JPH0742550B2 - Stainless steel with excellent strength and ductility - Google Patents
Stainless steel with excellent strength and ductilityInfo
- Publication number
- JPH0742550B2 JPH0742550B2 JP2271338A JP27133890A JPH0742550B2 JP H0742550 B2 JPH0742550 B2 JP H0742550B2 JP 2271338 A JP2271338 A JP 2271338A JP 27133890 A JP27133890 A JP 27133890A JP H0742550 B2 JPH0742550 B2 JP H0742550B2
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- steel
- ductility
- aging
- stainless steel
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Description
【発明の詳細な説明】 （産業上の利用分野） 本発明は強度および延性が要求される部品、例えば薄板
バネ、自動車やオートバイ等のエンジンを構成する金属
ガスケット部品、あるいはSi単結晶切断用刃物等の素材
に用いられるステンレス鋼に関するものである。特に、
冷間圧延を施した素材を各種部品に成形後時効硬化させ
て使用する部品、冷えば金属ガスケット部品等の素材に
適したステンレス鋼に関するものである。DETAILED DESCRIPTION OF THE INVENTION (Industrial field of application) The present invention relates to parts required to have strength and ductility, for example, thin leaf springs, metal gasket parts constituting engines of automobiles and motorcycles, or a blade for cutting a Si single crystal. The present invention relates to stainless steel used for materials such as. In particular,
TECHNICAL FIELD The present invention relates to a stainless steel suitable for a material such as a cold-rolled material that is used after being molded into various parts and then age-hardened, and a metal gasket part when cooled.
（従来の技術） 従来、上記部品の素材には冷間圧延し加工硬化させたス
テンレス鋼や析出硬化型のステンレス鋼が使用されてき
た。(Prior Art) Conventionally, cold rolled and work hardened stainless steel or precipitation hardened stainless steel has been used as a material for the above parts.
冷間加工により強度を上げるステンレス鋼としては、SU
S301鋼のように冷間加工中にマルテンサイト相を生じせ
しめて強度を上げる鋼種と、Mn、Ｎ等の加工硬化能を上
げる元素を添加した鋼種がある。しかしこれらの鋼種は
いずれも高い強度を得るために、相当量の冷間加工が必
要であり、延性が低いという問題がある。As a stainless steel whose strength is increased by cold working, SU
There are steel grades such as S301 steel that produce a martensite phase during cold working to increase strength, and steel grades that contain elements such as Mn and N that enhance work hardening ability. However, all of these steel grades require a considerable amount of cold working in order to obtain high strength, and have a problem of low ductility.
析出硬化型のステンレス鋼としては、微細なCu相を析出
させるSUS630鋼や、NiとAlの金属間化合物を析出させる
SUS631鋼等が一般に使用されている。しかし熱処理によ
るマルテンサイト相を利用するSUS630鋼では引張強度が
高々160kg f/mm2である。また冷間加工によって生じる
マルテンサイト相を利用するSUS631鋼においては引張強
度は190kg f/mm2程度まで引き出すことができるが、強
度上昇による延性低下が大きい。さらにAlを多量に添加
するSUS631鋼においては非金属介在物が鋼中に残存しや
すく、靭性あるいは疲労強度の低下を招く場合がある。As precipitation hardening type stainless steel, SUS630 steel which precipitates fine Cu phase and intermetallic compound of Ni and Al are precipitated.
SUS631 steel is generally used. However, the tensile strength of SUS630 steel, which utilizes the martensitic phase by heat treatment, is at most 160 kg f / mm 2 . In addition, the tensile strength of SUS631 steel, which utilizes the martensitic phase generated by cold working, can be pulled up to about 190 kg f / mm 2, but the ductility is greatly reduced due to the increase in strength. Furthermore, in SUS631 steel in which a large amount of Al is added, nonmetallic inclusions are likely to remain in the steel, which may lead to a decrease in toughness or fatigue strength.
