JP3236713B2 - Fe-Cr-Ni alloy with excellent deep drawability - Google Patents
Fe-Cr-Ni alloy with excellent deep drawabilityInfo
- Publication number
- JP3236713B2 JP3236713B2 JP26208493A JP26208493A JP3236713B2 JP 3236713 B2 JP3236713 B2 JP 3236713B2 JP 26208493 A JP26208493 A JP 26208493A JP 26208493 A JP26208493 A JP 26208493A JP 3236713 B2 JP3236713 B2 JP 3236713B2
- Authority
- JP
- Japan
- Prior art keywords
- ppm
- less
- group
- amount
- deep drawability
- 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.)
- Expired - Fee Related
Links
Landscapes
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Description
【０００１】[0001]
【産業上の利用分野】本発明は深絞り成形性に優れたＦ
ｅ−Ｃｒ−Ｎｉ系合金に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to an F
It relates to an e-Cr-Ni alloy.
【０００２】[0002]
【従来の技術】Ｆｅ−Ｃｒ−Ｎｉ系合金は、加工により
オーステナイト相がマルテンサイト変態するため、フラ
ンジ部分の加工硬化が著しく、深絞り成形性が良好でな
い。そのため、特開平２−１４１５５６号では、この加
工硬化を抑制するためにオーステナイト安定化元素であ
るＣｕを添加してオーステナイト相がマルテンサイト変
態することを抑制することも行なっているが、この場合
でも深絞り成形性の改善は十分でなかった。また、特開
平１−３０１８４０号や特開平４−２７２１５８号で
は、この加工硬化を抑制するためにＣ＋Ｎ量を低減する
ことにより変態したマルテンサイトを軟質化することが
行なわれているが、この場合でも深絞り成形性の改善は
十分でなかった。2. Description of the Related Art In an Fe-Cr-Ni alloy, the austenite phase undergoes a martensitic transformation by working, so that the work hardening of the flange portion is remarkable and the deep drawability is not good. Therefore, in Japanese Patent Application Laid-Open No. 2-141556, in order to suppress the work hardening, Cu which is an austenite stabilizing element is added to suppress the martensitic transformation of the austenite phase. The improvement in deep drawability was not sufficient. In JP-A-1-301840 and JP-A-4-272158, in order to suppress the work hardening, the transformed martensite is softened by reducing the amount of C + N. However, the deep drawability was not sufficiently improved.
【０００３】[0003]
【発明が解決しようとする課題】本発明は、深絞り成形
性を向上させたＦｅ−Ｃｒ−Ｎｉ系合金を提供すること
を目的とする。SUMMARY OF THE INVENTION An object of the present invention is to provide an Fe-Cr-Ni alloy having improved deep drawability.
【０００４】[0004]
【課題を解決するための手段】本発明者らは、前記問題
点を解決するために、種々の化学成分を有するＦｅ−Ｃ
ｒ−Ｎｉ系合金の深絞り成形性について調査を行ない、
Ｃ量を通常のＦｅ−Ｃｒ−Ｎｉ合金のレベルより減少さ
せると深絞り成形性が著しく向上することを発見した。
その機構は、必ずしも明らかではないが、Ｃ量を減少さ
せると深絞り加工に有利な集合組織が発達すること、お
よび加工により変態したマルテンサイト部分の延性が向
上することと関係していると考えられる。また、Ｃを低
減すると同時にＳ，Ｏを低減すると、おそらく鋼の延性
が向上することにより、深絞り成形性が著しく向上する
ことを発見して本発明に至った。このようなＦｅ−Ｃｒ
−Ｎｉ合金については、さらに固溶Ｃ量を低減させるＴ
ｉ群（Ｔｉ，Ｎｂ，Ｖ，Ｚｒ，Ｔａ，Ｍｏ，Ｗ）、延性
時のマルテンサイト変態を抑制して焼鈍時に変態しオー
ステナイトの集合組成がランダムになることを抑制する
Ｎ群（Ｎ，Ｍｎ，Ａｌ，Ｃｕ，Ｃｏ）、および、強度を
向上させて加工硬化率を向上させるＳｎ群（Ｓｎ，Ｓ
ｂ，Ｐ，Ｓｉ，Ｂ）を添加することで、さらに深絞り成
形性が向上する。Means for Solving the Problems In order to solve the above-mentioned problems, the present inventors have proposed Fe-C having various chemical components.
The deep drawability of the r-Ni alloy was investigated and
It has been discovered that reducing the C content below the level of conventional Fe-Cr-Ni alloys significantly improves deep draw formability.
Although the mechanism is not necessarily clear, it is considered that reducing the C content is related to the development of a texture advantageous for deep drawing and the improvement of the ductility of the martensite portion transformed by the processing. Can be Further, the present inventors have found that when S and O are reduced at the same time as C is reduced, the ductility of steel is likely to be improved, and the deep drawability is significantly improved. Such Fe-Cr
-Ni alloys, T to further reduce the amount of solid solution C
Group i (Ti, Nb, V, Zr, Ta, Mo, W), Group N (N, Mn) which suppresses martensitic transformation during ductility and transforms during annealing to suppress the austenite aggregate composition from becoming random. , Al, Cu, Co) and a Sn group (Sn, S) for improving the work hardening rate by improving the strength.
By adding (b, P, Si, B), deep drawing formability is further improved.
【０００５】すなわち、本発明は、Ｃｒ：１５〜５０ｗ
ｔ％， Ｎｉ：６．１〜５０ｗｔ％，Ｃ：１５ｐ
ｐｍ以下， Ｓ：５０ｐｐｍ以下，Ｏ：５０
ｐｐｍ以下含有し、残部はＦｅおよび不可避的不純物よ
りなる深絞り成形性に優れたＦｅ−Ｃｒ−Ｎｉ系合金を
提供するものである。That is, the present invention provides a method of
t%, Ni: 6.1 to 50 wt%, C: 15 p
pm or less, S: 50 ppm or less, O: 50
The present invention provides an Fe-Cr-Ni-based alloy containing at most ppm and the balance being Fe and unavoidable impurities and having excellent deep drawability.
