JPH0543976A - Production of fe-cr-al powder alloy - Google Patents
Production of fe-cr-al powder alloyInfo
- Publication number
- JPH0543976A JPH0543976A JP3226556A JP22655691A JPH0543976A JP H0543976 A JPH0543976 A JP H0543976A JP 3226556 A JP3226556 A JP 3226556A JP 22655691 A JP22655691 A JP 22655691A JP H0543976 A JPH0543976 A JP H0543976A
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- Prior art keywords
- alloy
- powder
- extrusion
- atomizing method
- producing
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- Manufacture Of Metal Powder And Suspensions Thereof (AREA)
- Powder Metallurgy (AREA)
Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明はＦｅ−Ｃｒ−Ａｌ系粉末
合金の製造方法に関し、さらに詳しくは、ヒーター等の
高温において使用するのに適しているＦｅ−Ｃｒ−Ａｌ
系粉末合金の製造方法に関するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for producing an Fe-Cr-Al-based powder alloy, and more specifically, Fe-Cr-Al suitable for use at high temperatures such as heaters.
The present invention relates to a method for producing a powdery alloy.
【０００２】[0002]
【従来技術】従来、家庭電気製品および工業用炉の発熱
体や精密抵抗線に有用な高電気抵抗のＦｅ−Ｃｒ−Ａｌ
系粉末合金を製造する方法としては、例えば、特開昭６
２−２８０３４８号公報に記載されているように、Ｆｅ
−Ｃｒ−Ａｌ系合金を真空溶解を行った後、不活性ガス
中においてガスアトマイズ法により製造した合金粉末を
ＨＩＰ成形および熱間圧延により製品とすることが行わ
れて来ている。2. Description of the Related Art Conventionally, Fe-Cr-Al having a high electric resistance which is useful for heating elements and precision resistance wires of household electric appliances and industrial furnaces.
As a method for producing a powder-based alloy, for example, Japanese Patent Laid-Open No.
As described in JP-A-2-280348, Fe
It has been practiced to vacuum-melt a —Cr—Al alloy and then to make an alloy powder produced by a gas atomizing method in an inert gas into a product by HIP molding and hot rolling.
【０００３】この従来のＦｅ−Ｃｒ−Ａｌ系粉末合金の
製造方法について、図３により説明すると、Ｆｅ−Ｃｒ
−Ａｌ系合金を真空溶解し、アルゴン等の不活性ガスア
トマイズ法により、酸素含有量２００ｐｐｍ以下、窒素
含有量３００ｐｐｍ以下の合金粉末を作製し、次いで、
１１００℃×１０００ａｔｍでＨＩＰ成形を行い、外側
に軟鋼層を付けたままの状態で圧延を行い製品とする。
なお、ガス成分が上記の範囲内であれば軟鋼シースを付
けた状態で割れることなく、熱間圧延を行うことができ
る（図３の工程Ａ）。The conventional method for producing the Fe-Cr-Al powder alloy will be described with reference to FIG.
-Al-based alloy is vacuum-melted and an alloy powder having an oxygen content of 200 ppm or less and a nitrogen content of 300 ppm or less is produced by an atomizing method of an inert gas such as argon, and then,
HIP molding is performed at 1100 ° C. × 1000 atm, and rolling is performed with the mild steel layer attached to the outside to obtain a product.
If the gas component is within the above range, hot rolling can be performed without cracking with the mild steel sheath attached (step A in FIG. 3).
【０００４】しかしながら、特開昭６２−２８０３４８
号公報においても、熱間加工性は極めて悪く、軟鋼容器
に充填した状態でなければ、圧延を行うことができない
ので、工業的な量産方法とは言えず、Ｆｅ−Ｃｒ−Ａｌ
系合金の熱間加工性の改善が望まれていた。However, JP-A-62-280348
Also in the publication, the hot workability is extremely poor, and rolling cannot be performed unless it is filled in a mild steel container. Therefore, it cannot be said to be an industrial mass production method, and Fe-Cr-Al cannot be said.
