JPS62130263A - Precipitation strengthened stainless steel superior in cold workability - Google Patents
Precipitation strengthened stainless steel superior in cold workabilityInfo
- Publication number
- JPS62130263A JPS62130263A JP26950585A JP26950585A JPS62130263A JP S62130263 A JPS62130263 A JP S62130263A JP 26950585 A JP26950585 A JP 26950585A JP 26950585 A JP26950585 A JP 26950585A JP S62130263 A JPS62130263 A JP S62130263A
- Authority
- JP
- Japan
- Prior art keywords
- stainless steel
- heat treatment
- content
- precipitation strengthened
- strengthened stainless
- 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
Landscapes
- Heat Treatment Of Steel (AREA)
Abstract
Description
【発明の詳細な説明】
〔産業上の利用分野〕
本発明はFeCr−NiCu系析出強化型ステンレス鋼
に関する。DETAILED DESCRIPTION OF THE INVENTION [Field of Industrial Application] The present invention relates to a FeCr-NiCu precipitation-strengthened stainless steel.
Fe−Cr−Ni−Cu系析出強化型ステンレス鋼は強
度が高く、かつ耐食性にすぐれていることより、高応力
を受け、軽量化が必要とされる構造物に多く用いられて
いる。Fe-Cr-Ni-Cu precipitation-strengthened stainless steel has high strength and excellent corrosion resistance, so it is often used in structures that are subject to high stress and require weight reduction.
Fe−Cr−Ni−Cu系析出強化型ステンレス鋼の中
で、マルテンサイト変態点(Ms点)が室温以下のもの
は、溶体化熱処理後の組織が通常オーステナイトである
ため軟かい。そのため従来は溶体化熱処理ままの状磨で
冷間加工による成形を行い、その後深冷(サブゼロ)熱
処理に引続き時効熱処理を施し、高強度を得る方法がと
られていた。Among Fe-Cr-Ni-Cu precipitation-strengthened stainless steels, those whose martensitic transformation point (Ms point) is below room temperature are soft because the structure after solution heat treatment is usually austenite. For this reason, the conventional method was to form the material by cold working while still solution heat treated, and then perform deep cooling (sub-zero) heat treatment followed by aging heat treatment to obtain high strength.
従って、この従来の析出強化型ステンレス鋼は冷間加工
が可能なことに加え、高強度が得られることが著しい特
徴となっているが、溶体化処理によっても軟化しない場
合が多く、そのため冷間加工に大容量のプレスが必要と
なり、設備費が膨大なものとなり、さらに冷間加工中に
割れを生じることが多いなどの欠点があった。Therefore, although this conventional precipitation-strengthened stainless steel is remarkable in that it can be cold-worked and has high strength, it often does not soften even after solution treatment; It required a large-capacity press for processing, resulting in enormous equipment costs, and it also had drawbacks such as cracks often occurring during cold working.
本発明はこの点に鑑み、溶体化熱処理によって容易に軟
化するために大容量のプレスを必要とせず、かつ冷間加
工中に割れの発生が認められず、さらに冷間加工後の深
冷熱処理および時効熱処理によって高強度が得られる材
料の開発を目的とするものである。In view of this, the present invention has been developed so that it is easily softened by solution heat treatment, does not require a large-capacity press, does not cause cracking during cold working, and is further developed by deep cold heat treatment after cold working. The purpose of this project is to develop materials that can obtain high strength through aging heat treatment.
本発明者らはFeCrNi−Cu系析出強化型ステンレ
ス鋼の冷間加工性および時効熱処FI!後の引張性質に
ついて詳細に検討した結果、(c+N)およびNの量を
特定することによって前述の目的を達成しうる鋼が得ら
れることを見出した。すなわち本発明は重量パーセント
で(C+N)0.06〜0.10%でかつN 0.0
05%以上、8110%以下、Mn0.5〜2.0%、
Ni4.5〜6.5%、Cr 14.5〜17.5%、
Cu1.0〜2.5%、Mo1.0〜2.5%、V0.