さらに近年、上記の従来鋼種より強度の高い析出硬化ス
テンレス鋼が提案されている。特開昭61−295356号公報
ではCuとSiを添加した高強度ステンレス鋼を提案してい
るが、成形加工を施す冷間圧延ままの状態での延性およ
び時効処理した状態での延性はいずれも低く、強度と延
性のバランスからは不十分である。また太田鶏一らも、
SiおよびCuを添加した析出硬化型ステンレス鋼を報告し
ている（鉄と鋼（1978）,S386）が、溶体化熱処理後の
冷却中に生じるマルテンサイト相を利用しているため、
引張強度が不十分である。Furthermore, in recent years, precipitation hardening stainless steels having higher strength than the above conventional steel grades have been proposed. Japanese Unexamined Patent Publication No. 61-295356 proposes a high-strength stainless steel to which Cu and Si are added. Low, insufficient in terms of balance between strength and ductility. Also, Ota Toriichi,
A precipitation-hardening stainless steel containing Si and Cu has been reported (iron and steel (1978), S386), but it utilizes the martensite phase that occurs during cooling after solution heat treatment.
Insufficient tensile strength.
（発明が解決しようとする課題） 本発明は薄板ばね、金属ガスケット等の強度および延性
が要求される部品の素材として使用できる強度、延性の
優れたステンレス鋼を提供することを目的とするもので
ある。(Problems to be Solved by the Invention) An object of the present invention is to provide a stainless steel having excellent strength and ductility that can be used as a material for components such as thin leaf springs and metal gaskets that require strength and ductility. is there.
（課題を解決するための手段） 本発明は従来鋼の問題点を克服し、強度と延性の優れた
ステンレス鋼、つまり強度−延性バランスの優れたステ
ンレス鋼の成分を見出したものである。本発明鋼は溶体
化状態で準安定オーステナイト相からなるように成分調
整されており、その後の冷間圧延あるいは冷間加工によ
ってオーステナイト相の一部がマルテンサイト相に変態
する。さらにその後の時効処理によって目的とする強度
レベルを実現するために、Siを添加している。本発明鋼
の第一の特徴は、SUS301等に比較して軽度の冷間圧延あ
るいは冷間加工でマルテンサイト相が形成され、またＮ
を0.05〜0.20％含有させマルテンサイト相を強化してい
るため、冷間圧延のままの状態でSUS301程度の強度を示
しながら十分な延性を確保している点である。従ってこ
の状態での加工性は従来のSUS301鋼等より極めて良好で
ある。第二の特徴は、冷間圧延後あるいは冷間加工後に
最適な時効処理を施すことにより強度が飛躍的に上昇す
ることである。この時効による強度上昇は、時効中にマ
ルテンサイト中に（Ni、Cr）3Si金属間化合物が微細に
析出するためであり、十分な効果を得るためには3.0％
を越えるSiの添加が必要である。従来の析出硬化型のス
テンレス鋼に比べその強度上昇は大きく、しかも時効に
よる延性低下も小さい。すなわち本発明鋼の時効後の強
度−延性バランスは従来鋼に比べ優れている。(Means for Solving the Problems) The present invention has overcome the problems of conventional steels and has found the components of stainless steel having excellent strength and ductility, that is, stainless steel having an excellent strength-ductility balance. The composition of the steel of the present invention is adjusted so as to be composed of a metastable austenite phase in a solution state, and a part of the austenite phase is transformed into a martensite phase by subsequent cold rolling or cold working. Further, Si is added to achieve the desired strength level by the subsequent aging treatment. The first feature of the steel of the present invention is that a martensite phase is formed by cold rolling or cold working which is lighter than that of SUS301 and the like.
Is strengthened in the martensite phase by containing 0.05 to 0.20% of Al, so that sufficient ductility is ensured while exhibiting strength of approximately SUS301 in the state as cold rolled. Therefore, the workability in this state is much better than that of the conventional SUS301 steel. The second feature is that the strength is dramatically increased by performing an optimum aging treatment after cold rolling or cold working. The increase in strength due to this aging is due to the fine precipitation of the (Ni, Cr) 3 Si intermetallic compound in martensite during aging, and 3.0% is required to obtain a sufficient effect.
It is necessary to add more than Si. Compared to the conventional precipitation hardening type stainless steel, its strength is greatly increased, and the deterioration of ductility due to aging is small. That is, the strength-ductility balance of the steel of the present invention after aging is superior to that of the conventional steel.
（作 用） まず、本発明鋼の成分限定理由について述べる。(Operation) First, the reasons for limiting the components of the steel of the present invention will be described.
