JP2002173740A - Precipitation hardening martensitic stainless steel strip having excellent shape flatness and its production method - Google Patents
Precipitation hardening martensitic stainless steel strip having excellent shape flatness and its production methodInfo
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- JP2002173740A JP2002173740A JP2000368532A JP2000368532A JP2002173740A JP 2002173740 A JP2002173740 A JP 2002173740A JP 2000368532 A JP2000368532 A JP 2000368532A JP 2000368532 A JP2000368532 A JP 2000368532A JP 2002173740 A JP2002173740 A JP 2002173740A
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- stainless steel
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- austenite
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- 229910001105 martensitic stainless steel Inorganic materials 0.000 title claims abstract description 18
- 238000004881 precipitation hardening Methods 0.000 title claims abstract description 13
- 238000004519 manufacturing process Methods 0.000 title claims description 9
- 230000009466 transformation Effects 0.000 claims abstract description 55
- 229910001566 austenite Inorganic materials 0.000 claims abstract description 36
- 229910000734 martensite Inorganic materials 0.000 claims abstract description 35
- 229910001220 stainless steel Inorganic materials 0.000 claims abstract description 18
- 239000010935 stainless steel Substances 0.000 claims abstract description 16
- 230000032683 aging Effects 0.000 claims abstract description 13
- 238000005097 cold rolling Methods 0.000 claims abstract description 10
- 239000011159 matrix material Substances 0.000 claims abstract description 5
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 4
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 4
- 230000002441 reversible effect Effects 0.000 claims description 54
- 238000010438 heat treatment Methods 0.000 claims description 19
- 238000000034 method Methods 0.000 claims description 9
- 229910052761 rare earth metal Inorganic materials 0.000 claims description 8
- 239000000203 mixture Substances 0.000 claims description 7
- 229910000831 Steel Inorganic materials 0.000 abstract description 36
- 239000010959 steel Substances 0.000 abstract description 36
- 229910052799 carbon Inorganic materials 0.000 abstract description 3
- 230000006866 deterioration Effects 0.000 abstract description 2
- 229910052757 nitrogen Inorganic materials 0.000 abstract description 2
- 230000000694 effects Effects 0.000 description 19
- 229910045601 alloy Inorganic materials 0.000 description 9
- 239000000956 alloy Substances 0.000 description 9
- 238000001816 cooling Methods 0.000 description 9
- 239000000243 solution Substances 0.000 description 9
- 230000008569 process Effects 0.000 description 8
- 238000012360 testing method Methods 0.000 description 8
- 229910000859 α-Fe Inorganic materials 0.000 description 7
- 230000007797 corrosion Effects 0.000 description 6
- 238000005260 corrosion Methods 0.000 description 6
- 239000000463 material Substances 0.000 description 6
- 238000012937 correction Methods 0.000 description 5
- 238000005096 rolling process Methods 0.000 description 5
- 230000002411 adverse Effects 0.000 description 4
- 238000005482 strain hardening Methods 0.000 description 4
- -1 304 is cold-rolled Inorganic materials 0.000 description 3
- 238000000137 annealing Methods 0.000 description 3
- 230000015572 biosynthetic process Effects 0.000 description 3
- 230000008859 change Effects 0.000 description 3
- 238000005520 cutting process Methods 0.000 description 3
- 238000005098 hot rolling Methods 0.000 description 3
- 238000011835 investigation Methods 0.000 description 3
- 238000010791 quenching Methods 0.000 description 3
- 230000000171 quenching effect Effects 0.000 description 3
- 230000009467 reduction Effects 0.000 description 3
- 230000002829 reductive effect Effects 0.000 description 3
- 238000003483 aging Methods 0.000 description 2
- 229910000963 austenitic stainless steel Inorganic materials 0.000 description 2
- 238000006243 chemical reaction Methods 0.000 description 2
- 230000003749 cleanliness Effects 0.000 description 2
- 238000005336 cracking Methods 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 238000001556 precipitation Methods 0.000 description 2
- 230000000717 retained effect Effects 0.000 description 2
- 229920006395 saturated elastomer Polymers 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 238000005728 strengthening Methods 0.000 description 2
- 238000005496 tempering Methods 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 102100022626 Glutamate receptor ionotropic, NMDA 2D Human genes 0.000 description 1
- 101000972840 Homo sapiens Glutamate receptor ionotropic, NMDA 2D Proteins 0.000 description 1
- 206010070834 Sensitisation Diseases 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- 230000009471 action Effects 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 239000012876 carrier material Substances 0.000 description 1
- 230000001419 dependent effect Effects 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000005242 forging Methods 0.000 description 1
- 238000009776 industrial production Methods 0.000 description 1
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 238000000691 measurement method Methods 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 230000036961 partial effect Effects 0.000 description 1
- 229910052698 phosphorus Inorganic materials 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 230000008313 sensitization Effects 0.000 description 1
- 238000009628 steelmaking Methods 0.000 description 1
- 229910052717 sulfur Inorganic materials 0.000 description 1
- 230000001131 transforming effect Effects 0.000 description 1
- 229910052727 yttrium Inorganic materials 0.000 description 1
Landscapes
- Heat Treatment Of Sheet Steel (AREA)
Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は、形状平坦度に優れ、ビ
ッカース硬さ３５０以上の析出硬化型マルテンサイト系
ステンレス鋼帯及びその製造方法に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a precipitation hardening type martensitic stainless steel strip having excellent flatness and a Vickers hardness of 350 or more, and a method for producing the same.