5%以下を含み、残部がFeおよび不可避不純物からな
る冷間加工性のすぐれた析出強1ヒ型ステンレス鋼に関
する。The present inventors investigated the cold workability and aging heat treatment FI of FeCrNi-Cu precipitation strengthened stainless steel! As a result of a detailed study of the tensile properties, it was discovered that by specifying the amounts of (c+N) and N, a steel capable of achieving the above objectives could be obtained. That is, in the present invention, (C+N) is 0.06 to 0.10% by weight and N 0.0
05% or more, 8110% or less, Mn0.5-2.0%,
Ni 4.5-6.5%, Cr 14.5-17.5%,
Cu1.0-2.5%, Mo1.0-2.5%, V0.
5% or less, with the remainder being Fe and unavoidable impurities, and having excellent cold workability and precipitation strength 1H type stainless steel.
本発明はさらに上述の組成にTi0.05〜0.2%、
Nb 0.2〜1.0%の1種または2種を含有させた
冷間加工性のすぐれた析出強化型ステンレス鋼に間する
。The present invention further includes 0.05 to 0.2% Ti in the above composition.
Precipitation-strengthened stainless steel with excellent cold workability contains one or two types of Nb in an amount of 0.2 to 1.0%.
(作用〕 次に各成分の限定理由を以下に示す。(effect) Next, the reasons for limiting each component are shown below.
第1表に示す組成の鋼種の引張試験と試験の結果に基づ
いて得られた図からC+Nが0.06%よりも低い領域
では溶体化処理したものに冷間加工を施すと割れを発生
する。From the figure obtained based on the results of tensile tests and tests of steels with compositions shown in Table 1, cracks occur when cold working is applied to solution-treated materials in the region where C+N is lower than 0.06%. .
またC十Nが0.10%を越える領域においては深冷熱
処理後時効熱処理を施したものの耐力および引張強さの
上昇があまり大きくない。さらにNが0゜005%未溝
ではオーステナイトを充分に安定化することができない
、従って、上述の理由によりC+Nの含有量は0.06
〜0.10%、Nの含有量は0.005%以上と限定し
た。Further, in a region where C0N exceeds 0.10%, the increase in yield strength and tensile strength is not so large even though aging heat treatment is performed after cryogenic heat treatment. Furthermore, if the N content is 0°005%, the austenite cannot be sufficiently stabilized. Therefore, for the above-mentioned reason, the C+N content is 0.06%.
~0.10%, and the N content was limited to 0.005% or more.
(い−、Si:1.0%r
Siはオーステナイト相安定化の効果があるが、その含
有量が1.0%を越えると介在物として析出し、清浄度
およびじん性が低下する。(I-, Si: 1.0%r Si has the effect of stabilizing the austenite phase, but if its content exceeds 1.0%, it will precipitate as inclusions, resulting in a decrease in cleanliness and toughness.
マン ン(Mn :0.5〜2.0%
Mnもオーステナイト相安定化の効果があるが、その含
有量が0.5%未満ではその効果が少なく、一方、含有
量が2.0%を越えると引張強さが低下する。Manganese (Mn: 0.5-2.0% Mn also has the effect of stabilizing the austenite phase, but the effect is small when the content is less than 0.5%. On the other hand, when the content is less than 2.0%, If it is exceeded, the tensile strength decreases.
ニッケルNi:4.5〜6.59’
Niはオーステナイト相の安定化並びにCuと相乗して
析出硬化をもたらすが、含有量が4,5%未満では効果
が少なく、一方、含有量が6.5%を越えると逆に引張
強さが低下する。Nickel Ni: 4.5 to 6.59' Ni stabilizes the austenite phase and works synergistically with Cu to bring about precipitation hardening, but if the content is less than 4.5%, the effect is small; If it exceeds 5%, the tensile strength will decrease.
クロムCr :14.5+−17,5%Crもオーステ
ナイト相の安定化並びに耐食性の観点より不可欠の元素
であるが、その含有量が145%未満ではそれらの効果
が少なく、一方、その含有量が17.5%を越えると時
効処理後の引張強さが低下する。Chromium Cr: 14.5+-17.5% Cr is also an essential element from the viewpoint of stabilizing the austenite phase and corrosion resistance, but if its content is less than 145%, these effects will be small; If it exceeds 17.5%, the tensile strength after aging will decrease.