【０００６】さらに、本発明は上記成分に加え、さらに
下記の（Ｉ）、（II）および（III)の三グループから選
択された少なくとも一つのグループを含有する深絞り性
に優れたＦｅ−Ｃｒ−Ｎｉ系合金を提供するものであ
る。 （Ｉ）Ｔｉ：０．０１〜１．０ｗｔ％， Ｎｂ：０．０
１〜１．０ｗｔ％，Ｖ：０．０１〜１．０ｗｔ％，
Ｚｒ：０．０１〜１．０ｗｔ％，Ｔａ：０．０１〜１．
０ｗｔ％， Ｍｏ：０．１〜５．０ｗｔ％、およびＷ：
０．１〜５．０ｗｔ％よりなる群より選択された少なく
とも一種（以下、Ｔｉ群という）。 （II）Ｎ：２００〜２０００ｐｐｍ， Ｍｎ：０．０１
〜２０ｗｔ％Ａｌ：０．０１〜５．０ｗｔ％， Ｃｕ：
０．１〜５．０ｗｔ％、およびＣｏ：０．１〜５．０ｗ
ｔ％よりなる群から選択された少なくとも一種（以下、
Ｎ群という）。 （III)Ｓｎ：０．０１〜１．０ｗｔ％， Ｓｂ：０．０
１〜１．０ｗｔ％，Ｐ：２００〜２０００ｐｐｍ，
Ｓｉ：０．１〜５．０ｗｔ％、およびＢ：３〜１００ｐ
ｐｍよりなる群より選択された少なくとも一種（以下、
Ｓｎ群という）。Further, the present invention provides an Fe--Cr alloy having excellent deep drawability which contains at least one group selected from the following three groups (I), (II) and (III) in addition to the above components. A Ni-based alloy. (I) Ti: 0.01 to 1.0 wt%, Nb: 0.0
1 to 1.0 wt%, V: 0.01 to 1.0 wt%,
Zr: 0.01-1.0 wt%, Ta: 0.01-1.
0 wt%, Mo: 0.1 to 5.0 wt%, and W:
At least one selected from the group consisting of 0.1 to 5.0 wt% (hereinafter referred to as Ti group). (II) N: 200 to 2000 ppm, Mn: 0.01
２０20 wt% Al: 0.01-5.0 wt%, Cu:
0.1 to 5.0 wt%, and Co: 0.1 to 5.0 w
at least one selected from the group consisting of
N group). (III) Sn: 0.01 to 1.0 wt%, Sb: 0.0
1 to 1.0 wt%, P: 200 to 2000 ppm,
Si: 0.1 to 5.0 wt%, and B: 3 to 100 p
pm (hereinafter, at least one selected from the group consisting of
Sn group).
【０００７】以下に本発明をさらに詳細に説明する。上
述したように、本発明は、Ｃｒ：１５〜５０ｗｔ％，
Ｎｉ：６．１〜５０ｗｔ％，Ｃ：１５ｐｐｍ以
下， Ｓ：５０ｐｐｍ以下，Ｏ：５０ｐｐｍ
以下含有し、残部はＦｅおよび不可避的不純物よりなる
深絞り成形性に優れたＦｅ−Ｃｒ−Ｎｉ系合金に関し、
さらには上記成分に加えて、さらに下記の（Ｉ）、（I
I）および（III)の三グループから選択された少なくと
も一つを含有する深絞り性に優れたＦｅ−Ｃｒ−Ｎｉ系
合金に関する。下記の（Ｉ）〜（III)グループの元素の
添加によりさらに深絞り性を向上させることができる。 （Ｉ）Ｔｉ：０．０１〜１．０ｗｔ％， Ｎｂ：０．０
１〜１．０ｗｔ％，Ｖ：０．０１〜１．０ｗｔ％，
Ｚｒ：０．０１〜１．０ｗｔ％，Ｔａ：０．０１〜１．
０ｗｔ％， Ｍｏ：０．１〜５．０ｗｔ％、およびＷ：
０．１〜５．０ｗｔ％よりなる群より選択された少なく
とも一種（以下、Ｔｉ群という）。 （II）Ｎ：２００〜２０００ｐｐｍ， Ｍｎ：０．０１
〜２０ｗｔ％Ａｌ：０．０１〜５．０ｗｔ％， Ｃｕ：
０．１〜５．０ｗｔ％、およびＣｏ：０．１〜５．０ｗ
ｔ％よりなる群から選択された少なくとも一種（以下、
Ｎ群という）。 （III)Ｓｎ：０．０１〜１．０ｗｔ％， Ｓｂ：０．０
１〜１．０ｗｔ％，Ｐ：２００〜２０００ｐｐｍ，
Ｓｉ：０．１〜５．０ｗｔ％、およびＢ：３〜１００ｐ
ｐｍよりなる群より選択された少なくとも一種（以下、
Ｓｎ群という）。Hereinafter, the present invention will be described in more detail. As described above, the present invention provides a method for producing Cr: 15 to 50 wt%,
Ni: 6.1 to 50 wt%, C: 15 ppm or less, S: 50 ppm or less, O: 50 ppm
Contained below, the balance relates to Fe-Cr-Ni-based alloy excellent in deep drawability comprising Fe and unavoidable impurities,
Further, in addition to the above components, the following (I) and (I
The present invention relates to an Fe-Cr-Ni-based alloy excellent in deep drawability containing at least one selected from the three groups I) and (III). The deep drawability can be further improved by adding the elements of the following groups (I) to (III). (I) Ti: 0.01 to 1.0 wt%, Nb: 0.0
1 to 1.0 wt%, V: 0.01 to 1.0 wt%,
Zr: 0.01-1.0 wt%, Ta: 0.01-1.
0 wt%, Mo: 0.1 to 5.0 wt%, and W:
At least one selected from the group consisting of 0.1 to 5.0 wt% (hereinafter referred to as Ti group). (II) N: 200 to 2000 ppm, Mn: 0.01
２０20 wt% Al: 0.01-5.0 wt%, Cu:
0.1 to 5.0 wt%, and Co: 0.1 to 5.0 w
at least one selected from the group consisting of
N group). (III) Sn: 0.01 to 1.0 wt%, Sb: 0.0
1 to 1.0 wt%, P: 200 to 2000 ppm,
Si: 0.1 to 5.0 wt%, and B: 3 to 100 p
pm (hereinafter, at least one selected from the group consisting of
Sn group).