It has been desired to improve hot workability of alloys.
【０００５】また、実際の試験結果においても、Ｆｅ−
Ｃｒ−Ａｌ系合金を真空溶解後、溶湯をアルゴンガスア
トマイズ法により合金粉末とし（酸素６１ｐｐｍ、窒素
１０５ｐｐｍ）、この合金粉末をＨＩＰを行った後、軟
鋼製カプセル層を除去し、ヒーター材ビレットの圧延を
行おうとしたが、クラックが発生して圧延は行えなかっ
た。In the actual test results, Fe-
After vacuum melting the Cr-Al alloy, the molten metal was made into alloy powder by the argon gas atomization method (oxygen 61 ppm, nitrogen 105 ppm), and after HIPing this alloy powder, the mild steel capsule layer was removed and the heater material billet was rolled. However, cracking occurred and rolling could not be performed.
【０００６】[0006]
【発明が解決しようとする課題】本発明は上記に説明し
た従来のＦｅ−Ｃｒ−Ａｌ系粉末合金の製造方法におけ
る種々の問題点に鑑み、本発明者が鋭意研究を行い、検
討を重ねた結果、Ｆｅ−Ｃｒ−Ａｌ系合金を粉末キャン
ニングおよびＨＩＰ後の熱間圧延において、殆どの試験
材が割れを発生する原因として、粒子間界面の窒化物、
酸化物の存在による粒界劣化によることを知見し、従っ
て、これら窒化物、酸化物が粒界に多数存在しても粒界
劣化を生じない、欠陥のない優れた性能を有するＦｅ−
Ｃｒ−Ａｌ系粉末合金の製造方法を開発したのである。DISCLOSURE OF THE INVENTION In view of various problems in the above-described conventional method for producing a Fe-Cr-Al powder alloy, the present invention has been earnestly studied and studied by the present inventor. As a result, in the hot rolling after powder canning and HIP of the Fe-Cr-Al alloy, the cause of cracking in most of the test materials is a nitride at the interparticle interface,
It was found that the grain boundary was deteriorated due to the presence of the oxide. Therefore, even if a large number of these nitrides and oxides were present in the grain boundary, the grain boundary was not deteriorated.
A method for producing a Cr-Al powder alloy has been developed.
【０００７】[0007]
【課題を解決するための手段】本発明に係るＦｅ−Ｃｒ
−Ａｌ系粉末合金の製造方法は、Ｃｒ２０〜３５ｗｔ
％、Ａｌ４〜１２ｗｔ％、を含有するＦｅ−Ｃｒ−Ａｌ
系合金溶湯をガスアトマイズ法、または、水アトマイズ
法により粉末化し、この合金粉末を予備成形し、また
は、予備成形することなく、押出比２以上の熱間押出加
工を行った後に成形加工を行うことを特徴とするＦｅ−
Ｃｒ−Ａｌ系粉末合金の製造方法を第１の発明とし、ま
た、合金粉末中の酸素は０.１０ｗｔ％以下、窒素は０.
０５〜０.２０ｗｔ％である請求項１記載のＦｅ−Ｃｒ
−Ａｌ系粉末合金の製造方法を第２の発明とし、合金粉
末がＺｒ、Ｎｂ、Ｔｉの１種以上および／またはＹ、Ｈ
ｆ、Ｓｃ、希土類元素の１種以上を合計で１ｗｔ％以下
含有する請求項２記載のＦｅ−Ｃｒ−Ａｌ系粉末合金の
製造方法を第３の発明とする３つの発明よりなるもので
ある。Fe-Cr according to the present invention
-Al-based powder alloy is manufactured by Cr 20 to 35 wt.