【０００２】[0002]
【従来の技術】ビッカース硬さが３５０以上の高強度ス
テンレス鋼として、マルテンサイト系ステンレス鋼，加
工硬化型ステンレス鋼，析出硬化型ステンレス鋼等が知
られている。マルテンサイト系ステンレス鋼は、高温の
オーステナイト状態から急冷してマルテンサイト変態さ
せることによって硬質化した材料であり、ＳＵＳ４１
０，ＳＵＳ４２０Ｊ２等の鋼種がある。マルテンサイト
系ステンレス鋼の製造では、焼入れ−焼戻しの調質処理
によってビッカース硬度３５０以上に調整することか
ら、焼入れ−焼戻しの熱処理工程を必須とする。また、
鋼帯でマルテンサイト変態を起こさせようとすると、焼
入れ後の靭性低下や完全にマルテンサイト変態すること
に起因した形状変化が大きいため、製造条件にかなりの
制約が加わる。2. Description of the Related Art Martensitic stainless steel, work hardening stainless steel, precipitation hardening stainless steel and the like are known as high-strength stainless steels having a Vickers hardness of 350 or more. Martensitic stainless steel is a material hardened by rapidly cooling from a high-temperature austenite state and transforming it into martensite.
0, SUS420J2, etc. In the production of martensitic stainless steel, a Vickers hardness of 350 or more is adjusted by quenching and tempering, so that a quenching and tempering heat treatment step is essential. Also,
If a martensitic transformation is to be caused in a steel strip, since the toughness decreases after quenching and the shape change due to the complete martensitic transformation is large, the manufacturing conditions are considerably restricted.
【０００３】そこで、形状変化が問題となる場合、加工
硬化型オーステナイト系ステンレス鋼が通常使用されて
いる。加工硬化型オーステナイト系ステンレス鋼は、Ｓ
ＵＳ３０１，ＳＵＳ３０４に代表され、溶体化処理状態
でオーステナイト相を呈し、その後の冷間圧延で加工誘
起マルテンサイトを生成することにより高強度が付与さ
れる。[0003] Therefore, when a change in shape is a problem, a work-hardening austenitic stainless steel is usually used. Work hardening type austenitic stainless steel is S
As represented by US301 and SUS304, they exhibit an austenitic phase in a solution-treated state, and then provide high strength by forming work-induced martensite by subsequent cold rolling.
【０００４】[0004]
【発明が解決しようとする課題】冷間圧延によって鋼帯
の形状も矯正されるが、硬度の圧延温度依存性が大き
く、且つコイル長手方向でも形状が種々変動しているた
め、冷間圧延によって工業的に且つ安定的に形状矯正す
ることは困難である。たとえば、ＳＵＳ３０１，ＳＵＳ
３０４等のステンレス鋼を冷間圧延するとオーステナイ
トが加工誘起マルテンサイトに変態するが、同一圧延率
での変態量は圧延時の温度に依存する。具体的には、圧
延時の温度が高いと加工誘起マルテンサイトが生成しに
くく硬度が低くなり、逆に圧延時の温度が低いと加工誘
起マルテンサイトが生成しやすく硬度が上昇する。ま
た、硬度上昇に応じて変形抵抗が大きくなり、形状矯正
が困難になる。Although the shape of the steel strip is corrected by cold rolling, the hardness is greatly dependent on the rolling temperature, and the shape varies in the longitudinal direction of the coil. It is difficult to perform shape correction industrially and stably. For example, SUS301, SUS
When stainless steel such as 304 is cold-rolled, austenite is transformed into work-induced martensite, but the transformation amount at the same rolling reduction depends on the temperature during rolling. Specifically, when the temperature at the time of rolling is high, the formation of work-induced martensite is difficult and the hardness is low, and when the temperature at the time of rolling is low, the work-induced martensite is easily formed and the hardness is increased. In addition, the deformation resistance increases as the hardness increases, and shape correction becomes difficult.
【０００５】[0005]
【課題を解決するための手段】本発明は、このような問
題を解消すべく案出されたものであり、マルテンサイト
からオーステナイトへの逆変態を利用することにより、
マルテンサイト変態に伴った形状悪化を抑え、形状平坦
度に優れた高硬度のマルテンサイト系ステンレス鋼帯又
は鋼板を提供することを目的とする。DISCLOSURE OF THE INVENTION The present invention has been devised to solve such a problem, and utilizes the reverse transformation from martensite to austenite to thereby provide:
It is an object of the present invention to provide a high-hardness martensitic stainless steel strip or steel sheet excellent in shape flatness while suppressing shape deterioration accompanying martensitic transformation.
【０００６】本発明の析出硬化型マルテンサイト系ステ
ンレス鋼は、その目的を達成するため、Ｃ：０．１５質
量％以下，Ｓｉ：２．０質量％以下，Ｍｎ：２．０質量
％以下，Ｎｉ：３．０〜１０．０質量％，Ｃｒ：１２．
０〜２０．０質量％，Ｍｏ：４．０質量％以下，Ｎ：
０．０５質量％以下，Ｔｉ：０．５０質量％以下，残部
が実質的にＦｅで、式（１）で定義されるＭｄ（Ｎ）値
が１００以上の組成をもち、逆変態オーステナイトから
生成したマルテンサイトがマトリックスに分散している
組織をもつことを特徴とする。 Md(N)＝580−520C−2Si−16Mn−16Cr−23Ni−300N−10Mo・・・（１）[0006] The precipitation hardening martensitic stainless steel of the present invention, in order to achieve the object, C: 0.15 mass% or less, Si: 2.0 mass% or less, Mn: 2.0 mass% or less, Ni: 3.0 to 10.0% by mass, Cr: 12.
0 to 20.0% by mass, Mo: 4.0% by mass or less, N:
0.05% by mass or less, Ti: 0.50% by mass or less, the balance being substantially Fe, having a composition with an Md (N) value defined by the formula (1) of 100 or more, and formed from reverse transformed austenite Characterized by having a structure in which martensite is dispersed in a matrix. Md (N) = 580-520C-2Si-16Mn-16Cr-23Ni-300N-10Mo ... (1)
【０００７】この析出硬化型マルテンサイト系ステンレ
ス鋼は、更にＣｕ：５．０質量％以下，Ｎｂ：０．５０
質量％以下，Ａｌ：２．０質量％以下，Ｂ：０．０１５
質量％以下，ＲＥＭ（希土類元素）：０．２質量％以
下，Ｙ：０．２質量％以下，Ｃａ：０．１質量％以下，
Ｍｇ：０．１０質量％以下の１種又は２種以上を含むこ
とができる。この場合、式（２）で定義されるＭｄ
（Ｎ）値が１００以上となるように成分調整される。 Md(N)＝580−520C−2Si−16Mn−16Cr−23Ni−26Cu−300N−10Mo ・・・（２）This precipitation hardening type martensitic stainless steel further has a Cu content of 5.0% by mass or less and an Nb content of 0.50%.
