JPH0617545B2 - Precipitation strengthened stainless steel with excellent cold workability - Google Patents
Precipitation strengthened stainless steel with excellent cold workabilityInfo
- Publication number
- JPH0617545B2 JPH0617545B2 JP14147286A JP14147286A JPH0617545B2 JP H0617545 B2 JPH0617545 B2 JP H0617545B2 JP 14147286 A JP14147286 A JP 14147286A JP 14147286 A JP14147286 A JP 14147286A JP H0617545 B2 JPH0617545 B2 JP H0617545B2
- Authority
- JP
- Japan
- Prior art keywords
- stainless steel
- cold workability
- heat treatment
- excellent cold
- precipitation
- 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 - Lifetime
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- Heat Treatment Of Steel (AREA)
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 application] The present invention relates to Fe—Cr—Ni—Cu based 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
が受け、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 based precipitation-strengthened stainless steels are high in strength and excellent in corrosion resistance. Therefore, they are often used in structures that receive high stress and need to be lightweight.
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のままの状態
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 having a martensite transformation point (Ms point) of room temperature or lower are soft because the structure after solution heat treatment is usually austenite. Therefore, conventionally, a method of obtaining high strength by performing forming by cold working in the state of the solution heat treatment and then performing deep-cooling (subzero) heat treatment followed by aging treatment has been used.
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, this conventional precipitation-strengthened stainless steel has a remarkable feature that it can be cold-worked and has high strength. However, in many cases, it does not soften even by solution treatment. There are drawbacks such that a large-capacity press is required for processing, the equipment cost becomes enormous, and cracks often occur during cold working.
このため、(C+N)量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60−2
69505号)。しかし、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 having excellent cold workability with controlled (C + N) content have been developed (Japanese Patent Application No. 60-2).
69505). However, in the present invention, although the solution treatment is softened as it is and the cold workability is improved, there is a problem that cracks occur when performing the cold work 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 point, the present invention does not require a large-capacity press for easily softening by solution heat treatment, and the occurrence of cracks is not recognized during repeated cold working. The purpose is to develop a material that can obtain high strength by 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。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N0.005%以上、Si1.0%以
下、Mn0.5〜2.0%、Ni4.5〜6.5%、C
r 14.5〜17.5%、Cu1.0〜2.5%、
Mo1.0〜2.5%、V0.5%以下、 さらに 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に関す
る。As a result of detailed investigations on the cold workability of Fe—Cr—Ni—Cu system precipitation strengthened stainless steel and the tensile properties after aging heat treatment, the inventors have specified the amounts of (C + N) and N, and further specified It has been found that by adding an amount of titanium a steel can be obtained which can achieve the above mentioned objects. That is, the present invention is (C + N) 0.06% by weight.
0.10% and N 0.005% or more, Si 1.0% or less, Mn 0.5 to 2.0%, Ni 4.5 to 6.5%, C
r 14.5 to 17.5%, Cu 1.0 to 2.5%,
Mo 1.0 to 2.5%, V 0.5% or less, Of the precipitation strengthening type stainless steel having excellent cold workability, which contains Ti and the balance is Fe and inevitable impurities.
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.
炭素+窒素(C+N):0.06〜0.10%かつ 窒素(N):0.005%以上 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。Carbon + Nitrogen (C + N): 0.06 to 0.10% and Nitrogen (N): 0.005% or more If C + N is lower than 0.06%, cracking occurs when subject to solution treatment and cold working. To occur.
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 the range where C + N exceeds 0.10%, the increase in yield strength and tensile strength is not so large even after aging treatment after deep-chill heat treatment. Further, if N is less than 0.005%, austenite cannot be sufficiently stabilized.
Therefore, the content of C + N is 0.06 for the above reason.
.About.0.10%, and the content of N is limited to 0.005% or more.
けい素(Si):1.0%以下 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。Silicon (Si): 1.0% or less Si has the effect of stabilizing the austenite phase, but if its content exceeds 1.0%, it precipitates as inclusions and the cleanliness and toughness deteriorate.
マンガン(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 to 2.0% Mn also has an effect of stabilizing the austenite phase, but if the content is less than 0.5%, the effect is small, while the content is 2.0%. If it exceeds, the tensile strength will decrease.