Cu:1.0〜2.5%
銅は析出硬化元素として重要であるが、1.0%未満の
含有量ではその効果が少なく、一方、その含有量が2.
5%を越えると熱間加工性が低下する。Cu: 1.0 to 2.5% Copper is important as a precipitation hardening element, but its effect is small if the content is less than 1.0%.
If it exceeds 5%, hot workability decreases.
モリブーンMO=1.0〜2,5/
Moは強度を増加させる効果があるが、1 、0 :’
6未満ではその効果が少なく、一方、25%を越えると
熱間加工性を悪化させる。Moly boon MO=1.0~2,5/Mo has the effect of increasing strength, but 1,0:'
If it is less than 6, the effect will be small, while if it exceeds 25%, hot workability will deteriorate.
バナジウムV :0.551
VはCを固定し、さらに析出硬化をもたらすが、0.5
%を越えて含有させるとじん性が低下する。Vanadium V: 0.551 V fixes C and causes further precipitation hardening, but 0.5
If the content exceeds %, the toughness will decrease.
ニ ブ Nb 、0.2〜1.0%
NbはCおよびNを固定する効果があるが、0.2%未
満の含有量ではその効果が少なく、一方、1.0%を越
えると介在物として存在し、清浄度が悪くなり、じん性
を低下させる。Nib Nb, 0.2-1.0% Nb has the effect of fixing C and N, but if the content is less than 0.2%, the effect is small, while if it exceeds 1.0%, inclusions It exists as a substance, impairs cleanliness and reduces toughness.
タンTi:0.05〜0.2%
TiはCおよびNを固定する効果があるが、0.05%
未満の含有量ではその効果が少なく、一方、02%を越
えると介在物として存在し、清浄度が悪くなり、じん性
を低下させる。Tan Ti: 0.05-0.2% Ti has the effect of fixing C and N, but 0.05%
If the content is less than 0.02%, the effect will be small, while if it exceeds 0.02%, it will exist as inclusions, resulting in poor cleanliness and reduced toughness.
本発明による効果を実証するために第2表に示すように
本発明材と比教材として従来材を遺り、これら材料に
01035℃での溶体化熱処理ままの状1での室温にお
ける曲げ試験、
■−10℃での深冷熱処理に引続き時効熱処理を施した
後の引張試験を実施したそれらの試験結果を第3表に示
す。In order to demonstrate the effects of the present invention, as shown in Table 2, the present invention materials and conventional materials were used as comparison materials, and these materials were subjected to a bending test at room temperature in the state 1 after solution heat treatment at 0.1035°C. (2) A tensile test was conducted after deep cooling heat treatment at -10°C followed by aging heat treatment. The test results are shown in Table 3.
第2表および第3表かられかるように、本発明材は冷間
曲げにおいても割れを発生せ、ず、さらに深冷処理およ
び時効熱処理を施した後において十分高い0.2%耐力
および引張強さが得られている。As can be seen from Tables 2 and 3, the material of the present invention does not crack even during cold bending, and has a sufficiently high 0.2% yield strength and tensile strength after deep cooling treatment and aging heat treatment. I am gaining strength.
本願発明による材料を用いることにより、溶体化熱処理
1ftに安定して軟かい状態が得られるため、■冷間加
工が容易となり、プレスの容量も小さくてすみ、設備費
が大幅に低減できた。By using the material according to the present invention, a stable soft state can be obtained after 1 ft of solution heat treatment, so (1) cold working becomes easy, the capacity of the press can be small, and equipment costs can be significantly reduced.
■冷間加工中に割れを発生することがなくなった。■Cracks no longer occur during cold working.
さらに冷間加工後の時効熱処理によって十分高い0.2
%耐力および引張強さを得ることができた。Furthermore, due to aging heat treatment after cold working, a sufficiently high 0.2
% proof stress and tensile strength could be obtained.