Mass% or less, Al: 2.0 mass% or less, B: 0.015
Mass% or less, REM (rare earth element): 0.2 mass% or less, Y: 0.2 mass% or less, Ca: 0.1 mass% or less,
Mg: One or more of 0.10% by mass or less can be contained. In this case, Md defined by equation (2)
(N) The component is adjusted so that the value becomes 100 or more. Md (N) = 580-520C-2Si-16Mn-16Cr-23Ni-26Cu-300N-10Mo (2)
【０００８】この析出硬化型マルテンサイト系ステンレ
ス鋼は、所定組成に調整されたステンレス鋼帯を溶体化
処理した後、４５０〜５５０℃で加熱する時効処理、次
いで５５０〜６５０℃に加熱してマトリックス中に３体
積％以上のオーステナイトを生成させる逆変態処理の２
段熱処理を施すことにより製造される。２段熱処理に先
立って、溶体化処理されたステンレス鋼を冷間圧延する
ことにより加工誘起マルテンサイトを生成させ、該加工
誘起マルテンサイトをオーステナイトに逆変態させるこ
とも可能である。逆変態処理では、８ｇ／ｃｍ2以上の
負荷を加えた状態で加熱すると、鋼帯の平坦度が更に向
上する。This precipitation hardening type martensitic stainless steel is prepared by subjecting a stainless steel strip adjusted to a predetermined composition to a solution treatment, then aging at 450 to 550 ° C., and then heating to 550 to 650 ° C. to form a matrix. Of reverse transformation to form 3% by volume or more austenite
It is manufactured by performing a step heat treatment. Prior to the two-step heat treatment, the solution-treated stainless steel may be cold-rolled to generate work-induced martensite, and the work-induced martensite may be reverse transformed into austenite. In the reverse transformation treatment, when heating is performed with a load of 8 g / cm 2 or more, the flatness of the steel strip is further improved.
【０００９】[0009]
【作用】本発明者等は、マルテンサイト系ステンレス鋼
板の製造条件が硬度及び形状平坦度に及ぼす影響を種々
調査検討した。その結果、溶体化処理後の冷却過程で生
成するマルテンサイト及び冷間圧延時に生成する加工誘
起マルテンサイトを加熱するとオーステナイトに逆変態
するが、このとき体積変化が形状平坦度の向上に利用で
きることを見出した。なお、本件明細書では、鋼板を包
含する意味で「鋼帯」を使用しているが、鋼板の熱処理
にあっても同様に逆変態オーステナイトが生じることは
勿論である。The present inventors have conducted various investigations and studies on the influence of the manufacturing conditions of the martensitic stainless steel sheet on the hardness and shape flatness. As a result, when the martensite generated in the cooling process after the solution treatment and the work-induced martensite generated during the cold rolling are heated, they reversely transform into austenite, and at this time, the volume change can be used to improve the shape flatness. I found it. In the present specification, “steel strip” is used to include a steel sheet, but it is a matter of course that reverse transformation austenite is similarly generated even in heat treatment of the steel sheet.
【００１０】本発明に従った熱処理工程では、溶体化処
理されたステンレス鋼帯を冷間圧延した後、時効処理
し、更に逆変態処理を施す（図１）。冷却過程でオース
テナイトからマルテンサイトに変態すると体積膨張が起
こり、早く冷却された部分で生じたマルテンサイト変態
に起因して鋼帯形状が崩れる。そこで、時効処理後にス
テンレス鋼帯を再加熱することによって加工誘起マルテ
ンサイトをオーステナイトに逆変態させる。この逆変態
により約１０％の体積収縮が生じ、マルテンサイト変態
時の鋼帯形状の崩れが解消される。また、逆変態時に外
力を加えると、拘束を受け継ぐ状態で変態が進行するた
め、鋼帯形状が更に改善される。[0010] In the heat treatment step according to the present invention, the solution-treated stainless steel strip is cold-rolled, then subjected to aging treatment, and further subjected to reverse transformation treatment (Fig. 1). When austenite is transformed to martensite during the cooling process, volume expansion occurs, and the steel strip shape is broken due to the martensite transformation generated in the rapidly cooled portion. Therefore, after the aging treatment, the stainless steel strip is reheated to reversely transform the work-induced martensite into austenite. This reverse transformation causes a volume shrinkage of about 10% and eliminates the collapse of the steel strip shape during the martensitic transformation. Further, when an external force is applied during the reverse transformation, the transformation proceeds in a state of inheriting the constraint, so that the shape of the steel strip is further improved.
【００１１】溶体化処理後の冷却過程及び冷間圧延過程
でマルテンサイトを生成させ、更に逆変態処理でオース
テナイトを生成させることによりマルテンサイト系ステ
ンレス鋼帯の形状平坦度が改善される。本発明では、こ
のようなマルテンサイト変態及び逆変態が形状平坦度に
及ぼす効果及び高硬度を維持する上で、次の合金設計を
採用した。[0011] By forming martensite in the cooling step and the cold rolling step after the solution treatment and further forming austenite in the reverse transformation treatment, the shape flatness of the martensitic stainless steel strip is improved. In the present invention, the following alloy design was adopted in order to maintain the effect of such martensitic transformation and reverse transformation on shape flatness and high hardness.