%, Al4-12 wt%, Fe-Cr-Al
The molten alloy is made into powder by the gas atomization method or the water atomization method, and this alloy powder is preformed, or without being preformed, hot extrusion with an extrusion ratio of 2 or more is performed, followed by forming. Fe- characterized by
The first invention is a method for producing a Cr-Al powder alloy, and oxygen in the alloy powder is 0.10 wt% or less and nitrogen is 0.1% or less.
Fe-Cr according to claim 1, wherein the content is 05 to 0.20 wt%.
A second invention is a method for producing an Al-based powder alloy, wherein the alloy powder is one or more of Zr, Nb, and Ti and / or Y, H.
A third aspect of the present invention is a method for producing a Fe-Cr-Al-based powder alloy according to claim 2, which contains 1 wt% or less of at least one of f, Sc, and a rare earth element in total.
【０００８】本発明に係るＦｅ−Ｃｒ−Ａｌ系粉末合金
の製造方法について、以下詳細に説明する。先ず、本発
明に係るＦｅ−Ｃｒ−Ａｌ系粉末合金の製造方法におい
て使用する合金の含有成分および成分割合について説明
する。The method of manufacturing the Fe-Cr-Al powder alloy according to the present invention will be described in detail below. First, the contained components and component ratios of the alloy used in the method for producing an Fe-Cr-Al-based powder alloy according to the present invention will be described.
【０００９】Ｃｒは耐酸化性を付与する元素であり、含
有量が２０ｗｔ％未満では耐酸化性が充分でなく、ま
た、３５ｗｔ％を越えるとシグマ相を形成して脆化す
る。よって、Ｃｒ含有量は２０〜３５ｗｔ％とする。[0009] Cr is an element which imparts oxidation resistance, and if the content is less than 20 wt%, the oxidation resistance is not sufficient, and if it exceeds 35 wt%, a sigma phase is formed to cause embrittlement. Therefore, the Cr content is set to 20 to 35 wt%.
【００１０】ＡｌはＣｒと同様に耐酸化性を付与する元
素であり、含有量が４ｗｔ％未満では耐酸化性が不足
し、また、１２ｗｔ％を越えると脆化する。よって、Ａ
ｌ含有量は４〜１２ｗｔ％とする。Al, like Cr, is an element that imparts oxidation resistance, and if the content is less than 4 wt%, the oxidation resistance is insufficient, and if it exceeds 12 wt%, it becomes brittle. Therefore, A
The l content is 4 to 12 wt%.
【００１１】酸素は含有量が０.１０ｗｔ％を越えると
加工性が劣化する。よつて、酸素含有量は０.１０ｗｔ
％以下とする。If the oxygen content exceeds 0.10 wt%, the workability deteriorates. Therefore, the oxygen content is 0.10 wt.
% Or less.
【００１２】窒素は含有量が０.０５ｗｔ％未満におい
ては耐クリープ性が悪くなり、また、０.２０ｗｔ％を
越えると加工性が悪化する。よって、窒素含有量は０.
０５〜０.２０ｗｔ％とする。If the nitrogen content is less than 0.05 wt%, the creep resistance is poor, and if it exceeds 0.20 wt%, the workability is poor. Therefore, the nitrogen content is 0.
It is set to 05 to 0.20 wt%.
【００１３】なお、本発明に係るＦｅ−Ｃｒ−Ａｌ系粉
末合金の製造方法においては、高温クリープ性を改善す
るためには、上記のように窒素含有量を０.０５〜０.２
０ｗｔ％に制御することによって効果があるものであ
り、この高窒素のＦｅ−Ｃｒ−Ａｌ系粉末合金の製造に
は、押出加工のような静水圧成分の大きい状態の加工が
すぐているのである。In the method of manufacturing the Fe-Cr-Al powder alloy according to the present invention, in order to improve the high temperature creep property, the nitrogen content should be 0.05 to 0.2 as described above.
Controlling to 0 wt% has an effect, and in the production of this high-nitrogen Fe-Cr-Al-based powder alloy, processing with a large hydrostatic pressure component, such as extrusion, is immediate. ..
