Co alloy powder, which comprises powdering an alloy mainly composed of Fe5Cr and Co and containing St and Ti as essential components by a molten atomization method, wherein as the alloy M together with Fe, Cr and Co
A method for producing a Fe-Cr-Co alloy powder, characterized in that an alloy containing n and/or B is used. 2. Cr17-45%, 605-30%, St by weight ratio
O, 1-5%, Ti001-5%, Mn O, 1-5
%, BO01 to 5%, and the remainder substantially consists of Fe.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP20000083A JPS6092409A (en) | 1983-10-27 | 1983-10-27 | Manufacture of fe-cr-co alloy powder |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP20000083A JPS6092409A (en) | 1983-10-27 | 1983-10-27 | Manufacture of fe-cr-co alloy powder |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS6092409A true JPS6092409A (en) | 1985-05-24 |
Family
ID=16417125
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP20000083A Pending JPS6092409A (en) | 1983-10-27 | 1983-10-27 | Manufacture of fe-cr-co alloy powder |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS6092409A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5503475A (en) * | 1992-10-23 | 1996-04-02 | Metec Corporation | Method for determining the carbon equivalent, carbon content and silicon content of molten cast iron |
-
1983
- 1983-10-27 JP JP20000083A patent/JPS6092409A/en active Pending
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5503475A (en) * | 1992-10-23 | 1996-04-02 | Metec Corporation | Method for determining the carbon equivalent, carbon content and silicon content of molten cast iron |
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