【０００８】以下に本発明の数値限定理由を述べる。The reasons for limiting the numerical values of the present invention will be described below.
【０００９】〔Ｃ〕図１に、実施例で述べる試験方法で
評価したＳＵＳ３０４の限界絞り比に及ぼすＣ量の影響
を示す。Ｃ量が減少していくと、１００ｐｐｍまでは限
界絞り比が低下する傾向にあるが、Ｃ量がさらに低下し
１５ｐｐｍ以下になると限界絞り比が著しく向上するこ
とを見い出した。その機構は必ずしも明らかではない
が、１００ｐｐｍまではＣ量が下がると加工に伴うマル
テンサイト変態が生じ易くなるために、フランジ部分の
加工硬化が大となり限界絞り比が低下するのに対し、さ
らにＣ量が下がった場合は同様にマルテンサイト変態は
生じるものの、マルテンサイト自身の強度が低下して、
また、マルテンサイトの分布が変化するために、全体と
しては加工硬化が抑制されること、および変形の多くを
受け持つオーステナイト相で深絞り加工に有利な集合組
成が発達して限界絞り比が向上したと考えられる。[C] FIG. 1 shows the effect of the amount of carbon on the limit drawing ratio of SUS304 evaluated by the test method described in the embodiment. It has been found that when the amount of C decreases, the limiting drawing ratio tends to decrease up to 100 ppm, but when the amount of C further decreases and becomes 15 ppm or less, the limiting drawing ratio is remarkably improved. Although the mechanism is not necessarily clear, when the C content is reduced to 100 ppm, the martensitic transformation accompanying the processing is apt to occur, so that the work hardening of the flange portion is increased and the limit drawing ratio is lowered, while the C content is further reduced. When the amount decreases, martensite transformation similarly occurs, but the strength of martensite itself decreases,
In addition, since the distribution of martensite changes, work hardening is suppressed as a whole, and the austenite phase, which is responsible for much of the deformation, has developed an aggregate composition advantageous for deep drawing and improved the limit drawing ratio. it is conceivable that.
【００１０】図２に、実施例で述べる試験方法で評価し
たＳＵＳ３１６の限界絞り比に及ぼすＣ量の影響を示
す。Ｃ量が減少していくと、３０ｐｐｍまでは限界絞り
比がほとんど変化しないが、１５ｐｐｍ以下になると著
しく向上することが分かる。以上のことから、本発明で
は、Ｃ量：１５ｐｐｍ以下を請求範囲とした。FIG. 2 shows the effect of the amount of carbon on the limit drawing ratio of SUS316 evaluated by the test method described in the examples. It can be seen that as the C content decreases, the limiting aperture ratio hardly changes up to 30 ppm, but it significantly improves at 15 ppm or less. Based on the above, in the present invention, the C content is 15 ppm or less.
【００１１】〔Ｓ〕図３に、実施例で述べる試験方法で
評価したＳＵＳ３０４の限界絞り比に及ぼすＳ量の影響
を示す。Ｓ量が減少していくと、５０ｐｐｍまでは限界
絞り比が向上し、５０ｐｐｍ以下ではほとんど変化しな
くなることが分かる。図４に、実施例で述べる試験方法
で評価したＳＵＳ３１６の限界絞り比に及ぼすＳ量の影
響を示す。Ｓ量が減少していくと、５０ｐｐｍまでは限
界絞り比が向上し、５０ｐｐｍ以下ではほとんど変化し
なくなることが分かる。以上のことから、本発明では、
Ｓ量：５０ｐｐｍ以下を請求範囲とした。[S] FIG. 3 shows the effect of the amount of S on the limit drawing ratio of SUS304 evaluated by the test method described in the embodiment. It can be seen that as the S content decreases, the limiting aperture ratio increases up to 50 ppm, and hardly changes at 50 ppm or less. FIG. 4 shows the effect of the amount of S on the limit drawing ratio of SUS316 evaluated by the test method described in the examples. It can be seen that as the S content decreases, the limiting aperture ratio increases up to 50 ppm, and hardly changes at 50 ppm or less. From the above, in the present invention,
S content: 50 ppm or less was defined as a claim.
【００１２】〔Ｏ〕図５に、実施例で述べる試験方法で
評価したＳＵＳ３０４の限界絞り比に及ぼすＯ量の影響
を示す。Ｏ量が減少していくと、５０ｐｐｍまでは限界
絞り比が向上し、５０ｐｐｍ以下ではほとんど変化しな
くなることが分かる。図６に、実施例で述べる試験方法
で評価したＳＵＳ３１６の限界絞り比に及ぼすＯ量の影
響を示す。Ｏ量が減少していくと、５０ｐｐｍまでは限
界絞り比が向上し、５０ｐｐｍ以下ではほとんど変化し
なくなることが分かる。以上のことから、本発明では、
Ｏ量：５０ｐｐｍを請求範囲とした。[O] FIG. 5 shows the effect of the amount of O on the limit drawing ratio of SUS304 evaluated by the test method described in the embodiment. It can be seen that as the amount of O decreases, the limiting aperture ratio increases up to 50 ppm, and hardly changes below 50 ppm. FIG. 6 shows the effect of the amount of O on the limit drawing ratio of SUS316 evaluated by the test method described in the examples. It can be seen that as the amount of O decreases, the limiting aperture ratio increases up to 50 ppm, and hardly changes below 50 ppm. From the above, in the present invention,
O content: 50 ppm was defined as a claim.
【００１３】〔Ｔｉ，Ｎｂ，Ｖ，Ｚｒ，Ｔａ，Ｍｏ，
Ｗ〕これらの元素は、Ｃを固定し、固溶Ｃ量を減少させ
て深絞りに有利な集合組成を発達させる元素であるが、
過剰に添加すると鋼が脆くなるので、本発明では、Ｔ
ｉ：０．０１〜１．０％、Ｎｂ：０．０１〜１．０％、
Ｖ：０．０１〜１．０％、Ｚｒ：０．０１〜１．０％、
Ｔａ：０．０１〜１．０％、Ｍｏ：０．１〜５．０％、
Ｗ：０．１〜５．０％のいずれか一種または二種以上を
請求範囲とした。[Ti, Nb, V, Zr, Ta, Mo,
W] These elements are elements that fix C, reduce the amount of solid solution C, and develop an aggregate composition advantageous for deep drawing.