【００１２】Ｃ：０．１５質量％以下 オーステナイト形成元素であり、マルテンサイト相の強
化に極めて有効である。また、逆変態を低温側に下げる
ことによって逆変態オーステナイト量が制御しやすくな
り、形状矯正や高強度化に有効に作用する。しかし、Ｃ
含有量の増加に伴って溶体化処理後の冷却過程や時効処
理中にＣｒ系炭化物が粒界に析出し、耐粒界腐食や疲労
特性を低下させる原因になりやすい。そこで、Ｃｒ系炭
化物の粒界析出が熱処理条件や冷却速度で抑制できるよ
うに、Ｃ含有量の上限を０．１５質量％に設定した。 C: 0.15% by mass or less Austenite-forming element, which is extremely effective for strengthening the martensite phase. Further, by lowering the reverse transformation to a lower temperature side, the amount of the reverse transformation austenite is easily controlled, which effectively acts on shape correction and high strength. But C
As the content increases, Cr-based carbides precipitate at the grain boundaries during the cooling process after the solution treatment or during the aging treatment, and this is likely to cause a reduction in intergranular corrosion resistance and fatigue characteristics. Therefore, the upper limit of the C content is set to 0.15% by mass so that grain boundary precipitation of the Cr-based carbide can be suppressed by the heat treatment conditions and the cooling rate.
【００１３】Ｓｉ：２．０質量％以下 フェライト形成元素であり、マルテンサイト相に固溶し
て硬質化し、冷間加工後の強度を向上させる作用を呈す
る。時効処理に際しては、歪時効を促進させることによ
って時効硬化能を向上する。しかし、過剰量のＳｉ添加
は高温割れを誘発し、製造上で種々のトラブルを発生さ
せることから、Ｓｉ含有量の上限を２．０質量％に設定
した。 Si: 2.0 mass% or less Ferrite-forming element, which forms a solid solution with the martensite phase to be hardened, and has an effect of improving the strength after cold working. In the aging treatment, the age hardening ability is improved by promoting strain aging. However, excessive addition of Si induces high-temperature cracking and causes various troubles in production, so the upper limit of the Si content was set to 2.0% by mass.
【００１４】Ｍｎ：２．０質量％以下 高温域でのδフェライトの生成を抑制すると共に、Ｃと
同様に逆変態開始温度を低温側に下げる作用があるた
め、逆変態オーステナイト量を制御しやすくなる。しか
し、２．０質量％を超える過剰量のＭｎが含まれると、
焼鈍後の残留オーステナイト量が多くなり、強度低下の
原因になる。Ｎｉ：３．０〜１０．０質量％ Ｍｎと同様に高温域でのδフェライトの生成を抑制する
作用を呈する。また、Ｃと同様に逆変態開始温度を低温
側に下げる作用があるため、逆変態オーステナイト量を
制御しやすくなる。Ｎｉは、析出硬化能を向上させる上
でも有効な成分である。このような作用は、３．０質量
％以上のＮｉ量で顕著になる。しかし、１０．０質量％
を超えるＮｉの過剰添加は、残留オーステナイト量の増
加を招き、強度低下の原因となる。 Mn: 2.0% by mass or less Suppresses the formation of δ ferrite in a high temperature range and lowers the reverse transformation start temperature to a low temperature side like C, so that the amount of reverse transformation austenite can be easily controlled. Become. However, when an excessive amount of Mn exceeding 2.0% by mass is contained,
The amount of retained austenite after annealing increases, causing a reduction in strength. Ni: 3.0 to 10.0% by mass Similar to Mn, it has an effect of suppressing the formation of δ ferrite in a high temperature range. Further, since the effect of lowering the reverse transformation start temperature to the lower temperature side is obtained similarly to C, the amount of the reverse transformation austenite can be easily controlled. Ni is an effective component for improving the precipitation hardening ability. Such an effect becomes remarkable when the amount of Ni is 3.0% by mass or more. However, 10.0 mass%
Excessive addition of Ni exceeding 10% causes an increase in the amount of retained austenite and causes a decrease in strength.
【００１５】Ｃｒ：１２．０〜２０．０質量％ 耐食性向上に有効な合金成分であり、１２．０質量％以
上のＣｒ量で意図する耐食性が確保される。しかし、フ
ェライト形成元素であることから、過剰なＣｒ含有は高
温域でδフェライト相が多量に生成する原因となり、δ
フェライト相抑制のために必要なＣ，Ｎ，Ｎｉ，Ｍｎ，
Ｃｕ等のオーステナイト形成元素の増量を招く。オース
テナイト形成元素の多量添加は室温でオーステナイトを
安定化させ、時効処理による高強度化に支障をきたす。
そのため、オーステナイト形成元素の増量が必要とされ
ないように、Ｃｒ含有量の上限を２０．０質量％に設定
した。 Cr: An alloy component effective for improving the corrosion resistance of 12.0 to 20.0% by mass. The intended corrosion resistance is ensured at a Cr content of 12.0% by mass or more. However, since it is a ferrite forming element, excessive Cr content causes a large amount of δ ferrite phase to be formed in a high temperature range, and δ
C, N, Ni, Mn,
This causes an increase in the amount of austenite-forming elements such as Cu. Addition of a large amount of austenite-forming element stabilizes austenite at room temperature, and hinders high strength by aging treatment.
Therefore, the upper limit of the Cr content was set to 20.0% by mass so that the amount of the austenite-forming element was not required to be increased.
【００１６】Ｍｏ：４．０質量％以下 耐食性向上に有効な成分であり、逆変態処理時に炭窒化
物を微細に分散させる作用を呈する。また、形状矯正に
利用される逆変態処理では、加熱温度が通常の時効処理
温度よりも高く設定されるが、Ｍｏを添加していると高
温時効による急激な歪の解放が抑制される。このような
作用は、１．５質量％以上のＭｏ添加で顕著になる。し
かし、４．０質量％を超える過剰量のＭｏが含まれる
と、高温域でδフェライトが生成しやすくなる。 Mo: 4.0% by mass or less Mo is an effective component for improving corrosion resistance, and exhibits an action of finely dispersing carbonitride during reverse transformation treatment. In the reverse transformation treatment used for shape correction, the heating temperature is set higher than the normal aging treatment temperature. However, when Mo is added, rapid release of strain due to high-temperature aging is suppressed. Such an effect becomes remarkable by adding 1.5% by mass or more of Mo. However, when an excessive amount of Mo exceeding 4.0% by mass is contained, δ ferrite is easily generated in a high temperature region.
