JPS63438A - Precipitation strengthening-type stainless steel excellent in cold workability - Google Patents
Precipitation strengthening-type stainless steel excellent in cold workabilityInfo
- Publication number
- JPS63438A JPS63438A JP14147286A JP14147286A JPS63438A JP S63438 A JPS63438 A JP S63438A JP 14147286 A JP14147286 A JP 14147286A JP 14147286 A JP14147286 A JP 14147286A JP S63438 A JPS63438 A JP S63438A
- Authority
- JP
- Japan
- Prior art keywords
- heat treatment
- stainless steel
- cold working
- precipitation strengthening
- type 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.)
- Granted
Links
- 229910001220 stainless steel Inorganic materials 0.000 title claims abstract description 11
- 239000010935 stainless steel Substances 0.000 title claims abstract description 9
- 238000001556 precipitation Methods 0.000 title abstract description 5
- 239000012535 impurity Substances 0.000 claims abstract description 3
- 238000010438 heat treatment Methods 0.000 abstract description 18
- 238000005482 strain hardening Methods 0.000 abstract description 13
- 230000032683 aging Effects 0.000 abstract description 7
- 229910018054 Ni-Cu Inorganic materials 0.000 abstract description 5
- 229910018481 Ni—Cu Inorganic materials 0.000 abstract description 5
- 229910052804 chromium Inorganic materials 0.000 abstract description 3
- 229910052748 manganese Inorganic materials 0.000 abstract description 3
- 229910052759 nickel Inorganic materials 0.000 abstract description 3
- 229910052802 copper Inorganic materials 0.000 abstract description 2
- 229910052720 vanadium Inorganic materials 0.000 abstract description 2
- 239000000203 mixture Substances 0.000 abstract 2
- 229910052750 molybdenum Inorganic materials 0.000 abstract 1
- 230000000694 effects Effects 0.000 description 12
- 239000000463 material Substances 0.000 description 7
- 229910001566 austenite Inorganic materials 0.000 description 5
- 230000007423 decrease Effects 0.000 description 5
- 239000010936 titanium Substances 0.000 description 5
- 229910000831 Steel Inorganic materials 0.000 description 3
- 239000011651 chromium Substances 0.000 description 3
- 238000001816 cooling Methods 0.000 description 3
- 239000010949 copper Substances 0.000 description 3
- 239000010959 steel Substances 0.000 description 3
- 238000005452 bending Methods 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 238000005336 cracking Methods 0.000 description 2
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 2
- 238000004881 precipitation hardening Methods 0.000 description 2
- 230000000087 stabilizing effect Effects 0.000 description 2
- 238000009864 tensile test Methods 0.000 description 2
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 229910017060 Fe Cr Inorganic materials 0.000 description 1
- 229910002544 Fe-Cr Inorganic materials 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- UPHIPHFJVNKLMR-UHFFFAOYSA-N chromium iron Chemical compound [Cr].[Fe] UPHIPHFJVNKLMR-UHFFFAOYSA-N 0.000 description 1
- 230000003749 cleanliness Effects 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 230000035882 stress Effects 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 229910052719 titanium Inorganic materials 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 1
- 239000013585 weight reducing agent Substances 0.000 description 1
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Ｆｅ−Ｃｒ−Ｎｉ−Ｃｕ系析出強化型ステンレ
ス鋼に関する。DETAILED DESCRIPTION OF THE INVENTION [Industrial Field of Application] The present invention relates to a Fe-Cr-Ni-Cu 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態
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 with a martensitic transformation point (Ms point) below room temperature usually have an austenitic structure after solution heat treatment and are soft; Forming is done by cold working in the same state as chemical heat treatment, and then deep cooling (sub-zero)
The conventional method was to perform aging heat treatment following heat treatment to obtain high strength.
従って、この従来の析出強化望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１ヒ処理によっても軟化しない
場きが多く、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
に割れと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, in many cases it does not soften even after solution treatment. Cold working requires a large-capacity press, resulting in enormous equipment costs, and it also has drawbacks such as cracking often occurs during cold working.