If added in excess, the steel becomes brittle.
i: 0.01 to 1.0%, Nb: 0.01 to 1.0%,
V: 0.01 to 1.0%, Zr: 0.01 to 1.0%,
Ta: 0.01 to 1.0%, Mo: 0.1 to 5.0%,
W: Any one or more of 0.1 to 5.0% is included in the claims.
【００１４】〔Ｎ，Ｍｎ，Ａｌ，Ｃｕ，Ｃｏ〕これらの
元素は、冷延時のマルテンサイト変態を抑制して焼鈍時
に変態しオーステナイトの集合組成がランダムになるこ
とを抑制する元素であるが、過剰に添加しても、それぞ
れの効果が飽和してしまうので、本発明では、Ｎ：２０
０〜２０００ｐｐｍ、Ｍｎ：０．０１〜２０％、Ａｌ：
０．０１〜５．０％、Ｃｕ：０．１〜５．０％、Ｃｏ：
０．１〜５．０％のいずれか一種または二種以上を請求
範囲とした。[N, Mn, Al, Cu, Co] These elements are elements that suppress martensitic transformation during cold rolling and transform during annealing to suppress the austenite aggregate composition from becoming random. Even if it is excessively added, the respective effects are saturated.
0 to 2000 ppm, Mn: 0.01 to 20%, Al:
0.01 to 5.0%, Cu: 0.1 to 5.0%, Co:
Any one or more of 0.1 to 5.0% is included in the claims.
【００１５】〔Ｓｎ，Ｓｂ，Ｐ，Ｓｉ，Ｂ〕これらの元
素は、合金の強度を向上させて、深絞り成形性を向上さ
せる元素であるが、過剰に添加すると鋼が脆くなるの
で、本発明では、Ｓｎ：０．０１〜１．０％、Ｓｂ：
０．０１〜１．０％、Ｐ：２００〜２０００ｐｐｍ、Ｓ
ｉ：０．１〜５．０％、Ｂ：３〜１００ｐｐｍのいずれ
か一種または二種以上を請求範囲とした。[Sn, Sb, P, Si, B] These elements are elements that improve the strength of the alloy and improve the deep drawability. However, if added in excess, the steel becomes brittle. In the invention, Sn: 0.01 to 1.0%, Sb:
0.01 to 1.0%, P: 200 to 2000 ppm, S
Any one or two or more of i: 0.1 to 5.0% and B: 3 to 100 ppm were claimed.
【００１６】このような超高純度のＦｅ−Ｃｒ−Ｎｉ系
合金は、原料として高純度電解鉄と電解Ｃｒと電解Ｎｉ
を所定量用いることで製造される。いずれの原料も主た
る不純物は酸素であり、この酸素を除去するために１０
-7torrよりも高い超高真空下で溶解、鋳造することによ
り本発明の超高純度Ｆｅ−Ｃｒ−Ｎｉ系合金を製造する
ことができる。Such ultra-high-purity Fe-Cr-Ni-based alloys are obtained by using high-purity electrolytic iron, electrolytic Cr and electrolytic Ni as raw materials.
Is manufactured by using a predetermined amount. The main impurity of each raw material is oxygen.
The ultrahigh-purity Fe-Cr-Ni-based alloy of the present invention can be manufactured by melting and casting under an ultrahigh vacuum higher than -7 torr.
【００１７】また、本発明は、熱延焼鈍板、冷延焼鈍板
のいずれで用いられても十分な効果が生じ、また、冷延
焼鈍板においては、その表面仕上ダル、ブライト、光輝
焼鈍、ヘアライン、研磨、鏡面等のいずれを採用しても
かまわない。なお、本発明はオーステナイト相の加工性
を向上させることが目的であり、オーステナイト相が体
積割合で５０〜１００％であるＦｅ−Ｃｒ−Ｎｉ系合金
を対象とするときに著効がある。Further, the present invention provides a sufficient effect when used in any of a hot-rolled annealed sheet and a cold-rolled annealed sheet. In the cold-rolled annealed sheet, the surface finish dull, bright, bright annealing, Any of hairline, polishing, mirror surface, etc. may be adopted. The purpose of the present invention is to improve the workability of the austenite phase, and is particularly effective when the Fe-Cr-Ni-based alloy in which the austenite phase is 50 to 100% by volume is targeted.
【００１８】[0018]
【実施例】以下、実施例をもって本発明を具体的に説明
する。 （実施例）表１に示す化学成分を有する合金１０ｋｇを
真空溶解炉で溶製し、鋳造し、熱間圧延により板厚４ｍ
ｍの圧延板とし、再結晶を目的とした熱延板焼鈍を施
し、機械的方法によって脱スケールし、冷間圧延により
板厚０．８ｍｍの冷延板とし、アンモニア分解ガス中で
９５０℃の再結晶焼鈍を施して冷延焼鈍板を作製した。The present invention will be specifically described below with reference to examples. (Example) 10 kg of an alloy having the chemical components shown in Table 1 was melted in a vacuum melting furnace, cast, and hot-rolled to a thickness of 4 m.
m rolled plate, subjected to hot rolled sheet annealing for the purpose of recrystallization, descaled by a mechanical method, cold rolled into a 0.8 mm thick cold rolled sheet, and 950 ° C. Recrystallization annealing was performed to produce a cold-rolled annealed plate.
【００１９】表１に併せて前述の方法で得られた冷延焼
鈍板について、シワ押さえ力：１０００ｋｇｆ、ポン
チ：３２ｍｍφ円筒、潤滑：牛脂、絞り速度（ポンチ速
度）：１０mm/secの条件で Swift深絞り試験を行なった
結果を示す。本発明の範囲に含まれる（１）〜（３７）
は、限界絞り比が２．０以上で深絞り成形性が良好であ
るのに対し、Ｃ量が１５ｐｐｍを越える（３８）〜（４
３）、Ｓ量が５０ｐｐｍを越える（４４）〜（４８）、
Ｏ量が５０ｐｐｍを越える（４９）〜（５３）は、限界
絞り比が２．０未満で深絞り成形性が良好でない。With respect to the cold-rolled annealed plate obtained by the above-mentioned method in combination with Table 1, wrinkle holding force: 1000 kgf, punch: 32 mmφ cylinder, lubrication: tallow, drawing speed (punch speed): 10 mm / sec, Swift The result of performing the deep drawing test is shown. (1) to (37) included in the scope of the present invention
Indicates that the critical draw ratio is 2.0 or more and the deep drawability is good, whereas the C content exceeds 15 ppm (38) to (4).