Ｃは冷間圧延によって生じるマルテンサイトを強化する
には有効な元素であるが、Ｎによる強化に比べ延性低下
が大きいことと、時効時にCr炭化物が粒界析出し粒界腐
食割れ感受性が高くなることから、Ｃ含有量は0.03％以
下とした。C is an effective element for strengthening martensite produced by cold rolling, but it has a large ductility reduction compared to strengthening by N, and Cr carbide precipitates at grain boundaries during aging, resulting in increased intergranular corrosion cracking susceptibility. Therefore, the C content is set to 0.03% or less.
Siは時効による強度上昇を大きくする最も重要な元素で
ある。この時効硬化はマルテンサイト相中の微細な（N
i、Cr）3Si金属間化合物の析出によるものであるが、鋼
中のSi含有量が3.0％以下では、十分に析出せず強度の
上昇が小さい。しかし5.0％を越えて添加すると、高温
で多量のδフェライトが生成するため熱間加工性が著し
く低下し製造が困難となるため、Si含有量は3.0％超〜
5.0％とした。Si is the most important element that greatly increases the strength due to aging. This age hardening is due to the fine (N
This is due to the precipitation of the intermetallic compound of (i, Cr) 3 Si, but if the Si content in the steel is 3.0% or less, the precipitation is not sufficient and the increase in strength is small. However, if added in excess of 5.0%, a large amount of δ-ferrite will be generated at high temperature, resulting in a marked decrease in hot workability and difficulty in manufacturing.
It was set to 5.0%.
MnはＮの固溶量を増加させるとともに、δフェライトの
生成を抑制するのに有効な元素である。0.05〜0.20％の
Ｎ含有量を確保するためにはMn含有量は1.0％超とする
ことが必要であるが、5.0％を超えるとオーステナイト
相が安定化し、冷間圧延あるいは冷間加工時のマルテン
サイト相の変態が抑制されるため、Mnの含有量は1.0％
超〜5.0％に限定した。Mn is an element effective in increasing the solid solution amount of N and suppressing the formation of δ ferrite. In order to secure the N content of 0.05 to 0.20%, it is necessary that the Mn content exceeds 1.0%, but if it exceeds 5.0%, the austenite phase is stabilized, and cold rolling or cold working occurs. The content of Mn is 1.0% because the transformation of martensite phase is suppressed.
Limited to super ~ 5.0%.
Crは耐食性上必須の元素で、ステンレス鋼として目的の
耐食性を付与し、溶体化処理後冷却中に生じるマルテン
サイトを抑制するためには13％以上のCr含有量が必要で
ある。しかしCrを多量に添加すると高温で多量のδフェ
ライトが生成し、熱間加工性を劣化させるのみならず、
溶体化処理後も多量のδフェライトが残存し、強度およ
び延性を低下させる。このδフェライトの生成を抑制す
るために、Ｃ、Ｎ、Ni等のオーステナイト生成元素を多
く添加すると、オーステナイト相が常温でより安定化
し、冷間圧延または冷間加工によって適量のマルテンサ
イトを生成することが難しくなる。常温で準安定なオー
ステナイト相を得るための合金バランスを考慮してCr含
有量の上限は17％とした。Cr is an essential element in terms of corrosion resistance, and 13% or more of Cr content is necessary to impart the desired corrosion resistance as stainless steel and suppress martensite generated during cooling after solution treatment. However, if a large amount of Cr is added, a large amount of δ ferrite is generated at high temperature, which not only deteriorates hot workability,
Even after the solution treatment, a large amount of δ-ferrite remains, which reduces strength and ductility. If a large amount of austenite-forming elements such as C, N, and Ni are added to suppress the formation of this δ ferrite, the austenite phase becomes more stable at room temperature, and an appropriate amount of martensite is formed by cold rolling or cold working. Becomes difficult. The upper limit of Cr content was set to 17% in consideration of the alloy balance for obtaining a metastable austenite phase at room temperature.