図はCfiとN量と冷間加工性および引張強さ、耐力と
の関係を示す図である。
C量(皇量%JThe figure shows the relationship between Cfi, N content, cold workability, tensile strength, and yield strength. C amount (Imperial amount %J
Claims (1)
でかつN0.005%以上、Si1.0%以下、Mn0
.5〜2.0%、Ni4.5〜6.5%、Cr14.5
〜17.5%、Cu1.0〜2.5%、Mo1.0〜2
.5%、V0.5%以下を含み、残部がFeおよび不可
避不純物からなる冷間加工性のすぐれた析出強化型ステ
ンレス鋼。 2、重量パーセントで(C+N)0.06〜0.10%
でかつN0.005%以上、Si1.0%以下、Mn0
.5〜2.0%、Ni4.5〜6.5%、Cr14.5
〜17.5%、Cu1.0〜2.5%、Mo1.0〜2
.5%、V0.5%以下を含み、さらにTi0.05〜
0.2%、Nb0.2〜1.0%の1種または2種を含
み、残部がFeおよび不可避不純物からなる冷間加工性
のすぐれた析出強化型ステンレス鋼。[Claims] 1. (C+N) 0.06 to 0.10% by weight
And N0.005% or more, Si1.0% or less, Mn0
.. 5-2.0%, Ni4.5-6.5%, Cr14.5
~17.5%, Cu1.0~2.5%, Mo1.0~2
.. Precipitation-strengthened stainless steel with excellent cold workability, containing 0.5% or less of V and 0.5% or less of V, with the remainder consisting of Fe and unavoidable impurities. 2. (C+N) 0.06-0.10% by weight
And N0.005% or more, Si1.0% or less, Mn0
.. 5-2.0%, Ni4.5-6.5%, Cr14.5
~17.5%, Cu1.0~2.5%, Mo1.0~2
.. 5%, V0.5% or less, and Ti0.05~
A precipitation-strengthened stainless steel with excellent cold workability, containing one or two of 0.2% and 0.2 to 1.0% of Nb, with the balance being Fe and unavoidable impurities.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP26950585A JPS62130263A (en) | 1985-12-02 | 1985-12-02 | Precipitation strengthened stainless steel superior in cold workability |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP26950585A JPS62130263A (en) | 1985-12-02 | 1985-12-02 | Precipitation strengthened stainless steel superior in cold workability |
Publications (1)
Publication Number | Publication Date |
---|---|
JPS62130263A true JPS62130263A (en) | 1987-06-12 |
Family
ID=17473354
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP26950585A Pending JPS62130263A (en) | 1985-12-02 | 1985-12-02 | Precipitation strengthened stainless steel superior in cold workability |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPS62130263A (en) |
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH02282424A (en) * | 1989-04-20 | 1990-11-20 | Uchiyama Mfg Corp | Production of metal gasket |
WO2014112353A1 (en) * | 2013-01-16 | 2014-07-24 | Jfeスチール株式会社 | Stainless steel seamless tube for use in oil well and manufacturing process therefor |
-
1985
- 1985-12-02 JP JP26950585A patent/JPS62130263A/en active Pending
Cited By (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH02282424A (en) * | 1989-04-20 | 1990-11-20 | Uchiyama Mfg Corp | Production of metal gasket |
WO2014112353A1 (en) * | 2013-01-16 | 2014-07-24 | Jfeスチール株式会社 | Stainless steel seamless tube for use in oil well and manufacturing process therefor |
EP2947167A4 (en) * | 2013-01-16 | 2016-01-13 | Jfe Steel Corp | Stainless steel seamless tube for use in oil well and manufacturing process therefor |
JP5861786B2 (en) * | 2013-01-16 | 2016-02-16 | Jfeスチール株式会社 | Stainless steel seamless steel pipe for oil well and manufacturing method thereof |
US10240221B2 (en) | 2013-01-16 | 2019-03-26 | Jfe Steel Corporation | Stainless steel seamless pipe for oil well use and method for manufacturing the same |
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