3) the S content exceeds 50 ppm (44) to (48);
When the O content exceeds 50 ppm, the critical draw ratio is less than 2.0, and the deep drawability is not good.
【００２０】[0020]
【表１】 [Table 1]
【００２１】[0021]
【表２】 [Table 2]
【００２２】[0022]
【表３】 [Table 3]
【００２３】[0023]
【表４】 [Table 4]
【００２４】[0024]
【発明の効果】本発明のＦｅ−Ｃｒ−Ｎｉ系合金は、Ｃ
量を低下させることにより、深絞り成形に適切な集合組
成を生じ、また、その加工誘起マルテンサイトの延性が
向上するので、深絞り成形性に優れる。また、Ｃ量を低
下させているので、耐食性に優れるという特徴も有す
る。The Fe--Cr--Ni alloy of the present invention has a C
By reducing the amount, an aggregate composition suitable for deep drawing is produced, and the ductility of the process-induced martensite is improved, so that the deep drawing is excellent. Further, since the amount of carbon is reduced, it also has a feature of being excellent in corrosion resistance.
【図１】 実施例で述べた試験方法で評価したＳＵＳ３
０４の限界絞り比に及ぼすＣ量の影響を示す図である。FIG. 1 SUS3 evaluated by the test method described in the examples.
FIG. 9 is a diagram showing the influence of the amount of C on the limiting aperture ratio of No. 04.
【図２】 実施例で述べた試験方法で評価したＳＵＳ３
１６の限界絞り比に及ぼすＣ量の影響を示す図である。FIG. 2 shows SUS3 evaluated by the test method described in the examples.
It is a figure which shows the influence of the amount of C which has a limit throttle ratio of No. 16.
【図３】 実施例で述べた試験方法で評価したＳＵＳ３
０４の限界絞り比に及ぼすＳ量の影響を示す図である。FIG. 3 shows SUS3 evaluated by the test method described in the examples.
It is a figure which shows the influence of the S amount on the limiting aperture ratio of No. 04.
【図４】 実施例で述べた試験方法で評価したＳＵＳ３
１６の限界絞り比に及ぼすＳ量の影響を示す図である。FIG. 4 shows SUS3 evaluated by the test method described in the examples.
It is a figure which shows the influence of the amount of S which acts on the limiting aperture ratio of No. 16.
【図５】 実施例で述べた試験方法で評価したＳＵＳ３
０４の限界絞り比に及ぼすＯ量の影響を示す図である。FIG. 5 shows SUS3 evaluated by the test method described in the examples.
FIG. 9 is a diagram showing the influence of the amount of O on the limiting aperture ratio of No. 04.
【図６】 実施例で述べた試験方法で評価したＳＵＳ３
１６の限界絞り比に及ぼすＯ量の影響を示す図である。FIG. 6 shows SUS3 evaluated by the test method described in the examples.
It is a figure which shows the influence of the amount of O which acts on the 16th limiting aperture ratio.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 佐 藤 進 千葉県千葉市中央区川崎町１番地 川崎 製鉄株式会社技術研究本部内 (72)発明者 冨 樫 房 夫 千葉県千葉市中央区川崎町１番地 川崎 製鉄株式会社技術研究本部内 (56)参考文献 特開 平１−92342（ＪＰ，Ａ) 特開 平４−214841（ＪＰ，Ａ) 特開 平５−117813（ＪＰ，Ａ) 特開 昭63−312952（ＪＰ，Ａ) 特開 平４−272158（ＪＰ，Ａ) 特開 昭57−16152（ＪＰ，Ａ) 特開 平５−209228（ＪＰ，Ａ) (58)調査した分野(Int.Cl.7，ＤＢ名) C22C 38/00 302 C22C 38/40 ──────────────────────────────────────────────────の Continuing on the front page (72) Inventor Susumu Sato 1 Kawasaki-cho, Chuo-ku, Chiba-shi, Chiba Kawasaki-Steel Co., Ltd. (72) Inventor Fusao Togashi Kawasaki-cho, Chuo-ku, Chiba-shi, Chiba No. 1 Kawasaki Steel Corporation Research and Development Headquarters (56) References JP-A-1-92342 (JP, A) JP-A-4-214841 (JP, A) JP-A-5-117813 (JP, A) JP JP-A-63-312952 (JP, A) JP-A-4-272158 (JP, A) JP-A-57-16152 (JP, A) JP-A-5-209228 (JP, A) (58) Fields investigated (Int) .Cl. 7 , DB name) C22C 38/00 302 C22C 38/40
Claims (8)
６．１〜５０ｗｔ％，Ｃ：１５ｐｐｍ以下，
Ｓ：５０ｐｐｍ以下，Ｏ：５０ｐｐｍ以下含有し、残
部はＦｅおよび不可避的不純物よりなる深絞り成形性に
優れたＦｅ−Ｃｒ−Ｎｉ系合金。(1) Cr: 15 to 50 wt%, Ni:
6.1 to 50 wt%, C: 15 ppm or less,
Fe-Cr-Ni alloy containing S: 50 ppm or less, O: 50 ppm or less, and the balance is Fe and unavoidable impurities and excellent in deep drawing formability.