Niは溶体化処理後の組織をオーステナイトにする基本的
な元素で、含有量が５％未満では、溶体化処理後の冷却
中にマルテンサイトが生成する。このマルテンサイト相
は冷間圧延中あるいは冷間加工中に生成するマルテンサ
イト相に比べ強度が低いため、目的の強度を得られな
い。またNi含有量が８％以上となるオーステナイトが安
定化し、冷間圧延あるいは冷間加工によってマルテンサ
イト相が生成しなくなるため、その上限は８％未満とし
た。Ni is a basic element that makes the structure after solution treatment austenite, and if the content is less than 5%, martensite is generated during cooling after solution treatment. Since this martensite phase has a lower strength than the martensite phase formed during cold rolling or cold working, the desired strength cannot be obtained. Further, since the austenite having a Ni content of 8% or more is stabilized and the martensite phase is not formed by cold rolling or cold working, the upper limit is set to less than 8%.
Ｎはマルテンサイト相を強化すると同時に、残留オース
テナイト相をも強化させる重要な元素である。Ｃもマル
テンサイトあるいは残留オーステナイトの強化には有効
であるが、強化による延性低下が大きい。本発明鋼では
強化による延性低下の少ないＮを添加したことが特徴で
ある。このマルテンサイト相あるいは残留オーステナイ
ト相の強化に十分な効果を得るためには、Ｎは0.05％以
上必要であるが、0.20％を越えて添加すると鋳造時に多
数のブローホールが生成するため、その上限は0.20％と
した。N is an important element that strengthens not only the martensite phase but also the retained austenite phase. C is also effective for strengthening martensite or retained austenite, but the decrease in ductility due to strengthening is large. The steel of the present invention is characterized by the addition of N, which causes less reduction in ductility due to strengthening. In order to obtain a sufficient effect for strengthening this martensite phase or retained austenite phase, N must be 0.05% or more, but if it is added in excess of 0.20%, a large number of blowholes will be formed during casting, so its upper limit is set. Was 0.20%.
本発明鋼が従来鋼より高強度、高延性を実現するために
は上記成分範囲で十分であるが、本発明鋼の熱間加工性
を良好に維持し、熱間圧延等において割れ、疵を防止す
るためにはAl、Caあるいはランタノイド系希土類元素の
微量添加が有効である。しかしこれら元素を過剰に添加
すると酸化物等の介在物の形で多数鋼中に残存すること
になり、延性あるいは疲労強度を低下させるため、その
添加量の範囲はAlで0.01〜0.20％、ランタノイド系希土
類元素で0.002〜0.050％、Caで0.001〜0.020％とした。
なおランタノイド系希土類元素の含有量は、La、Ce、P
r、Nd等のランタノイド系元素の含有量の総量である。The present invention steel has a higher strength than the conventional steel, the above composition range is sufficient to achieve high ductility, while maintaining good hot workability of the present invention steel, cracking in hot rolling, etc. In order to prevent it, it is effective to add a trace amount of Al, Ca or lanthanoid rare earth elements. However, if these elements are added excessively, they will remain in many steels in the form of inclusions such as oxides, which will lower the ductility or fatigue strength, so the range of addition is 0.01 to 0.20% for Al, lanthanoids. The rare earth elements were 0.002 to 0.050% and Ca was 0.001 to 0.020%.
The contents of lanthanoid rare earth elements are La, Ce, P
It is the total content of lanthanoid elements such as r and Nd.
さらに溶製中に不可避的に混入してくるＰ、Ｓは極力低
いことが望ましく、Ｐは応力腐食割れの観点から、また
ＳはMnSを形成し延性低下をもたらすことから、それぞ
れの含有量は0.05％以下、0.005％以下とすることが望
ましい。Furthermore, it is desirable that P and S, which are inevitably mixed during melting, be as low as possible. P is from the viewpoint of stress corrosion cracking, and S forms MnS, which leads to a decrease in ductility. It is desirable to set it to 0.05% or less and 0.005% or less.