【００１４】Ｚｒ、Ｎｂ、Ｔｉ、Ｙ、Ｈｆ、Ｓｃおよび
希土類元素のＣｅ、Ｌａ、Ｐｒ、Ｎｄ等は酸化膜が合金
に密着する作用を高くし、酸化膜が剥離して酸化物量が
増大することを防止する元素であり、含有量が１ｗｔ％
を越えると合金の靭性が低下する。よって、Ｚｒ、Ｎ
ｂ、Ｔｉ、Ｙ、Ｈｆ、Ｓｃおよび希土類元素のＣｅ、Ｌ
ａ、Ｐｒ、Ｎｄ等の含有量は何れも合計で１ｗｔ％以下
とする。Zr, Nb, Ti, Y, Hf, Sc and rare earth elements Ce, La, Pr, Nd, etc. enhance the action of the oxide film adhering to the alloy, and the oxide film is peeled off to increase the amount of oxide. It is an element that prevents this, the content is 1 wt%
If it exceeds, the toughness of the alloy will decrease. Therefore, Zr, N
b, Ti, Y, Hf, Sc and rare earth elements Ce, L
The total content of a, Pr, Nd, etc. is 1 wt% or less.
【００１５】次に、本発明に係るＦｅ−Ｃｒ−Ａｌ系粉
末合金の製造方法について図１により説明する。Next, a method of manufacturing the Fe-Cr-Al-based powder alloy according to the present invention will be described with reference to FIG.
【００１６】上記に説明した含有成分および成分割合の
Ｆｅ−Ｃｒ−Ａｌ系合金を、真空溶解或いは大気溶解に
より溶解し、得られた溶湯を窒素等のガスアトマイズ法
または水アトマイズ法によりＦｅ−Ｃｒ−Ａｌ系合金粉
末とする。このＦｅ−Ｃｒ−Ａｌ系合金粉末を以下説明
する３つの工程（図１）により成形を行う。ＨＩＰ成
形→熱間押出→熱間圧延（工程Ｂ） 熱間押出→熱間圧延（工程Ｃ） ＣＩＰ成形→熱間押出→熱間圧延（工程Ｄ） この工程Ｄは、窒素ガスアトマイズ粉末を内径７０φ×
長さ１５０ｍｍの軟鋼製カプセルに充填し、真空加熱脱
気後密封し、プレフォームした。この時の粉末の充填密
度は約７０％であった。このプレフォームにＣＩＰ（冷
間静水圧成形プレス）を使用して、５０００ｋｇ／ｃｍ
2で１時間の加圧処理を行うことより、充填密度を約８
５％にまで上昇させた。このプロセス（ＣＩＰ）は、押
出工程における加熱を容易にするために行うものであ
り、特に行わなくてもよく、この時は、工程Ｃとなる。
なお、各工程において熱間圧延は必ずしも行わなくても
良い。The Fe-Cr-Al-based alloy having the above-described components and component ratios is melted by vacuum melting or atmospheric melting, and the obtained molten metal is Fe-Cr- by a gas atomizing method such as nitrogen or a water atomizing method. Al-based alloy powder is used. This Fe-Cr-Al alloy powder is molded by the three steps (FIG. 1) described below. HIP molding → hot extrusion → hot rolling (step B) hot extrusion → hot rolling (step C) CIP molding → hot extrusion → hot rolling (step D) In this step D, a nitrogen gas atomized powder having an inner diameter of 70φ is used. ×
It was filled in a 150 mm long mild steel capsule, vacuum heated and deaerated, sealed, and preformed. The packing density of the powder at this time was about 70%. 5000 kg / cm using CIP (Cold Isostatic Press) on this preform
By performing pressure treatment at 2 for 1 hour, the packing density is about 8
Raised to 5%. This process (CIP) is performed in order to facilitate heating in the extrusion step, and may not be performed in particular, and in this case, step C is performed.