【００１７】Ｎ：０．０５質量％以下 Ｃと同様にオーステナイト形成元素であり、逆変態開始
温度を低温側に下げるため逆変態オーステナイト量を制
御しやすく、形状矯正及び高強度化に有効に作用する。
しかし、Ｔｉを添加している合金系では非金属介在物を
生成しやすい成分であることから、Ｎ含有量の上限を
０．０５質量％に設定した。Ｔｉ：０．５０質量％以下 析出硬化に有効な合金成分であり，逆変態処理時に強度
を上昇させる作用も呈する。しかし、０．５０質量％を
超える過剰量のＴｉが含まれると、スラブ表面に疵が発
生しやすくなり、製造面での問題が大きくなる。 N: 0.05% by mass or less N is an austenite-forming element like C. Since the reverse transformation start temperature is lowered to a lower temperature side, the amount of reverse transformation austenite is easily controlled, and it effectively acts on shape correction and high strength. I do.
However, the upper limit of the N content was set to 0.05% by mass, since the alloy system to which Ti is added is a component that easily generates nonmetallic inclusions. Ti: 0.50 mass% or less Ti is an alloy component effective for precipitation hardening, and also exhibits an effect of increasing the strength during the reverse transformation treatment. However, if an excessive amount of Ti exceeding 0.50% by mass is included, flaws are likely to be generated on the slab surface, and the problem in production becomes large.
【００１８】Ｃｕ：５．０質量％以下 必要に応じて添加される合金成分であり、オーステナイ
ト形成元素として働き、逆変態開始温度を低温側に下げ
ると共に、逆変態時に時効硬化作用を発現する。しか
し、５．０質量％を超えるＣｕの過剰添加は、熱間加工
性を劣化させ、割れ発生の原因になる。Ｎｂ：０．５０質量％以下 必要に応じて添加される合金成分であり、逆変態時の強
度上昇に有効である。しかし、高温強度上昇に起因して
熱間加工性を低下させる成分であることから、Ｎｂを添
加する場合には上限を０．５０質量％に設定する。 Cu: 5.0% by mass or less Cu is an alloy component added as necessary, acts as an austenite-forming element, lowers the reverse transformation start temperature to a lower temperature side, and exhibits an age hardening effect at the time of reverse transformation. However, excessive addition of Cu exceeding 5.0% by mass deteriorates hot workability and causes cracking. Nb: 0.50% by mass or less N is an alloy component added as necessary, and is effective in increasing the strength during reverse transformation. However, since Nb is a component that reduces hot workability due to an increase in high-temperature strength, the upper limit is set to 0.50% by mass when Nb is added.
【００１９】Ａｌ：２．０質量％以下 必要に応じて添加される合金成分であり、製鋼段階での
脱酸剤として働くと共に、Ｔｉ，Ｎｂと同様に析出硬化
能を上昇させる。しかし、２．０質量％を超えてＡｌを
添加しても、析出硬化能上昇に及ぼす効果が飽和するば
かりでなく、溶接性低下，表面欠陥の頻発等の弊害が現
れる。Ｂ：０．０１５質量％以下 必要に応じて添加される合金成分であり、熱間圧延温度
域においてδフェライト相とオーステナイト相の変形抵
抗の差に起因してエッジクラックが熱延鋼帯に発生する
ことを防止する作用を呈する。しかし、０．０１５質量
％を超える過剰量のＢを添加すると、低融点硼化物が生
成しやすくなり、却って熱間加工性が低下する。 Al: 2.0% by mass or less Al is an alloy component that is added as needed, acts as a deoxidizing agent in the steel making stage, and increases the precipitation hardening ability similarly to Ti and Nb. However, even if Al is added in excess of 2.0% by mass, the effect of increasing the precipitation hardening ability is not only saturated, but also adverse effects such as reduced weldability and frequent occurrence of surface defects appear. B: 0.015% by mass or less Alloy component added as required, and edge cracks occur in the hot-rolled steel strip due to the difference in deformation resistance between the δ ferrite phase and the austenite phase in the hot rolling temperature range. It has the effect of preventing the occurrence of However, if an excessive amount of B exceeding 0.015% by mass is added, a low-melting-point boride is likely to be formed, and the hot workability is rather deteriorated.
【００２０】ＲＥＭ（希土類元素）：０．２質量％以下 Ｙ：０．２質量％以下 Ｃａ：０．１質量％以下 Ｍｇ：０．１０質量％以下 必要に応じて添加される合金成分であり、何れも熱間加
工性を向上させる作用を呈し、耐酸化性の向上にも有効
である。しかし、これら作用は、ＲＥＭ（希土類元
素）：０．２質量％，Ｙ：０．２質量％，Ｃａ：０．１
質量％，Ｍｇ：０．１０質量％で飽和し、それ以上添加
しても鋼材の清浄度が悪くなる。 REM (rare earth element): 0.2% by mass or less Y: 0.2% by mass or less Ca: 0.1% by mass or less Mg: 0.10% by mass or less Alloy component added as necessary Both have the effect of improving hot workability and are also effective in improving oxidation resistance. However, these effects are as follows: REM (rare earth element): 0.2% by mass, Y: 0.2% by mass, Ca: 0.1%.
% By mass, Mg: Saturated at 0.10% by mass, and even if added more, the cleanliness of the steel material deteriorates.
【００２１】その他、Ｐ，Ｓ，Ｏ等が含まれることがあ
る。Ｐは、固溶強化能の大きな成分ではあるが、靭性に
悪影響を及ぼすことから、通常許容されている０．０６
０質量％に上限を設定することが好ましい。Ｓは、熱間
圧延時に耳割れ発生の原因となる有害元素であることか
ら低いほど好ましい。Ｓ起因の悪影響はＢ添加によって
抑制されるので、許容できるＳ量を０．０２０質量％以
下とする。Ｏは、酸化物系の非金属介在物となり鋼材の
清浄度を低下させ、プレス成形性や曲げ加工性に悪影響
を及ぼすことから０．０２質量％以下にすることが好ま
しい。In addition, P, S, O and the like may be included. Although P is a component having a large solid solution strengthening ability, it has an adverse effect on toughness.