６．１〜５０ｗｔ％，Ｃ：１５ｐｐｍ以下，
Ｓ：５０ｐｐｍ以下，Ｏ：５０ｐｐｍ以下含有し、さ
らに、 Ｔｉ：０．０１〜１．０ｗｔ％， Ｎｂ：０．０１〜
１．０ｗｔ％，Ｖ：０．０１〜１．０ｗｔ％， Ｚ
ｒ：０．０１〜１．０ｗｔ％，Ｔａ：０．０１〜１．０
ｗｔ％， Ｍｏ：０．１〜５．０ｗｔ％、およびＷ：
０．１〜５．０ｗｔ％よりなる群より選択された少なく
とも一種を含有し、残部はＦｅおよび不可避的不純物よ
りなる深絞り成形性に優れたＦｅ−Ｃｒ−Ｎｉ系合金。2. Cr: 15 to 50 wt%, Ni:
6.1 to 50 wt%, C: 15 ppm or less,
S: 50 ppm or less, O: 50 ppm or less, Ti: 0.01 to 1.0 wt%, Nb: 0.01 to
1.0 wt%, V: 0.01 to 1.0 wt%, Z
r: 0.01 to 1.0 wt%, Ta: 0.01 to 1.0
wt%, Mo: 0.1 to 5.0 wt%, and W:
An Fe-Cr-Ni-based alloy containing at least one selected from the group consisting of 0.1 to 5.0 wt%, with the balance being Fe and unavoidable impurities, and excellent in deep drawing formability.
６．１〜５０ｗｔ％，Ｃ：１５ｐｐｍ以下，
Ｓ：５０ｐｐｍ以下，Ｏ：５０ｐｐｍ以下含有し、さ
らに、 Ｎ：２００〜２０００ｐｐｍ， Ｍｎ：０．０１〜
２０ｗｔ％Ａｌ：０．０１〜５．０ｗｔ％， Ｃｕ：
０．１〜５．０ｗｔ％、およびＣｏ：０．１〜５．０ｗ
ｔ％よりなる群から選択された少なくとも一種を含有
し、残部はＦｅおよび不可避的不純物よりなる深絞り成
形性に優れたＦｅ−Ｃｒ−Ｎｉ系合金。3. Cr: 15 to 50 wt%, Ni:
6.1 to 50 wt%, C: 15 ppm or less,
S: 50 ppm or less, O: 50 ppm or less, N: 200 to 2000 ppm, Mn: 0.01 to
20 wt% Al: 0.01-5.0 wt%, Cu:
0.1 to 5.0 wt%, and Co: 0.1 to 5.0 w
Fe-Cr-Ni-based alloy containing at least one selected from the group consisting of t% and the balance being Fe and unavoidable impurities and having excellent deep draw formability.
６．１〜５０ｗｔ％，Ｃ：１５ｐｐｍ以下，
Ｓ：５０ｐｐｍ以下，Ｏ：５０ｐｐｍ以下含有し、さ
らに、 Ｓｎ：０．０１〜１．０ｗｔ％， Ｓｂ：０．０１〜
１．０ｗｔ％，Ｐ：２００〜２０００ｐｐｍ， Ｓ
ｉ：０．１〜５．０ｗｔ％、およびＢ：３〜１００ｐｐ
ｍよりなる群より選択された少なくとも一種を含有し、
残部はＦｅおよび不可避的不純物よりなる深絞り成形性
に優れたＦｅ−Ｃｒ−Ｎｉ系合金。4. Cr: 15 to 50 wt%, Ni:
6.1 to 50 wt%, C: 15 ppm or less,
S: 50 ppm or less, O: 50 ppm or less, Sn: 0.01 to 1.0 wt%, Sb: 0.01 to
1.0 wt%, P: 200 to 2000 ppm, S
i: 0.1 to 5.0 wt%, and B: 3 to 100 pp
m, at least one selected from the group consisting of
The remainder is an Fe-Cr-Ni-based alloy which is excellent in deep drawability and consists of Fe and unavoidable impurities.
６．１〜５０ｗｔ％，Ｃ：１５ｐｐｍ以下，
Ｓ：５０ｐｐｍ以下，Ｏ：５０ｐｐｍ以下含有し、さ
らに、 Ｔｉ：０．０１〜１．０ｗｔ％， Ｎｂ：０．０１〜
１．０ｗｔ％，Ｖ：０．０１〜１．０ｗｔ％， Ｚ
ｒ：０．０１〜１．０ｗｔ％，Ｔａ：０．０１〜１．０
ｗｔ％， Ｍｏ：０．１〜５．０ｗｔ％、およびＷ：
０．１〜５．０ｗｔ％よりなる群より選択された少なく
とも一種を含有し、かつ、 Ｎ：２００〜２０００ｐｐｍ， Ｍｎ：０．０１〜２
０ｗｔ％，Ａｌ：０．０１〜５．０ｗｔ％， Ｃｕ：
０．１〜５．０ｗｔ％、およびＣｏ：０．１〜５．０ｗ
ｔ％よりなる群より選択された少なくとも一種を含有
し、残部はＦｅおよび不可避的不純物よりなる深絞り成
形性に優れたＦｅ−Ｃｒ−Ｎｉ系合金。5. Cr: 15 to 50 wt%, Ni:
6.1 to 50 wt%, C: 15 ppm or less,
S: 50 ppm or less, O: 50 ppm or less, Ti: 0.01 to 1.0 wt%, Nb: 0.01 to
1.0 wt%, V: 0.01 to 1.0 wt%, Z
r: 0.01 to 1.0 wt%, Ta: 0.01 to 1.0
wt%, Mo: 0.1 to 5.0 wt%, and W:
Containing at least one selected from the group consisting of 0.1 to 5.0 wt%, and N: 200 to 2000 ppm, Mn: 0.01 to 2
0 wt%, Al: 0.01 to 5.0 wt%, Cu:
0.1 to 5.0 wt%, and Co: 0.1 to 5.0 w
An Fe-Cr-Ni alloy containing at least one selected from the group consisting of t% and the balance being Fe and unavoidable impurities and having excellent deep draw formability.