本発明鋼は加工硬化型高強度ステンレス鋼として、冷間
圧延ままでも使用することができる。本発明鋼では溶体
化状態でのオーステナイト相の安定度が低いこととＮ添
加による強化のため、少ない圧延率で硬いマルテンサイ
ト相が生成し、強度が上昇する。さらに強度上昇に伴う
延性低下が従来鋼に比較して小さい利点を有する。しか
し本発明鋼の最大の特徴はその冷間圧延後の時効処理に
よって強度が著しく上昇することである。以下にこの特
徴を最大限に活かす製造方法について説明する。The steel of the present invention can be used as cold-rolled as work hardening type high strength stainless steel. In the steel of the present invention, since the stability of the austenite phase in the solution state is low and the strengthening by the addition of N, a hard martensite phase is generated with a small rolling rate, and the strength is increased. Further, it has an advantage that the decrease in ductility due to the increase in strength is smaller than that of conventional steel. However, the greatest feature of the steel of the present invention is that its strength is remarkably increased by the aging treatment after the cold rolling. A manufacturing method that makes the most of this feature will be described below.
本発明鋼は溶製後、熱間圧延あるいはさらに冷間圧延を
行った後、溶体化熱処理により全部あるいは大部分の組
織を準安定なオーステナイト相に調整する。この時の溶
体化熱処理条件としては、900〜1200℃の温度範囲が望
ましく、溶体化温度が低温すぎると前工程で生じた析出
物を十分固溶化することができず、また高温すぎると強
度、延性に有害なδフェライトが多量に生成する。The steel of the present invention is melted and then hot-rolled or cold-rolled, and then solution heat treatment is performed to adjust all or most of the structure to a metastable austenite phase. As the solution heat treatment conditions at this time, a temperature range of 900 to 1200 ° C. is desirable, and if the solution temperature is too low, the precipitates generated in the previous step cannot be sufficiently solid-soluted, and if the temperature is too high, the strength, A large amount of δ ferrite, which is harmful to ductility, is generated.
溶体化熱処理後、冷間圧延によって導入される歪を使っ
て、準安定オーステナイト相をマルテンサイト相に変態
せしめる。時効熱処理後に十分な強度を得るためには十
分な量のマルテンサイト相が必要であり、そのためには
冷間圧延での圧下比が10％以上必要である。また時効処
理後の強度にはこの段階での圧下率が強く影響し、圧下
率が大きいほど時効処理による強度上昇が大きい一方
で、時効による延性低下もやや大きくなる。従って最終
製品に要求される強度および延性を考え、それに合わせ
て冷間圧延率を決定することが望ましい。After the solution heat treatment, the strain introduced by cold rolling is used to transform the metastable austenite phase to the martensite phase. A sufficient amount of martensite phase is required to obtain sufficient strength after the aging heat treatment, and for this purpose, the reduction ratio in cold rolling is required to be 10% or more. Further, the strength after aging treatment is strongly affected by the rolling reduction at this stage, and the larger the rolling reduction, the greater the increase in strength due to aging treatment, but the slightly lower ductility due to aging. Therefore, it is desirable to consider the strength and ductility required for the final product and to determine the cold rolling rate accordingly.
冷間圧延ままでの状態では、時効熱処理後に比べ材料強
度も低く、また延性も従来の加工硬化型高強度ステンレ
ス鋼に比べ高いため、加工性は良好である。従ってこの
段階で各種バネ、金属ガスケット等に加工を行うことが
望ましい。In the state as cold-rolled, the material strength is lower than that after the aging heat treatment, and the ductility is higher than that of the conventional work-hardening high-strength stainless steel, so the workability is good. Therefore, it is desirable to process various springs, metal gaskets, etc. at this stage.
冷間圧延後、あるいは冷間加工した後に行う時効熱処理
としては、300〜600℃の温度範囲内で0.1〜30時間加熱
することが適切である。つまり、300℃未満では時効に
よる強度上昇が十分現れず、600℃越えて加熱するとマ
ルテンサイト相の一部がオーステナイト相に逆変態し、
時効熱処理によって逆に強度が低下する。また0.1時間
未満の加熱時間では時効による強度上昇が十分現れず、
30時間を越えて加熱しても強度上昇効果は飽和し、製造
工程上意味を持たない。As the aging heat treatment performed after cold rolling or after cold working, heating within a temperature range of 300 to 600 ° C. for 0.1 to 30 hours is appropriate. That is, if the temperature is lower than 300 ° C, the strength does not sufficiently increase due to aging, and if the temperature is higher than 600 ° C, a part of the martensite phase reversely transforms into an austenite phase,
On the contrary, the strength is lowered by the aging heat treatment. Also, if the heating time is less than 0.1 hours, the strength increase due to aging does not appear sufficiently,
Even if it is heated for more than 30 hours, the strength increasing effect is saturated and has no meaning in the manufacturing process.
