JP2002146488A - Martensitic stainless steel having excellent workability - Google Patents
Martensitic stainless steel having excellent workabilityInfo
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- JP2002146488A JP2002146488A JP2001263693A JP2001263693A JP2002146488A JP 2002146488 A JP2002146488 A JP 2002146488A JP 2001263693 A JP2001263693 A JP 2001263693A JP 2001263693 A JP2001263693 A JP 2001263693A JP 2002146488 A JP2002146488 A JP 2002146488A
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Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、例えば二輪車のデ
ィスクブレーキ材などの車輌部材や機械部材などの用途
に好適な、焼入れたままで用いるマルテンサイト系ステ
ンレス鋼に関し、必要な焼入れ特性のほか、とくに焼き
入れ前には優れた加工性（打抜加工性、曲げ加工性な
ど）を有するマルテンサイト系ステンレス鋼を提案する
ものである。なお、本発明にいう％は、特にことわらな
いかぎり、すべて質量％を意味するものとする。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a martensitic stainless steel used as-quenched, which is suitable for use as a vehicle member or a machine member such as a disc brake material of a motorcycle, for example. It proposes a martensitic stainless steel having excellent workability (such as punching workability and bending workability) before quenching. In the present invention, all percentages mean mass% unless otherwise specified.
【０００２】[0002]
【従来の技術】二輪車のディスクブレーキ材には、ブレ
ーキとしての性能を長期間維持するために耐摩耗性が必
要である。この耐摩耗性は、一般に硬度が高くなるに従
い良好となるが、一方、靱性は逆に低下する。これらの
点を考慮して、耐摩耗性と靱性の両方を要求される車両
や機械の部材には、ロックウェル硬度ＨＲＣで30〜40の
範囲に制御された鋼が用いられる場合が多い。従来、こ
の用途に使用されるステンレス鋼としては、Ｃ：0.2％
の SUS 420J1およびＣ：0.3％の SUS 420J2等の高Ｃマ
ルテンサイト系ステンレス鋼か、低Ｃ高Mnマルテンサイ
ト系ステンレス鋼が用いられてきた。2. Description of the Related Art Disc brake materials for motorcycles need to have wear resistance in order to maintain the performance as a brake for a long period of time. The wear resistance generally improves as the hardness increases, but on the other hand, the toughness decreases. In consideration of these points, steel whose rockwell hardness HRC is controlled in the range of 30 to 40 is often used for members of vehicles and machines that require both wear resistance and toughness. Conventionally, as the stainless steel used for this purpose, C: 0.2%
High C martensitic stainless steel or low C high Mn martensitic stainless steel such as SUS420J1 and C: 0.3% SUS420J2 has been used.
【０００３】しかし、上記 SUS 420J1、SUS 420J2等の
高Ｃマルテンサイト系ステンレス鋼では、焼入れ温度が
変動したときの硬度の変化が大きいために、焼入れのみ
で所定の硬度を得るには、極めて精度の高い熱処理管理
が必要であった。また、仮に焼戻しにより焼入れ条件の
管理を緩和できたとしても、焼戻しによって析出するCr
炭窒化物の周囲に、低Cr濃度の領域が生じて、耐食性が
低下するという難点があった。However, in the above-mentioned high C martensitic stainless steels such as SUS420J1, SUS420J2, etc., the hardness changes greatly when the quenching temperature fluctuates. High heat treatment management was required. Also, even if tempering could moderate the management of quenching conditions,
There is a problem that a region with a low Cr concentration is formed around the carbonitride and the corrosion resistance is reduced.
【０００４】一方、特公昭60−2380号公報に示されるよ
うな低Ｃ高Mnマルテンサイト系ステンレス鋼では、焼入
れ温度に対する硬度の変動が少ないため、高Ｃマルテン
サイト系ステンレス鋼におけるような過酷な熱処理条件
の管理は不要となる。しかし、この材料を用いてディス
クブレーキなどの部材を製造する際には、焼入れ前の打
ち抜き工程で、打ち抜き型で剪断される近傍が塑性変形
域に引きずり込まれて、「ダレ（垂れ下がり・反り上が
りともいう）」（図１参照）になりやすく、加工精度を
低下させるという問題が残されていた。打ち抜き部の縁
辺部にダレが発生すると、外形の維持、他部材と摺動し
たときのビビリ防止等の必要性から、その後の工程で、
ダレを除去するために、切削・研摩作業を余分に行わな
ければならず、工数負荷の増大と歩止ロスを招くことに
なる。On the other hand, in a low C high Mn martensitic stainless steel as disclosed in Japanese Patent Publication No. 60-2380, there is little variation in hardness with respect to the quenching temperature. Management of heat treatment conditions is not required. However, when manufacturing components such as disc brakes using this material, in the punching process before quenching, the area that is sheared by the punching die is dragged into the plastic deformation area, and the sag (sagging / curling) occurs. (See FIG. 1), and there remains a problem that the processing accuracy is reduced. If sagging occurs at the edge of the punched part, it is necessary to maintain the outer shape and prevent chatter when sliding with other members, so in the subsequent process,
In order to remove the sagging, extra cutting and polishing work must be performed, resulting in an increase in man-hour load and a loss in yield.
【０００５】前述した部材を製造するのに求められるこ
のほかの特性としては、焼入れ前の成形性（曲げ成形
性）、被削性（穴あけ性等）が、さらにまた、焼入れ加
熱時の耐酸化性などが挙げられる。しかし、これら何れ
の特性についても、従来の成分系の鋼では限界があり、
改善の余地が残されていた。[0005] Other characteristics required for manufacturing the above-mentioned members include the formability before bending (bending formability) and the machinability (such as drilling properties), and the oxidation resistance during quenching heating. And the like. However, with respect to any of these properties, there is a limit in conventional component steel.