It is preferable to set the upper limit to 0% by mass. Since S is a harmful element that causes ear cracks during hot rolling, the lower the S, the better. Since the adverse effect caused by S is suppressed by adding B, the allowable amount of S is set to 0.020% by mass or less. O becomes an oxide-based nonmetallic inclusion, lowers the cleanliness of the steel material, and has an adverse effect on press formability and bending workability.
【００２２】Ｍｄ（Ｎ）値：１００以上 Md(N)＝580−520C−2Si−16Mn−16Cr−23Ni−26Cu−300
N−10Mo 本発明の高強度マルテンサイト系ステンレス鋼帯では、
溶体化処理後又は冷間圧延後の逆変態処理によって逆変
態オーステナイトを生成させ、該逆変態オーステナイト
を再度マルテンサイト変態することにより形状矯正をし
ている。そのため、加工に対するオーステナイトの安定
度を示す指標であるＭｄ（Ｎ）値を１００以上とするこ
とにより、Ｍｆ点（冷却中にオーステナイトがマルテン
サイトの完全に変態する終了温度）が０〜５０℃とな
り、室温でほぼマルテンサイト単相の組織が得られる。 Md (N) value: 100 or more Md (N) = 580-520C-2Si-16Mn-16Cr-23Ni-26Cu-300
N-10Mo In the high-strength martensitic stainless steel strip of the present invention,
Reverse transformation austenite is generated by a reverse transformation treatment after solution treatment or after cold rolling, and the reverse transformation austenite is subjected to martensitic transformation again to correct the shape. Therefore, by setting the Md (N) value, which is an index indicating the stability of austenite to working, to 100 or more, the Mf point (the end temperature at which austenite completely transforms martensite during cooling) becomes 0 to 50 ° C. At room temperature, an almost martensitic single phase structure is obtained.
【００２３】以上のように成分調整されたステンレス鋼
は、逆変態を利用して形状矯正される。逆変態処理は、
溶体化処理後の冷却過程で生成するマルテンサイト及び
冷延工程で生成する加工誘起マルテンサイトを逆変態オ
ーステナイトにする処理であり、連続熱処理炉又はバッ
チ式加熱炉が使用される。逆変態処理では、マルテンサ
イトがオーステナイトに逆変態する温度域にステンレス
鋼帯が加熱される。The shape of the stainless steel component adjusted as described above is corrected by utilizing the reverse transformation. The reverse transformation process is
This is a process in which martensite generated in the cooling process after the solution treatment and work-induced martensite generated in the cold rolling process are converted into reverse transformed austenite, and a continuous heat treatment furnace or a batch heating furnace is used. In the reverse transformation treatment, the stainless steel strip is heated to a temperature range in which martensite is reverse transformed into austenite.
【００２４】適正な速度で逆変態オーステナイトを生成
させる上では、加熱温度を５５０〜６５０℃の範囲に設
定する。５５０℃未満の加熱温度では、逆変態オーステ
ナイトの生成反応が著しく遅く、工業生産上で不利にな
る。逆に６５０℃を超える加熱温度では、逆変態オース
テナイトの生成反応が極端に早くなり、マルテンサイト
も軟質化するため、３５０以上のビッカース硬度を安定
して確保することが困難になる。高すぎる加熱温度は、
炭化物析出に起因した鋭敏化によって耐食性を低下させ
る虞もある。In order to generate reverse transformed austenite at an appropriate rate, the heating temperature is set in the range of 550 to 650 ° C. At a heating temperature of less than 550 ° C., the reaction for forming the reverse transformed austenite is extremely slow, which is disadvantageous in industrial production. Conversely, if the heating temperature exceeds 650 ° C., the reaction for forming the reverse transformed austenite becomes extremely fast, and the martensite becomes soft, so that it becomes difficult to stably secure a Vickers hardness of 350 or more. Heating temperature that is too high
Corrosion resistance may be reduced due to sensitization caused by carbide precipitation.
【００２５】マルテンサイトからオーステナイトに逆変
態する際、収縮変形による形状矯正効果が発現し、コイ
ル間の張力によって鋼帯の形状が良好に確保され、或い
は鋼板自体の自重によって良好な鋼板形状が確保され
る。本発明者等の調査・研究によるとき、３％以上の逆
変態オーステナイトを生成させると逆変態処理の効果が
顕著になることを見出した。また、押し板等によって鋼
板に荷重を加えた状態で逆変態処理すると、鋼板形状が
更に改善される。この場合、逆変態時の高温強度を考慮
すると、単位面積当り８ｇ／ｃｍ2以上の荷重を加える
ことが好ましい。During the reverse transformation from martensite to austenite, a shape correcting effect is exhibited by shrinkage deformation, and a good shape of the steel strip is secured by the tension between the coils, or a good shape of the steel sheet is secured by the weight of the steel sheet itself. Is done. According to investigations and studies by the present inventors, it has been found that when 3% or more of reverse transformed austenite is generated, the effect of the reverse transformation treatment becomes significant. In addition, when the reverse transformation process is performed in a state where a load is applied to the steel plate by a push plate or the like, the shape of the steel plate is further improved. In this case, it is preferable to apply a load of 8 g / cm 2 or more per unit area in consideration of the high temperature strength at the time of reverse transformation.
【００２６】[0026]
【実施例】表１の組成をもつステンレス鋼を真空溶解炉
で２５０ｋｇ溶製し、鍛造，熱延，焼鈍，冷延を経て板
厚１．０〜１．５ｍｍの冷延板を製造した。表中、１〜
７が本発明で規定した条件を満足するステンレス鋼、８
〜１４が本発明で規定した条件を外れるステンレス鋼で
ある。EXAMPLE 250 kg of stainless steel having the composition shown in Table 1 was melted in a vacuum melting furnace and subjected to forging, hot rolling, annealing and cold rolling to produce a cold rolled sheet having a thickness of 1.0 to 1.5 mm. In the table, 1 to
7 is a stainless steel satisfying the conditions specified in the present invention, 8
No. to No. 14 are stainless steels out of the conditions specified in the present invention.