このため、（Ｃ＋Ｎ）Ｘを制御した冷間加工性のすぐれ
た析出強化型ステンレス鋼が開発されている（特願昭６
０−２６９５０５号）、シかし、この発明においては、
溶体化処理ままでは軟化し、冷間加工性は向上したもの
の、再度の冷間加工を行う際、割れが生じるなどの問題
があった。For this reason, precipitation-strengthened stainless steels with controlled (C+N)X and excellent cold workability have been developed (patent application No. 6).
0-269505), but in this invention,
Although the solution treatment resulted in softening and improved cold workability, there were problems such as cracks occurring when cold working was performed again.
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、かつ繰返し
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 repeated cold working, and is further developed by deep cooling after cold working. The aim is to develop materials that can obtain high strength through heat treatment and aging heat treatment.
本発明者らはＦｅ−Ｃｒ−Ｎｉ−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理後の引張性質に
ついて詳細に検討した結果、（Ｃ＋Ｎ）およびＮの量を
特定し、さらに特定量のチタンを添加することによって
前述の目的を達成しうる鋼が得られることを見出した。As a result of a detailed study of the cold workability and tensile properties after aging heat treatment of Fe-Cr-Ni-Cu precipitation-strengthened stainless steel, the inventors identified the amounts of (C+N) and N, and further determined It has been found that by adding a certain amount of titanium, a steel can be obtained which is capable of achieving the aforementioned objectives.
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 ０．００５％以上、Ｓｉ
１．０％以下、Ｍｎ０．５〜２．０％、Ｎｉ４．５〜６
．５％、Ｃｒ１４．５〜１７．５％、Ｃｕ１．０〜２．
５％、Ｍｏｌ、０〜２．５％、■ ０．５％以下、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に関する。That is, the present invention has a weight percent (C+N) of 0.06.
~0.10% and N 0.005% or more, Si
1.0% or less, Mn 0.5-2.0%, Ni 4.5-6
．． 5%, Cr14.5-17.5%, Cu1.0-2.
5%, Mol, 0-2.5%, ■ 0.5% or less, the balance being Fe and unavoidable impurities, and relates to a precipitation-strengthened stainless steel with excellent cold workability.
次に各成分の限定理由を以下に示す。 Next, the reasons for limiting each component are shown below.
Ｃ＋Ｎが０．０６％よりも低い範囲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。In a range where C+N is lower than 0.06%, cracks occur when cold working is applied to a solution-treated material.
またＣ＋Ｎが０．１０％を越える範囲においては深冷熱
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％未満
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 range in which C+N exceeds 0.10%, the increase in yield strength and tensile strength is not so great even when aging heat treatment is performed after cryogenic heat treatment. Furthermore, if N is less than 0.005%, 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.
番い Ｓｉ：１，０°パ
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。Si: 1.0°P Si has the effect of stabilizing the austenite phase, but if its content exceeds 1.0%, it precipitates as inclusions, reducing cleanliness and toughness.
マン ンＭｎ ：０．５〜２．０％
Ｍ ｎ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。Mn: 0.5 to 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 ：４．５〜６．５％
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 6.5% 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ｆヒ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１４．５％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陵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 stability of the austenite phase and corrosion resistance, but if its content is less than 14.5%, these effects will be small; Content is 17
．． If it exceeds 5%, the tensile strength of the aged ribs 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 when the content is less than 1.0%;
If it exceeds 5%, hot workability decreases.
モ１ブーンＭＯ：１．０〜２ 、５９／ＭＯは強度を増
加させる効果があるが、１．０％未満ではその効果が少
なく、一方、２．５％を越えると熱間加工性を悪化させ
る。MO1 Boon MO: 1.0-2, 59/MO has the effect of increasing strength, but if it is less than 1.0%, the effect is small, and on the other hand, if it exceeds 2.5%, hot workability deteriorates. let
バナジウム■ ：０．５％ν
■はＣを固定し、さらに析出硬（ヒをもたらすが、０．
５％を越えて含有させるとじん性が低下する。Vanadium ■: 0.5% ν ■ fixes C and further causes precipitation hardness, but 0.5% ν
If the content exceeds 5%, the toughness will decrease.