Note that hot rolling does not necessarily have to be performed in each step.
【００１８】従来法においては、合金粉末表面にＡｌＮ
またはＡｌ2Ｏ3等が偏析するため、ＨＩＰ成形後の圧
延、鍛造等の成形加工を行うには保護シースがなければ
不可能であるが、本発明に係るＦｅ−Ｃｒ−Ａｌ系粉末
合金の製造方法のように、押出比２以上の熱間押出を行
った材料では、粒界上のＡｌＮやＡｌ2Ｏ3等の偏析層が
破壊分散されて、粒界強度が向上し熱間加工が可能とな
るのである。このことは、合金粉末表面にＺｒ、Ｎｂ、
Ｔｉ、Ｙ、Ｈｆ、Ｓｃ、Ｃｅ、Ｌａ、Ｐｒ、Ｎｄ等の窒
化物や酸化物が同時に多数存在していても、押出比２以
上の熱間押出を行えば、割れのない優れた性能を有する
Ｆｅ−Ｃｒ−Ａｌ系粉末合金を製造することができる。In the conventional method, AlN is formed on the surface of the alloy powder.
Or, since Al 2 O 3 and the like segregate, it is impossible to carry out forming processing such as rolling and forging after HIP forming without a protective sheath, but of the Fe—Cr—Al-based powder alloy according to the present invention. As in the manufacturing method, in the material subjected to hot extrusion with an extrusion ratio of 2 or more, the segregation layer such as AlN or Al 2 O 3 on the grain boundary is destroyed and dispersed, the grain boundary strength is improved, and hot working is performed. It will be possible. This means that Zr, Nb,
Even if many nitrides and oxides such as Ti, Y, Hf, Sc, Ce, La, Pr, and Nd exist at the same time, if hot extrusion with an extrusion ratio of 2 or more is performed, excellent performance without cracking is obtained. It is possible to produce a Fe-Cr-Al-based powder alloy that has.
【００１９】また、本発明に係るＦｅ−Ｃｒ−Ａｌ系粉
末合金の製造方法において、ＨＩＰ成形を行った後（行
わない場合もある。）、押出比２以上で熱間加工を行っ
た場合について説明する。即ち、０.０１ｗｔ％Ｃ−２
３ｗｔ％Ｃｒ−５ｗｔ％Ａｌ鋼粉末のＨＩＰ成形体およ
び押出比４で押出した合金の高温高速引張試験の結果を
図２に示してある。In addition, in the method for producing an Fe-Cr-Al-based powder alloy according to the present invention, a case where hot working is performed at an extrusion ratio of 2 or more after HIP forming (may not be performed). explain. That is, 0.01 wt% C-2
The results of a high temperature high speed tensile test of a HIP compact of 3 wt% Cr-5 wt% Al steel powder and an alloy extruded at an extrusion ratio of 4 are shown in FIG.
【００２０】この図２より、ＨＩＰ成形体の絞り値は何
れの温度においても２０％以下であって極めて低いが、
押出加工後の絞り値は何れの温度においても８０％以上
であって加工性が大幅に向上していることがわかる。As shown in FIG. 2, the HIP molded product has an extremely low aperture value of 20% or less at any temperature.
It can be seen that the drawing value after extrusion is 80% or more at any temperature, and the workability is greatly improved.
【００２１】[0021]
【実 施 例】本発明に係るＦｅ−Ｃｒ−Ａｌ系粉末合
金の製造方法の実施例を比較例と共に説明する。[Examples] Examples of the method for producing the Fe-Cr-Al-based powder alloy according to the present invention will be described together with comparative examples.
【００２２】[0022]
【実 施 例 １】表１に使用するＦｅ−Ｃｒ−Ａｌ系合
金の含有成分および成分割合を示してある。この合金
は、Ｆｅ−２３Ｃｒ−５Ａｌ系、Ｆｅ−２７Ｃｒ−５Ａ
ｌ系の２種類を選択した。[Example 1] Table 1 shows the components and ratios of the Fe-Cr-Al alloys used. This alloy is Fe-23Cr-5Al system, Fe-27Cr-5A.