（実施例） 実施例１ 第１表のＢ〜Ｆに示す化学成分を有する本発明鋼と、Ｋ
〜Ｎに示す比較鋼を実験室の真空溶解炉にて溶製し、熱
間圧延にて3.0mm厚の熱延板を作製した。また第１表の
Ｈ〜Ｊに示す従来鋼は通常の製造工程で溶製し、3.0mm
厚まで熱間圧延したものを使用した。この熱延板を1100
℃で焼鈍した後、冷間圧延機で0.5mm厚まで圧延し、105
0℃で１分間保持した後、直ちに水冷する溶体化処理を
行った。溶体化処理後、マルテンサイト相を生成せしめ
る冷間圧延を行った。この冷間圧延ままでの引張強度、
伸びおよび硬さを調査した。次にこの冷間圧延板に450
℃で１時間の時効熱処理を施し、空冷した。そして時効
後の引張強度、伸びおよび硬さも調査し、時効の効果を
確認した。(Example) Example 1 Steels of the present invention having chemical components shown in B to F of Table 1 and K
Comparative steels shown by to N were melted in a vacuum melting furnace in a laboratory, and hot-rolled to a thickness of 3.0 mm by hot rolling. In addition, the conventional steels shown in H to J of Table 1 were melted in the normal manufacturing process and
It was hot rolled to a thickness. 1100 this hot rolled sheet
After annealing at ℃, cold rolling mill rolled to 0.5mm thickness,
After holding at 0 ° C. for 1 minute, a solution treatment of immediately cooling with water was performed. After the solution treatment, cold rolling was performed to generate a martensite phase. Tensile strength in this cold rolled state,
The elongation and hardness were investigated. Then put 450
Aging heat treatment was performed at 1 ° C. for 1 hour, followed by air cooling. Then, the tensile strength, elongation and hardness after aging were also investigated to confirm the effect of aging.
上記鋼の調査結果を第２表に示す。本発明鋼Ｂ〜Ｆは従
来鋼Ｈ〜Ｊあるいは比較鋼Ｋ〜Ｎに比べ、時効による強
度上昇が大きく、時効後は非常に高い強度レベルを実現
している。さらに同じ強度レベルのものを比較すると、
時効前あるいは時効後の伸びはいずれも従来鋼あるいは
比較鋼より大きいことがわかる。第１図は上記の本発明
鋼、従来鋼および比較鋼の強度と延性の関係を示してお
り、この図からも本発明鋼が単に高強度を達成している
ばかりでなく、強度−延性バランスの優れた材料である
ことが明らかである。Table 2 shows the survey results of the above steels. The invention steels B to F have a greater strength increase due to aging than the conventional steels H to J or the comparative steels K to N, and have achieved a very high strength level after aging. Further comparing the same intensity level,
It can be seen that the elongation before and after aging is larger than that of the conventional steel or the comparative steel. FIG. 1 shows the relationship between the strength and ductility of the steels of the present invention, conventional steels and comparative steels described above. From this figure, it is clear that the steels of the present invention not only achieve high strength but also the strength-ductility balance. It is clear that it is an excellent material.