ＴｉはＣおよびＮを固定する効果があるが、割れの発生
が認められ、一方、Ｔｉ＞（Ｃ＋Ｎ）では縁返し冷間曲
げ加工時に再び割れが生じるようになる。Although Ti has the effect of fixing C and N, cracks are observed to occur. On the other hand, if Ti>(C+N), cracks will occur again during edge-turning cold bending.
〔実施例〕
本発明による効果を実証するために第１表に示す材料を
製造した。これら材料に１０３５°Ｃでの溶体化熱処理
ままの状態での室温における引張試験および曲げ試験を
実施した。[Example] In order to demonstrate the effects of the present invention, materials shown in Table 1 were manufactured. These materials were subjected to a tensile test and a bending test at room temperature while solution heat treated at 1035°C.
さらに、１０℃での深冷熱処理に引続き５４０℃で時効
熱処理を施した後の引張試験を実施した。Furthermore, a tensile test was conducted after performing deep cooling heat treatment at 10°C and subsequently aging heat treatment at 540°C.
それらの試験結果を第２表に示す。The test results are shown in Table 2.
なお、第１表に示す材料の（Ｃ＋Ｎ）量（重量％）とＴ
ｉ ｉｌ （重量％）との関係を図に示した。In addition, the (C+N) amount (wt%) and T of the materials shown in Table 1
The relationship with i il (weight %) is shown in the figure.
本願発明による材料を用いることにより、溶体１ヒ熱処
理後に特願昭６０−２６９５０５号で発明された材料に
比較して、０．２％耐力が低いため、■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, the yield strength is 0.2% lower than that of the material invented in Japanese Patent Application No. 60-269505 after heat treatment with solution 1, so cold working becomes easier and press The capacity was small, and equipment costs were significantly reduced.
■冷間加工中に割れと発生することがなくなった。■Cracks no longer occur during cold working.
さらに、冷間加工後の深冷熱処理および時効熱処理によ
って十分高い０．２％耐力および引張強さが得られた。Furthermore, sufficiently high 0.2% yield strength and tensile strength were obtained by deep cold heat treatment and aging heat treatment after cold working.
図は第１表に示す組成の本発明材および比較材の（Ｃ＋
Ｎ）量（重量５＋≦）とＴｉ量（重量％）との間の関係
を示す図である。
・本発明鋼
×比較鋼
Ｔｉ （重量６／、）The figure shows (C+
It is a figure showing the relationship between the amount of N (weight 5+≦) and the amount of Ti (weight %).・Invention steel x comparative steel Ti (weight 6/,)
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、さらに（Ｃ＋Ｎ）／３
≦Ｔｉ≦（Ｃ＋Ｎ）のＴｉ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。1. (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 (C+N)/3
A precipitation-strengthened stainless steel with excellent cold workability, containing Ti with the balance being Fe and unavoidable impurities, where ≦Ti≦(C+N).
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP14147286A JPH0617545B2 (en) | 1986-06-19 | 1986-06-19 | Precipitation strengthened stainless steel with excellent cold workability |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP14147286A JPH0617545B2 (en) | 1986-06-19 | 1986-06-19 | Precipitation strengthened stainless steel with excellent cold workability |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS63438A true JPS63438A (en) | 1988-01-05 |
| JPH0617545B2 JPH0617545B2 (en) | 1994-03-09 |
Family
ID=15292679
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP14147286A Expired - Lifetime JPH0617545B2 (en) | 1986-06-19 | 1986-06-19 | Precipitation strengthened stainless steel with excellent cold workability |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0617545B2 (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4807995A (en) * | 1985-07-04 | 1989-02-28 | Oem Messtechnik Gmbh | Process for electro optical inspection of the mouth area of glass bottles |
| JPH02282424A (en) * | 1989-04-20 | 1990-11-20 | Uchiyama Mfg Corp | Production of metal gasket |
-
1986
- 1986-06-19 JP JP14147286A patent/JPH0617545B2/en not_active Expired - Lifetime
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4807995A (en) * | 1985-07-04 | 1989-02-28 | Oem Messtechnik Gmbh | Process for electro optical inspection of the mouth area of glass bottles |
| JPH02282424A (en) * | 1989-04-20 | 1990-11-20 | Uchiyama Mfg Corp | Production of metal gasket |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0617545B2 (en) | 1994-03-09 |
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Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| EXPY | Cancellation because of completion of term |