Two types of 1 series were selected.
【００２３】Ｎｏ.１、Ｎｏ.２、Ｎｏ.３、Ｎｏ.４は表
１に示す組成に調整した合金を真空溶解した後、アルゴ
ンガスアトマイザーにより合金粉末を製造した。この合
金粉末を内径７０φ×長さ１５０ｍｍの軟鋼製容器内に
充填し、真空加熱脱気後密封した。In No. 1, No. 2, No. 3 and No. 4, alloy powders having the compositions shown in Table 1 were vacuum melted, and then alloy powders were produced by an argon gas atomizer. This alloy powder was filled in a mild steel container having an inner diameter of 70φ and a length of 150 mm, deaerated under vacuum heating, and then sealed.
【００２４】次いで、ＨＩＰ成形（１１５０℃×１００
０ａｔｍ）した後、軟鋼容器層を切削除去し、６０φ×
長さ１３０ｍｍのビレットを製作した。このビレットを
１１００℃の温度で加熱後、圧延を行ったが、ビレット
表面に無数のクラックが発生した。Then, HIP molding (1150 ° C. × 100)
0 atm), the mild steel container layer is then removed by cutting, and 60φ x
A billet having a length of 130 mm was manufactured. This billet was heated at a temperature of 1100 ° C. and then rolled, but numerous cracks were generated on the billet surface.
【００２５】Ｎｏ.５、Ｎｏ.６は本発明に係るＦｅ−Ｃ
ｒ−Ａｌ系粉末合金の製造方法によるものであり、大気
溶解後、溶湯を窒素ガスアトマイザーにより合金粉末を
製造し、次いで、上記のＮｏ.１、Ｎｏ.２と同様な方法
によりＨＩＰ成形により製作した６０φ×長さ１３０ｍ
ｍの成形体を、押出比４で熱間押出加工により３０φ×
長さ５２０のバー材とした。No. 5 and No. 6 are Fe-C according to the present invention
According to the manufacturing method of r-Al-based powder alloy, after melting in air, the molten metal is manufactured into an alloy powder by a nitrogen gas atomizer, and then manufactured by HIP molding by the same method as No. 1 and No. 2 described above. 60φ x length 130m
The molded body of m is hot-extruded at an extrusion ratio of 4 to obtain 30φ ×
A bar material having a length of 520 was used.
【００２６】このバー材に熱間圧延を行ったがクラック
の発生は認められなかった。The bar material was hot-rolled, but no crack was observed.
【００２７】[0027]
【実 施 例 ２】表１のＮｏ.７、Ｎｏ.８は、Ｆｅ−Ｃ
ｒ−Ａｌ系合金を大気溶解後、溶湯を窒素ガスアトマイ
ザーにより合金粉末を製造し、内径２１０φ×長さ１５
０ｍｍの軟鋼製カプセルに密封し、１１００℃の温度に
加熱後、押出比２０で押出加工を行って製作した合金で
ある。この合金は、次工程の圧延によるクラックの発生
はなかった。[Example 2] No. 7 and No. 8 in Table 1 are Fe-C
After melting the r-Al-based alloy in the air, the molten metal is manufactured into an alloy powder with a nitrogen gas atomizer, and the inner diameter is 210φ × length 15
It is an alloy produced by sealing in a 0 mm mild steel capsule, heating to a temperature of 1100 ° C., and then extruding at an extrusion ratio of 20. This alloy did not generate cracks due to rolling in the next step.