実施例２ 実施例１で作製した本発明鋼の中で溶体化処理後の冷間
圧延率を30％とした鋼板Ｃと、実施例１で作製した記号
Ｉの従来鋼で50％冷間圧延した鋼板を使用し、第２図に
示すビード形状の試験片を作製した。その後、450℃で
１時間保定後空冷の時効熱処理を行った。このビード部
を有する試験片を圧縮治具の間に挟み、ビード部が完全
に潰れるまで圧縮荷重を負荷し、その状態で１秒保持し
た後、圧縮荷重を開放した。このサイクルを1000回まで
繰り返し、その途中でのビード高さの変化あるいは割れ
発生の有無を観察した。また同じ条件で時効処理した鋼
板についてバネ限界値の測定および応力腐食割れ試験を
実施した。応力腐食割れ試験は、0.25mm t×10mm w×75
mm lの試験片を半径7mmでＵ曲げ拘束し、42％の沸騰MgC
l2水溶液中に浸漬保持し、その破断時間を測定した。そ
の結果を第３表に示す。従来鋼（SUS301相当）に比べ強
度、延性が優れている本発明鋼は、バネ特性あるいは疲
労特性にも優れ、また耐応力腐食割れ性も良好であるこ
とがわかり、各種バネあるいは金属ガスケット用素材と
して適している。 Example 2 Among the steels of the present invention produced in Example 1, a steel plate C having a cold rolling rate after solution treatment of 30% and a conventional steel of the symbol I produced in Example 1 were 50% cold rolled. The bead-shaped test piece shown in FIG. 2 was produced using the prepared steel plate. After that, the sample was held at 450 ° C. for 1 hour and then air-cooled for aging heat treatment. The test piece having this bead portion was sandwiched between compression jigs, a compression load was applied until the bead portion was completely crushed, and the state was held for 1 second, and then the compression load was released. This cycle was repeated up to 1000 times and changes in the bead height or the occurrence of cracks were observed during the cycle. Further, the spring limit value measurement and the stress corrosion cracking test were carried out on the steel sheet aged under the same conditions. The stress corrosion cracking test is 0.25 mm t × 10 mm w × 75
U-bending restraint of a test piece of mm l with a radius of 7 mm and boiling MgC of 42%
It was dipped and held in an l 2 aqueous solution and the breaking time was measured. The results are shown in Table 3. The steel of the present invention, which is superior in strength and ductility to the conventional steel (equivalent to SUS301), has excellent spring characteristics or fatigue characteristics, and also has good resistance to stress corrosion cracking. Suitable as
（発明の効果） 以上詳述したように、本発明鋼は従来の加工硬化型ステ
ンレス鋼あるいは析出硬化型ステンレス鋼に比べ、高強
度を実現しているのみならず、延性も高いことから強度
−延性バランスに優れたステンレス鋼であると言える。
そして本発明鋼はバネ特性、疲労特性あるいは応力腐食
割れに対する抵抗力も高いため、各種金属バネあるいは
金属ガスケット用等の素材として最適であり、本発明は
産業上寄与するところは極めて大である。 (Effects of the Invention) As described in detail above, the steel of the present invention not only achieves high strength, but also has high ductility compared to conventional work-hardening stainless steel or precipitation-hardening stainless steel. It can be said that the stainless steel has an excellent ductility balance.
Since the steel of the present invention has high spring characteristics, fatigue characteristics, and high resistance to stress corrosion cracking, it is optimal as a material for various metal springs, metal gaskets, etc., and the present invention greatly contributes to industry.
【図面の簡単な説明】 第１図は実施例１における本発明鋼、従来鋼および比較
鋼の冷間圧延ままの状態ならびに時効処理状態での引張
強度と伸びの関係を示したグラフで、記号の○、△およ
び□はそれぞれ本発明鋼、従来鋼ならびに比較鋼の冷間
圧延ままでの結果を示し、●、▲および■は各々の時効
処理状態での結果を示す。 第２図は実施例２におけるビード部の圧縮・開放試験に
使用した試験片の概略図を示したものである。（ａ）は
試験片の全体図、（ｂ）は（ａ）におけるＣ−Ｃ′断面
図を示す。BRIEF DESCRIPTION OF THE DRAWINGS FIG. 1 is a graph showing the relationship between the tensile strength and the elongation of the steel of the present invention, the conventional steel and the comparative steel in Example 1 in the as-cold-rolled state and in the aging treated state. ◯, Δ and □ indicate the results of the present invention steel, the conventional steel and the comparative steel in the as cold-rolled state, and ●, ▲ and ■ indicate the results in each aging treatment state. FIG. 2 is a schematic view of a test piece used for the compression / opening test of the bead portion in Example 2. (A) is an overall view of the test piece, and (b) is a sectional view taken along line CC 'in (a).