【００２７】 [0027]
【００２８】各ステンレス鋼帯を１０５０℃×１分で焼
鈍した後、一部の鋼帯を冷間圧延し、更に全鋼帯を時効
処理し、次いで６００秒の逆変態処理を施した。冷間圧
延，時効処理及び逆変体処理の条件を表２に示す。製造
された各鋼帯について、冷却中３００℃近傍でフェライ
ト含量計を用いた磁気的測定法で保持時間６００秒の逆
変態処理で生成した逆変態オーステナイト量を測定し
た。逆変態処理された鋼帯の幅方向両側１０ｍｍを切り
落として板幅２００ｍｍ、長さ１５００ｍｍの鋼板を切
り出し、最大耳高さで鋼帯の平坦度を評価した。測定結
果を、表面ビッカース硬度（荷重１０ｋｇ）と共に、表
２に併せ示す。After annealing each stainless steel strip at 1050 ° C. for 1 minute, a part of the steel strip was cold-rolled, all the steel strips were aged, and then reverse transformation was performed for 600 seconds. Table 2 shows the conditions of the cold rolling, the aging treatment, and the reverse transformation treatment. For each of the manufactured steel strips, the amount of reverse transformed austenite generated by the reverse transformation treatment with a holding time of 600 seconds was measured at around 300 ° C. by a magnetic measurement method using a ferrite content meter during cooling. A steel plate having a width of 200 mm and a length of 1500 mm was cut out by cutting 10 mm on both sides in the width direction of the steel strip subjected to the reverse transformation treatment, and the flatness of the steel strip was evaluated at the maximum ear height. Table 2 shows the measurement results together with the surface Vickers hardness (load: 10 kg).
【００２９】表２にみられるように、試験番号１〜１１
（本発明例）では、平均ビッカース硬度が３５０以上、
逆変態処理された鋼帯の最大耳高さが３．０ｍｍ以下に
なっていた。他方、試験番号１２〜１４は、本発明で規
定した組成を満足するものではあるが、時効処理温度が
４５０〜５５０℃外れる試験番号１２，１３や逆変態処
理温度が６５０℃を超える試験番号１４では、材料の軟
化が著しく進行し、３５０未満のビッカース硬度を示し
た。本発明で規定した組成を外れる試験番号１５〜２０
では、ビッカース硬度３５０以上で且つ優れた形状の鋼
帯が得られなかった。また、試験番号１２，１７．１８
では、ＴｉＮやＡｌＮに起因する表面欠陥が発生し、炭
素含有量の多い試験番号２０では逆変態処理後の放置期
間に部分的な錆が発生した。As shown in Table 2, test numbers 1 to 11
(Example of the present invention), the average Vickers hardness is 350 or more,
The maximum ear height of the reverse-transformed steel strip was 3.0 mm or less. On the other hand, although Test Nos. 12 to 14 satisfy the composition specified in the present invention, Test Nos. 12 and 13 in which the aging temperature deviates from 450 to 550 ° C. and Test No. 14 in which the reverse transformation temperature exceeds 650 ° C. In Example 1, the material softened remarkably, and showed a Vickers hardness of less than 350. Test numbers 15 to 20 deviating from the composition specified in the present invention
Did not provide a steel strip having a Vickers hardness of 350 or more and an excellent shape. In addition, test numbers 12, 17.18
In Test No. 2, surface defects caused by TiN and AlN occurred, and in Test No. 20 having a large carbon content, partial rust occurred during the standing period after the reverse transformation treatment.
【００３０】 [0030]
【００３１】鋼板形状を更に矯正するため、鋼帯幅方向
両側１０ｍｍをカットして切り出した幅２００ｍｍ，長
さ３００ｍｍの鋼板に表３に示す各種押え圧で厚板を挟
み込んだ。この条件下で６００秒の逆変態処理し、鋼板
に加えた荷重が鋼板平坦度に及ぼす影響を調査した。調
査結果を、逆変態オーステナイト量及び表面平均ビッカ
ース硬度（荷重１０ｋｇ）と共に表３に示す。表３にみ
られるように、逆変態処理中の鋼板に荷重を加えること
により、最大耳高さが１．０ｍｍ以下と更に小さくなっ
た。加えた荷重と最大耳高さとの関係から、８ｇ／ｃｍ
2以上の荷重で鋼板が効果的に形状矯正されることが判
る。To further correct the shape of the steel plate, a thick plate was sandwiched between steel plates having a width of 200 mm and a length of 300 mm by cutting and cutting 10 mm on both sides in the width direction of the steel strip with various pressing pressures shown in Table 3. Under these conditions, reverse transformation treatment was performed for 600 seconds, and the effect of the load applied to the steel sheet on the flatness of the steel sheet was examined. The results of the investigation are shown in Table 3 together with the amount of reverse transformation austenite and the surface average Vickers hardness (load: 10 kg). As shown in Table 3, the maximum ear height was further reduced to 1.0 mm or less by applying a load to the steel sheet undergoing the reverse transformation. From the relationship between the applied load and the maximum ear height, 8 g / cm
It can be seen that the shape of the steel sheet is effectively corrected with a load of 2 or more.