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): 4.5-6.5% Ni stabilizes the austenite phase and synergizes with Cu to bring about precipitation hardening, but if the content is less than 4.5%, the effect is small, while the content is On the other hand, if it exceeds 6.5%, the tensile strength is lowered.
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性性の観点よ
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後の引張強さが低下する。Chromium (Cr): 14.5 to 17.5% Cr is also an essential element from the viewpoint of stabilizing the austenite phase and resistance, but if its content is less than 14.5%, these effects are small, while , Its content is 17.
If it exceeds 5%, the tensile strength after aging treatment decreases.
銅(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。Copper (Cu): 1.0 to 2.5% Copper is important as a precipitation hardening element, but if the content is less than 1.0%, its effect is small, while its content is 2.
If it exceeds 5%, the hot workability deteriorates.
モリブデン(Mo):1.0〜2.5% 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。Molybdenum (Mo): 1.0 to 2.5% Mo has the effect of increasing the strength, but if it is less than 1.0%, it has little effect, while if it exceeds 2.5%, the hot workability deteriorates. Let
バナジウム(V):0.5%以下 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): 0.5% or less V fixes C and causes precipitation hardening, but 0.5
If it is contained in excess of%, the toughness decreases.
TiはCおよびNを固定する効果があるが、 では、繰返し冷間曲げ加工により割れの発生が認めら
れ、一方、Ti>(C+N)では繰返し冷間曲げ加工時に
再び割れが生じるようになる。 Ti has the effect of fixing C and N, On the other hand, the occurrence of cracks was recognized by the repeated cold bending work, while on the other hand, when Ti> (C + N), the cracks started to occur again during the repeated cold bending work.
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℃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。The materials shown in Table 1 were manufactured to demonstrate the effect of the present invention. These materials were subjected to a tensile test and a bending test at room temperature in the as-solution-treated state 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。それらの試験
結果を第2表に示す。Further, a tensile test was conducted after the deep-cooling heat treatment at 10 ° C. was followed by the aging heat treatment at 540 ° C. The test results are shown in Table 2.
なお、第1表に示す材料料の(C+N)量(重量%)とTi
量(重量%)との関係を図に示した。The (C + N) amount (% by weight) of the material shown in Table 1 and Ti
The relationship with the amount (% by weight) is shown in the figure.
〔発明の効果〕 本願発明による材料を用いることにより、溶体化熱処理
後に特願昭60−269505号で発生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。 [Effects of the Invention] By using the material according to the present invention, compared with the material generated in Japanese Patent Application No. 60-269505 after solution heat treatment,
Since the 0.2% proof stress is low, cold working is easy, the press capacity is small, and the equipment cost can be reduced significantly.
冷間加工中に割れを発生することがなくなった。さら
に、冷間加工後の深冷熱処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。No more cracking during cold working. Furthermore, sufficiently high 0.2% proof stress and tensile strength were obtained by deep cold heat treatment and aging heat treatment after cold working.
【図面の簡単な説明】 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%)とTi(重量%)との間の関係を示す図で
ある。BRIEF DESCRIPTION OF THE DRAWINGS The figure shows (C +) of the invention material and the comparative material having the compositions shown in Table 1.
FIG. 3 is a diagram showing the relationship between N) amount (wt%) and Ti (wt%).
Claims (1)
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%、M
o1.0〜2.5%、V0.5%以下を含み、さらに 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. A weight percent of (C + N) 0.06-.
0.10% and N 0.005% or more, Si 1.0% or less, Mn 0.5 to 2.0%, Ni 4.5 to 6.5%, Cr 14.5 to 17.5%, Cu 1.0 to 2 0.5%, M
o 1.0-2.5%, including V 0.5% or less, Precipitation-strengthened stainless steel with excellent cold workability, which contains Ti and the balance is Fe and inevitable impurities.
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 JPS63438A (en) | 1988-01-05 |
JPH0617545B2 true 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) |
Families Citing this family (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
DE3523975A1 (en) * | 1985-07-04 | 1987-01-08 | Oem Messtechnik Gmbh | METHOD FOR OPTO-ELECTRONIC INSPECTION OF 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
Also Published As
Publication number | Publication date |
---|---|
JPS63438A (en) | 1988-01-05 |
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Legal Events
Date | Code | Title | Description |
---|---|---|---|
EXPY | Cancellation because of completion of term |