───────────────────────────────────────────────────── フロントページの続き (72)発明者 荒川 基彦 東京都千代田区大手町２―６―３ 新日本 製鐵株式會社内 (72)発明者 南野 繁 山口県光市大字島田3434番地 新日本製鐵 株式會社光製鐵所内 (56)参考文献 特開 平２−225647（ＪＰ，Ａ) 特開 平２−225646（ＪＰ，Ａ) 特開 昭63−317628（ＪＰ，Ａ) 特開 昭61−295356（ＪＰ，Ａ) 「材料とプロセス」ｖｏｌ．４（1991) Ｐ．2062 ─────────────────────────────────────────────────── ─── Continuation of the front page (72) Inventor Motohiko Arakawa 2-6-3 Otemachi, Chiyoda-ku, Tokyo Shin Nippon Steel Stock Company (72) Inventor Shigeru Minamino 3434 Shimada, Hikari City, Yamaguchi Prefecture Made in Japan (56) References JP-A-2-225647 (JP, A) JP-A-2-225646 (JP, A) JP-A-63-317628 (JP, A) JP-A-61- 295356 (JP, A) "Materials and Processes" vol. 4 (1991) P. 2062
Claims (1)
％以下、Mn1.0％超〜5.0％以下、Cr13〜17％、Ni5〜８
％未満、N0.05〜0.20％を含有し、さらにAl0.01〜0.20
％、ランタノイド系希土類元素、0.002〜0.050％および
Ca0.001〜0.020％のうち１種または２種以上を含有する
ことを特徴とする強度、延性の優れたステンレス鋼。1. By weight%, C0.03% or less, Si more than 3.0% to 5.0.
% Or less, Mn more than 1.0% to 5.0% or less, Cr13 to 17%, Ni5 to 8
%, N0.05-0.20%, Al0.01-0.20
%, Lanthanoid rare earth elements, 0.002-0.050% and
Stainless steel with excellent strength and ductility, characterized by containing one or more of 0.001 to 0.020% Ca.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2271338A JPH0742550B2 (en) | 1990-10-09 | 1990-10-09 | Stainless steel with excellent strength and ductility |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2271338A JPH0742550B2 (en) | 1990-10-09 | 1990-10-09 | Stainless steel with excellent strength and ductility |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH04147946A JPH04147946A (en) | 1992-05-21 |
| JPH0742550B2 true JPH0742550B2 (en) | 1995-05-10 |
Family
ID=17498669
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2271338A Expired - Lifetime JPH0742550B2 (en) | 1990-10-09 | 1990-10-09 | Stainless steel with excellent strength and ductility |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0742550B2 (en) |
Families Citing this family (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH08134595A (en) * | 1994-11-11 | 1996-05-28 | Nippon Steel Corp | High strength stainless steel sheet excellent in stress corrosion cracking resistance |
| FR2850398B1 (en) * | 2003-01-28 | 2005-02-25 | Usinor | PROCESS FOR MANUFACTURING HOT-ROLLED AND COLD HIGH-RESISTANCE ROLLED STEEL SHEET AND OBTAINED SHEET |
| JP5100144B2 (en) * | 2007-02-08 | 2012-12-19 | 日新製鋼株式会社 | Steel plate for spring, spring material using the same, and manufacturing method thereof |
| SI3080311T1 (en) * | 2013-12-13 | 2020-02-28 | Outokumpu Oyj | Method for producing high-strength duplex stainless steel |
| KR20230074779A (en) * | 2021-02-24 | 2023-05-31 | 닛테츠 스테인레스 가부시키가이샤 | Austenitic stainless steel, manufacturing method thereof, and leaf spring |
Family Cites Families (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5721030A (en) * | 1980-07-12 | 1982-02-03 | Anritsu Electric Co Ltd | Solenoid relay |
| JPS61295356A (en) * | 1985-06-24 | 1986-12-26 | Nisshin Steel Co Ltd | High strength stainless steel |
| JPH0826404B2 (en) * | 1987-06-22 | 1996-03-13 | 日新製鋼株式会社 | Method for producing high strength stainless steel with excellent overhang strength and toughness |
| JPH02225647A (en) * | 1989-02-27 | 1990-09-07 | Nisshin Steel Co Ltd | High strength and high ductility stainless steel material and its manufacture |
-
1990
- 1990-10-09 JP JP2271338A patent/JPH0742550B2/en not_active Expired - Lifetime
Non-Patent Citations (1)
| Title |
|---|
| 「材料とプロセス」ｖｏｌ．４（１９９１）Ｐ．２０６２ |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH04147946A (en) | 1992-05-21 |
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