６．１〜５０ｗｔ％，Ｃ：１５ｐｐｍ以下，
Ｓ：５０ｐｐｍ以下，Ｏ：５０ｐｐｍ以下含有し、さ
らに、 Ｔｉ：０．０１〜１．０ｗｔ％， Ｎｂ：０．０１〜
１．０ｗｔ％，Ｖ：０．０１〜１．０ｗｔ％， Ｚ
ｒ：０．０１〜１．０ｗｔ％，Ｔａ：０．０１〜１．０
ｗｔ％， Ｍｏ：０．１〜５．０ｗｔ％、およびＷ：
０．１〜５．０ｗｔ％よりなる群より選択された少なく
とも一種を含有し、かつ、 Ｓｎ：０．０１〜１．０ｗｔ％， Ｓｂ：０．０１〜
１．０ｗｔ％，Ｐ：２００〜２０００ｐｐｍ， Ｓ
ｉ：０．１〜５．０ｗｔ％、およびＢ：３〜１００ｐｐ
ｍよりなる群より選択された少なくとも一種を含有し、
残部はＦｅおよび不可避的不純物よりなる深絞り成形性
に優れたＦｅ−Ｃｒ−Ｎｉ系合金。6. Cr: 15 to 50 wt%, Ni:
6.1 to 50 wt%, C: 15 ppm or less,
S: 50 ppm or less, O: 50 ppm or less, Ti: 0.01 to 1.0 wt%, Nb: 0.01 to
1.0 wt%, V: 0.01 to 1.0 wt%, Z
r: 0.01 to 1.0 wt%, Ta: 0.01 to 1.0
wt%, Mo: 0.1 to 5.0 wt%, and W:
It contains at least one selected from the group consisting of 0.1 to 5.0 wt%, and Sn: 0.01 to 1.0 wt%, Sb: 0.01 to
1.0 wt%, P: 200 to 2000 ppm, S
i: 0.1 to 5.0 wt%, and B: 3 to 100 pp
m, at least one selected from the group consisting of
The remainder is an Fe-Cr-Ni-based alloy which is excellent in deep drawability and consists of Fe and unavoidable impurities.
６．１〜５０ｗｔ％，Ｃ：１５ｐｐｍ以下，
Ｓ：５０ｐｐｍ以下，Ｏ：５０ｐｐｍ以下含有し、さ
らに、 Ｎ：２００〜２０００ｐｐｍ， Ｍｎ：０．０１〜
２０ｗｔ％Ａｌ：０．０１〜５．０ｗｔ％， Ｃｕ：
０．１〜５．０ｗｔ％、およびＣｏ：０．１〜５．０ｗ
ｔ％よりなる群から選択された少なくとも一種を含有
し、かつ、 Ｓｎ：０．０１〜１．０ｗｔ％， Ｓｂ：０．０１〜
１．０ｗｔ％，Ｐ：２００〜２０００ｐｐｍ， Ｓ
ｉ：０．１〜５．０ｗｔ％、およびＢ：３〜１００ｐｐ
ｍよりなる群より選択された少なくとも一種を含有し、
残部はＦｅおよび不可避的不純物よりなる深絞り成形性
に優れたＦｅ−Ｃｒ−Ｎｉ系合金。7. Cr: 15 to 50 wt%, Ni:
6.1 to 50 wt%, C: 15 ppm or less,
S: 50 ppm or less, O: 50 ppm or less, N: 200 to 2000 ppm, Mn: 0.01 to
20 wt% Al: 0.01-5.0 wt%, Cu:
0.1 to 5.0 wt%, and Co: 0.1 to 5.0 w
At least one selected from the group consisting of t%, Sn: 0.01 to 1.0 wt%, Sb: 0.01 to
1.0 wt%, P: 200 to 2000 ppm, S
i: 0.1 to 5.0 wt%, and B: 3 to 100 pp
m, at least one selected from the group consisting of
The remainder is an Fe-Cr-Ni-based alloy which is excellent in deep drawability and consists of Fe and unavoidable impurities.
６．１〜５０ｗｔ％，Ｃ：１５ｐｐｍ以下，
Ｓ：５０ｐｐｍ以下，Ｏ：５０ｐｐｍ以下含有し、さ
らに、 Ｔｉ：０．０１〜１．０ｗｔ％， Ｎｂ：０．０１〜
１．０ｗｔ％，Ｖ：０．０１〜１．０ｗｔ％， Ｚ
ｒ：０．０１〜１．０ｗｔ％，Ｔａ：０．０１〜１．０
ｗｔ％， Ｍｏ：０．１〜５．０ｗｔ％、およびＷ：
０．１〜５．０ｗｔ％よりなる群より選択された少なく
とも一種を含有し、かつ、 Ｎ：２００〜２０００ｐｐｍ， Ｍｎ：０．０１〜２
０ｗｔ％，Ａｌ：０．０１〜５．０ｗｔ％， Ｃｕ：
０．１〜５．０ｗｔ％、およびＣｏ：０．１〜５．０ｗ
ｔ％よりなる群より選択された少なくとも一種を含有
し、かつ、 Ｓｎ：０．０１〜１．０ｗｔ％， Ｓｂ：０．０１〜
１．０ｗｔ％，Ｐ：２００〜２０００ｐｐｍ， Ｓ
ｉ：０．１〜５．０ｗｔ％，およびＢ：３〜１００ｐｐ
ｍよりなる群より選択された少なくとも一種を含有し、
残部はＦｅおよび不可避的不純物よりなる深絞り成形性
に優れたＦｅ−Ｃｒ−Ｎｉ系合金。8. Cr: 15 to 50 wt%, Ni:
6.1 to 50 wt%, C: 15 ppm or less,
S: 50 ppm or less, O: 50 ppm or less, Ti: 0.01 to 1.0 wt%, Nb: 0.01 to
1.0 wt%, V: 0.01 to 1.0 wt%, Z
r: 0.01 to 1.0 wt%, Ta: 0.01 to 1.0
wt%, Mo: 0.1 to 5.0 wt%, and W:
Containing at least one selected from the group consisting of 0.1 to 5.0 wt%, and N: 200 to 2000 ppm, Mn: 0.01 to 2
0 wt%, Al: 0.01 to 5.0 wt%, Cu:
0.1 to 5.0 wt%, and Co: 0.1 to 5.0 w
At least one selected from the group consisting of t%, Sn: 0.01-1.0 wt%, Sb: 0.01-
1.0 wt%, P: 200 to 2000 ppm, S
i: 0.1 to 5.0 wt%, and B: 3 to 100 pp
m, at least one selected from the group consisting of
The remainder is an Fe-Cr-Ni-based alloy which is excellent in deep drawability and consists of Fe and unavoidable impurities.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP26208493A JP3236713B2 (en) | 1993-10-20 | 1993-10-20 | Fe-Cr-Ni alloy with excellent deep drawability |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP26208493A JP3236713B2 (en) | 1993-10-20 | 1993-10-20 | Fe-Cr-Ni alloy with excellent deep drawability |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH07118809A JPH07118809A (en) | 1995-05-09 |
| JP3236713B2 true JP3236713B2 (en) | 2001-12-10 |
Family
ID=17370811
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP26208493A Expired - Fee Related JP3236713B2 (en) | 1993-10-20 | 1993-10-20 | Fe-Cr-Ni alloy with excellent deep drawability |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3236713B2 (en) |
Families Citing this family (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE19631712C2 (en) * | 1996-07-13 | 2001-08-02 | Schmidt & Clemens | Use of an austenitic chromium-nickel-molybdenum steel alloy |
| DE19628350B4 (en) * | 1996-07-13 | 2004-04-15 | Schmidt & Clemens Gmbh & Co | Use of a stainless ferritic-austenitic steel alloy |
| DE19781031T1 (en) * | 1996-09-27 | 1998-12-17 | Nippon Yakin Kogyo Co Ltd | Austenitic stainless steel with antimicrobial properties and process for its manufacture |
| WO2017168640A1 (en) * | 2016-03-30 | 2017-10-05 | 株式会社日立製作所 | Chromium-based two-phase alloy product and method for producing same |
| WO2018186298A1 (en) * | 2017-04-03 | 2018-10-11 | 日立金属株式会社 | Cr-Fe-Ni-BASED ALLOY PRODUCT AND METHOD FOR MANUFACTURING SAME |