【００３２】 [0032]
【００３３】[0033]
【発明の効果】以上に説明したように、本発明のマルテ
ンサイト系ステンレス鋼帯は、成分を適正に管理すると
共に逆変態オーステナイトに由来するマルテンサイトを
分散させることにより形状平坦度が良好である。ビッカ
ース硬度も３５０以上の高い値を示し、耐食性にも優れ
ていることから、プレスプレート，ステンレスフレー
ム，板バネ，フラッパーバルブ，メタルガスケット，ラ
ッピングキャリア材，キャリアプレート，ステンレスミ
ラー，ダンパースプリング，ディスクブレーキ，ブレー
キマスターキー，スチールベルト，メタルマスク等の各
種バネ材や高強度材として広範な分野で使用される。As described above, the martensitic stainless steel strip of the present invention has good shape flatness by properly controlling the components and dispersing the martensite derived from reverse transformed austenite. . Vickers hardness is high value of 350 or more, and it has excellent corrosion resistance. Therefore, press plate, stainless steel frame, leaf spring, flapper valve, metal gasket, wrapping carrier material, carrier plate, stainless steel mirror, damper spring, disk brake It is used in a wide range of fields as various spring materials and high-strength materials such as brake master keys, steel belts, and metal masks.
【図１】 本発明に従った熱処理工程を示す図FIG. 1 is a diagram showing a heat treatment step according to the present invention.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 藤本 廣 山口県新南陽市野村南町4976番地 日新製 鋼株式会社ステンレス事業本部内 Ｆターム(参考） 4K037 EA01 EA02 EA04 EA05 EA06 EA09 EA12 EA13 EA14 EA15 EA17 EA18 EA19 EA20 EA21 EA27 EA28 EA36 EB11 EB13 FL02 FM01 HA05 ────────────────────────────────────────────────── ─── Continued on the front page (72) Inventor Hiroshi Fujimoto 4976 Nomura Minamicho, Shinnanyo-shi, Yamaguchi Prefecture F-term (reference) 4N037 EA01 EA02 EA04 EA05 EA06 EA09 EA12 EA13 EA14 EA15 EA17 EA18 EA19 EA20 EA21 EA27 EA28 EA36 EB11 EB13 FL02 FM01 HA05
Claims (5)
質量％以下，Ｍｎ：２．０質量％以下，Ｎｉ：３．０〜
１０．０質量％，Ｃｒ：１２．０〜２０．０質量％，Ｍ
ｏ：４．０質量％以下，Ｎ：０．０５質量％以下，Ｔ
ｉ：０．５０質量％以下，残部が実質的にＦｅで、式
（１）で定義されるＭｄ（Ｎ）値が１００以上の組成を
もち、逆変態オーステナイトから生成したマルテンサイ
トがマトリックスに分散している組織をもつことを特徴
とする形状平坦度に優れたビッカース硬さＨＶ３５０以
上の析出硬化型マルテンサイト系ステンレス鋼。 Md(N)＝580−520C−2Si−16Mn−16Cr−23Ni−300N−10Mo・・・（１）C: 0.15% by mass or less, Si: 2.0
Mass% or less, Mn: 2.0 mass% or less, Ni: 3.0 to
10.0% by mass, Cr: 12.0 to 20.0% by mass, M
o: 4.0% by mass or less, N: 0.05% by mass or less, T
i: 0.50% by mass or less, balance being substantially Fe, having a composition having an Md (N) value defined by the formula (1) of 100 or more, and dispersing martensite generated from inversely transformed austenite in a matrix. A precipitation-hardening martensitic stainless steel having a Vickers hardness of HV350 or more, which is excellent in shape flatness and characterized by having a texture in the form. Md (N) = 580-520C-2Si-16Mn-16Cr-23Ni-300N-10Mo ... (1)
０．５０質量％以下，Ａｌ：２．０質量％以下，Ｂ：
０．０１５質量％以下，ＲＥＭ（希土類元素）：０．２
質量％以下，Ｙ：０．２質量％以下，Ｃａ：０．１質量
％以下，Ｍｇ：０．１０質量％以下の１種又は２種以上
を含み、式（２）で定義されるＭｄ（Ｎ）値が１００以
上である請求項１記載の析出硬化型マルテンサイト系ス
テンレス鋼。 Md(N)＝580−520C−2Si−16Mn−16Cr−23Ni−26Cu−300N−10Mo ・・・（２）2. Cu: 5.0 mass% or less, Nb:
0.50% by mass or less, Al: 2.0% by mass or less, B:
0.015% by mass or less, REM (rare earth element): 0.2
Md (Md) contains one or more of Y, 0.2% by mass or less, Ca: 0.1% by mass or less, and Mg: 0.10% by mass or less, and is defined by the formula (2). The precipitation hardening type martensitic stainless steel according to claim 1, wherein N) value is 100 or more. Md (N) = 580-520C-2Si-16Mn-16Cr-23Ni-26Cu-300N-10Mo (2)
鋼を溶体化処理した後、４５０〜５５０℃で加熱する時
効処理、次いで５５０〜６５０℃に加熱してマトリック
ス中に３体積％以上のオーステナイトを生成させる逆変
態処理の２段熱処理を施すことを特徴とする形状平坦度
に優れたマルテンサイト系ステンレス鋼の製造方法。3. A solution treatment of the stainless steel having the composition according to claim 1 or 2, followed by aging treatment at 450 to 550 ° C., and then heating at 550 to 650 ° C. to form 3% by volume or more in the matrix. A method for producing a martensitic stainless steel having excellent shape flatness, comprising performing a two-step heat treatment of a reverse transformation treatment for forming austenite.
延する請求項３記載の製造方法。4. The production method according to claim 3, wherein cold rolling is performed between the solution treatment and the two-step heat treatment.
逆変態処理し、最大耳高さ１．０ｍｍ以下とする請求項
３又は４記載の製造方法。5. The method according to claim 3, wherein the reverse transformation is performed under a load of 8 g / cm 2 or more to reduce the maximum ear height to 1.0 mm or less.
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| JP2000368532A JP2002173740A (en) | 2000-12-04 | 2000-12-04 | Precipitation hardening martensitic stainless steel strip having excellent shape flatness and its production method |
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|---|---|---|---|
| JP2000368532A JP2002173740A (en) | 2000-12-04 | 2000-12-04 | Precipitation hardening martensitic stainless steel strip having excellent shape flatness and its production method |
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| JP2002173740A true JP2002173740A (en) | 2002-06-21 |
Family
ID=18838744
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|---|---|---|---|
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| Country | Link |
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| JP (1) | JP2002173740A (en) |
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