【００２８】[0028]
【実 施 例 ３】表１のＮｏ.９、Ｎｏ.１０はＦｅ−Ｃ
ｒ−Ａｌ系合金を真空溶解後、溶湯を窒素ガスアトマイ
ザーにより合金粉末を製造し、内径７０φ×長さ１５０
ｍｍの軟鋼製カプセルに密封し、ＣＩＰ成形（常温、５
０００ａｔｍ）により製作した６０φ×長さ１３０ｍｍ
の成形体を、押出比２で熱間押出加工により４２φ×長
さ２６５ｍｍのバー材とした。このバー材を１１００℃
の温度に加熱後、圧延を行ったがクラックの発生は認め
られなかった。[Example 3] No. 9 and No. 10 in Table 1 are Fe-C
After the r-Al alloy is melted in vacuum, an alloy powder is produced from the molten metal by a nitrogen gas atomizer, and the inner diameter is 70φ and the length is 150.
Sealed in a mm steel capsule and CIP molded (at room temperature, 5
000atm) 60φ x length 130mm
The molded body of was subjected to hot extrusion processing at an extrusion ratio of 2 to obtain a bar material having 42φ and a length of 265 mm. This bar material is 1100 ℃
After heating to the above temperature, rolling was performed, but no crack was observed.
【００２９】[0029]
【実 施 例 ４】表１のＮｏ.１１、Ｎｏ.１２は、Ｆｅ
−Ｃｒ−Ａｌ系合金を大気溶解後、溶湯を水アトマイザ
ーにより合金粉末を製造し、内径７０φ×長さ１５０ｍ
ｍの軟鋼製カプセルに密封し、１１００℃の温度に加熱
後、押出比１０で押出加工を行って製造した。この合金
も、次工程の１１５０℃の温度における熱間圧延におい
て、クラックの発生を認められなかった。[Example 4] No. 11 and No. 12 in Table 1 are Fe.
After melting the -Cr-Al-based alloy in the air, the melt is made into alloy powder with a water atomizer, and the inner diameter is 70φ and the length is 150 m.
It was manufactured by sealing in a m. mild steel capsule, heating to a temperature of 1100 ° C., and then extruding at an extrusion ratio of 10. No cracks were observed in this alloy during hot rolling at a temperature of 1150 ° C. in the next step.
【００３０】[0030]
【表１】 [Table 1]
【００３１】[0031]
【発明の効果】以上説明したように、本発明に係るＦｅ
−Ｃｒ−Ａｌ系粉末合金の製造方法は上記の構成である
から、製造された粉末合金が如何なる溶解法および如何
なるアトマイズ法を組み合わせて製造された合金粉末で
あっても、合金粉末表面には多量の酸化物、窒化物等が
存在しても、押出加工を行うことによってＡｌＮ、Ａｌ
2Ｏ3等の偏析層が破壊・分散されるので、割れ発生起点
となる粒界の靭性向上を図ることができ、従って、熱間
加工性を著しく向上させ、熱間加工を容易に行うことが
できるという優れた効果を有するものである。As described above, Fe according to the present invention
Since the manufacturing method of the —Cr—Al powder alloy has the above-mentioned constitution, even if the manufactured powder alloy is the alloy powder manufactured by combining any melting method and any atomizing method, a large amount is present on the surface of the alloy powder. Even if there are oxides, nitrides, etc. of AlN and Al
Since the segregation layer of 2 O 3 etc. is destroyed / dispersed, it is possible to improve the toughness of the grain boundary that is the starting point of cracking. Therefore, the hot workability is remarkably improved and the hot work is easily performed. It has an excellent effect that
【図１】本発明に係るＦｅ−Ｃｒ−Ａｌ系粉末合金の製
造方法を説明するための工程図である。FIG. 1 is a process chart for explaining a method for manufacturing an Fe—Cr—Al-based powder alloy according to the present invention.
【図２】加工温度と絞り値との関係を示す図である。FIG. 2 is a diagram showing a relationship between a processing temperature and an aperture value.