Family Cites Families (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5716152A (en) * | 1980-06-30 | 1982-01-27 | Nippon Yakin Kogyo Co Ltd | Austenite-containing stainless steel having deep drawing property |
| JPS63312952A (en) * | 1987-06-16 | 1988-12-21 | Nippon Mining Co Ltd | Material for piezoelectric oscillator case |
| JPH0192342A (en) * | 1987-10-05 | 1989-04-11 | Kawasaki Steel Corp | Austenitic stainless steel plate having excellent deep drawability |
| JP3068861B2 (en) * | 1990-12-14 | 2000-07-24 | 日新製鋼株式会社 | Stainless steel for engine gasket excellent in moldability and method of manufacturing the same |
| JPH04272158A (en) * | 1991-02-28 | 1992-09-28 | Nippon Stainless Steel Co Ltd | Nonmagnetic stainless steel having low work hardenability |
| JP3096076B2 (en) * | 1991-03-13 | 2000-10-10 | 川崎製鉄株式会社 | Manufacturing method of cold rolled steel sheet for ultra deep drawing with excellent local deformability |
| JPH05117813A (en) * | 1991-04-18 | 1993-05-14 | Nisshin Steel Co Ltd | Stainless steel for metal gasket having excellent formability and fatigue characteristic and this manufacture |
-
1993
- 1993-10-20 JP JP26208493A patent/JP3236713B2/en not_active Expired - Fee Related
Also Published As
| Publication number | Publication date |
|---|---|
| JPH07118809A (en) | 1995-05-09 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JP2807566B2 (en) | Austenitic high manganese steel having excellent formability, strength and weldability, and method for producing the same | |
| JP2005015909A (en) | High-strength low-specific-gravity steel sheet and method for manufacturing the same | |
| JP3064871B2 (en) | Ferritic stainless steel hot-rolled steel sheet with excellent roughening resistance and high temperature fatigue properties after forming | |
| JP7268182B2 (en) | Ferritic stainless steel sheet, manufacturing method thereof, and ferritic stainless steel member | |
| JP3236713B2 (en) | Fe-Cr-Ni alloy with excellent deep drawability | |
| JP3296599B2 (en) | Thin steel sheet for press working with high tensile rigidity and excellent press formability | |
| JP3247244B2 (en) | Fe-Cr-Ni alloy with excellent corrosion resistance and workability | |
| JP3245356B2 (en) | Austenitic stainless cold-rolled steel sheet excellent in stretch formability and method for producing the same | |
| JP3142427B2 (en) | Ferritic stainless steel sheet excellent in secondary work brittleness resistance and method for producing the same | |
| JP6279118B1 (en) | High-strength duplex stainless steel with excellent corrosion resistance and bending workability | |
| JPH0717946B2 (en) | Method for producing duplex stainless steel with excellent resistance to concentrated sulfuric acid corrosion | |
| JP2001271143A (en) | Ferritic stainless steel excellent in ridging resistance and its production method | |
| JP2828793B2 (en) | High-strength cold-rolled steel sheet excellent in deep drawability, chemical conversion property, secondary work brittleness resistance and spot weldability, and method for producing the same | |
| JPH07126758A (en) | Manufacture of ferritic stainless steel sheet excellent in bendability | |
| JP3299287B2 (en) | High strength steel sheet for forming and its manufacturing method | |
| JPH11279682A (en) | High strength steel sheet good in workability and spot weldability and its production | |
| JP2755014B2 (en) | Method for producing high-strength cold-rolled steel sheet for deep drawing with excellent secondary work brittleness resistance | |
| JP2658706B2 (en) | Manufacturing method of high strength and high ductility cold rolled steel sheet with excellent aging resistance | |
| JP3023014B2 (en) | Cold rolled mild steel sheet for ultra deep drawing | |
| CN111868286B (en) | Steel plate | |
| JP3288456B2 (en) | Manufacturing method of cold drawn steel sheet for deep drawing with excellent corrosion resistance | |
| JP3449028B2 (en) | Ferritic steel with excellent high temperature fatigue properties | |
| JP2518795B2 (en) | Soft austenitic stainless steel with excellent hot workability | |
| JP3234642B2 (en) | High tensile cold rolled steel sheet for deep drawing and method for producing the same | |
| JP2876966B2 (en) | Cold rolled steel sheet with excellent low temperature bake hardenability |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| A01 | Written decision to grant a patent or to grant a registration (utility model) |
Free format text: JAPANESE INTERMEDIATE CODE: A01 Effective date: 20010904 |
|
| LAPS | Cancellation because of no payment of annual fees |