【図３】従来のＦｅ−Ｃｒ−Ａｌ系粉末合金の製造方法
を示す工程図である。FIG. 3 is a process chart showing a method for producing a conventional Fe—Cr—Al-based powder alloy.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 細 川 博 埼玉県熊谷市熊谷810 株式会社リケン熊 谷事業所内 (72)発明者 武 本 昌 之 埼玉県熊谷市熊谷810 株式会社リケン熊 谷事業所内 ─────────────────────────────────────────────────── ─── Continuation of the front page (72) Inventor Hiroshi Hosokawa 810 Riken Kumagaya Works, Kumagaya City, Saitama Prefecture (72) Inventor Masayuki Takemoto 810 Rikuma Kumagaya Works, Kumagaya City, Saitama Prefecture
Claims (3)
％、を含有するＦｅ−Ｃｒ−Ａｌ系合金溶湯をガスアト
マイズ法、または、水アトマイズ法により粉末化し、こ
の合金粉末を予備成形し、または、予備成形することな
く、押出比２以上の熱間押出加工を行った後に成形加工
を行うことを特徴とするＦｅ−Ｃｒ−Ａｌ系粉末合金の
製造方法。1. Cr 20 to 35 wt%, Al 4 to 12 wt
% Of the Fe-Cr-Al alloy molten metal is pulverized by a gas atomizing method or a water atomizing method, and the alloy powder is preformed or hot extrusion with an extrusion ratio of 2 or more without preforming. A method for producing an Fe-Cr-Al-based powder alloy, which comprises performing a forming process after performing the process.
窒素は０.０５〜０.２０ｗｔ％である請求項１記載のＦ
ｅ−Ｃｒ−Ａｌ系粉末合金の製造方法。2. Oxygen in the alloy powder is 0.10 wt% or less,
Nitrogen is 0.05 to 0.20 wt% and F according to claim 1.
A method for producing an e-Cr-Al-based powder alloy.
よび／またはＹ、Ｈｆ、Ｓｃ、希土類元素の１種以上を
合計で１ｗｔ％以下含有する請求項２記載のＦｅ−Ｃｒ
−Ａｌ系粉末合金の製造方法。3. The Fe-Cr alloy according to claim 2, wherein the alloy powder contains at least 1 wt% of Zr, Nb and Ti and / or at least one of Y, Hf, Sc and rare earth elements in a total amount of 1 wt% or less.
-A method for manufacturing an Al-based powder alloy.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP22655691A JP2928411B2 (en) | 1991-08-12 | 1991-08-12 | Method for producing Fe-Cr-Al powder alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP22655691A JP2928411B2 (en) | 1991-08-12 | 1991-08-12 | Method for producing Fe-Cr-Al powder alloy |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH0543976A true JPH0543976A (en) | 1993-02-23 |
| JP2928411B2 JP2928411B2 (en) | 1999-08-03 |
Family
ID=16847015
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP22655691A Expired - Fee Related JP2928411B2 (en) | 1991-08-12 | 1991-08-12 | Method for producing Fe-Cr-Al powder alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2928411B2 (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH06279811A (en) * | 1993-03-25 | 1994-10-04 | Kobe Steel Ltd | Production of fe-cr-al alloy powder |
| US5989491A (en) * | 1996-04-10 | 1999-11-23 | Sanyo Special Steel Co., Ltd. | Oxide dispersion strengthened heat resisting powder metallurgy alloy and process for producing the same |
-
1991
- 1991-08-12 JP JP22655691A patent/JP2928411B2/en not_active Expired - Fee Related
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH06279811A (en) * | 1993-03-25 | 1994-10-04 | Kobe Steel Ltd | Production of fe-cr-al alloy powder |
| US5989491A (en) * | 1996-04-10 | 1999-11-23 | Sanyo Special Steel Co., Ltd. | Oxide dispersion strengthened heat resisting powder metallurgy alloy and process for producing the same |
Also Published As
| Publication number | Publication date |
|---|---|
| JP2928411B2 (en) | 1999-08-03 |
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