There was room for improvement.
【０００６】[0006]
【発明が解決しようとする課題】このように、従来の低
Ｃ高Mnマルテンサイト系ステンレス鋼は、焼入れ硬度の
焼入れ温度依存性が小さいために、熱処理管理が容易で
あると言う利点を有していたものの、一方では、焼入れ
前の加工成形段階において、特に打ち抜き加工でダレが
生じるという問題があった。さらに、焼入れ前の加工成
形においては、厳しい曲げ加工のときに割れが発生する
という問題もあった。このほか、従来技術では、焼入れ
前の被削性（穴あけ性）や焼入れ加熱時の耐酸化性も、
必ずしも十分ではなかった。そこで、本発明は、従来技
術が抱えているかかる問題を解消して、所定の焼入れ硬
度が安定して得られるとともに、焼入れ前における、打
ち抜き加工性、曲げ加工性に優れたマルテンサイト系ス
テンレス鋼を提供することにある。さらに、本発明は、
被削性、焼入れ時の耐酸化性をも一段と改善したマルテ
ンサイト系ステンレス鋼を提供することにある。As described above, the conventional low C high Mn martensitic stainless steel has the advantage that the heat treatment can be easily controlled because the quenching hardness has a small dependence on the quenching temperature. On the other hand, on the other hand, there is a problem that sagging occurs in the working and forming step before quenching, particularly during punching. Further, in the work forming before quenching, there is a problem that cracks occur during severe bending. In addition, in the prior art, the machinability (drillability) before quenching and the oxidation resistance during quenching
Not always enough. Therefore, the present invention solves the above-described problems of the prior art, and provides a predetermined quenching hardness stably, and before quenching, a martensitic stainless steel excellent in punching workability and bending workability. Is to provide. Further, the present invention provides
An object of the present invention is to provide a martensitic stainless steel having further improved machinability and oxidation resistance during quenching.
【０００７】[0007]
【課題を解決するための手段】本発明の要旨構成は以下
のとおりである。 (1) 質量％で、Ｃ＋Ｎ：0.04超〜0.10％、Si：0.5％以
下、Mn：1.0〜2.5％、Cr：10.0超〜14.5％、Al：0.100
％以下を含み、かつＶ：0.40％以下、Ti：0.40％以下、
Zr：0.40％以下、Ta：0.40％以下、Hf：0.40％以下から
選ばれる１種または２種以上を合計で0.02〜0.40％含有
し、残部はFeおよび不可避的不純物から成ることを特徴
とする加工性に優れたマルテンサイト系ステンレス鋼。The gist of the present invention is as follows. (1) In mass%, C + N: more than 0.04 to 0.10%, Si: 0.5% or less, Mn: 1.0 to 2.5%, Cr: more than 10.0 to 14.5%, Al: 0.100
%: V: 0.40% or less, Ti: 0.40% or less,
One or more selected from the group consisting of Zr: 0.40% or less, Ta: 0.40% or less, and Hf: 0.40% or less in a total amount of 0.02 to 0.40%, with the balance being Fe and unavoidable impurities. Martensitic stainless steel with excellent workability.
【０００８】(2)上記(1)に記載の成分に加え、さらに、
質量％で、Ni：0.6％以下、Cu：0.5％以下から選ばれる
１種または２種を含むことを特徴とする加工性に優れた
マルテンサイト系ステンレス鋼。(2) In addition to the components described in the above (1),
A martensitic stainless steel excellent in workability, characterized by containing one or two types selected from Ni: 0.6% or less and Cu: 0.5% or less by mass%.
【０００９】(3)上記(1)または(2)に記載の成分に加
え、さらに、質量％で、Mo：0.012〜0.500％を含むこと
を特徴とする加工性に優れたマルテンサイト系ステンレ
ス鋼。(3) A martensitic stainless steel excellent in workability, characterized by containing Mo: 0.012 to 0.500% by mass% in addition to the components described in the above (1) or (2). .
【００１０】(4)上記(1)〜(3)のいずれか１つに記載の
成分に加え、さらに、質量％で、Ｂ：0.0002〜0.0050％
を含むことを特徴とする加工性に優れたマルテンサイト
系ステンレス鋼。(4) In addition to the components described in any one of (1) to (3) above, B: 0.0002 to 0.0050% by mass%
A martensitic stainless steel excellent in workability, characterized by containing.
【００１１】(5)上記(1)〜(4)のいずれか１つに記載の
成分に加え、さらに、質量％で、Co：0.50％以下、Ｗ：
0.30％以下から選ばれる１種または２種を含むことを特
徴とする加工性に優れたマルテンサイト系ステンレス
鋼。(5) In addition to the components described in any one of (1) to (4) above, further, in mass%, Co: 0.50% or less, W:
A martensitic stainless steel excellent in workability, characterized by containing one or two selected from 0.30% or less.
【００１２】(6)上記(1)〜(5)のいずれか１つに記載の
成分に加え、さらに、質量％で、Ca：0.0050％以下、M
g：0.0050％以下から選ばれる１種または２種を含むこ
とを特徴とする加工性に優れたマルテンサイト系ステン
レス鋼。(6) In addition to the components described in any one of (1) to (5) above, further, in mass%, Ca: 0.0050% or less, M
g: A martensitic stainless steel excellent in workability, characterized by containing one or two selected from 0.0050% or less.
【００１３】[0013]
【発明の実施の形態】以下、本発明のマルテンサイト系
ステンレス鋼の成分組成を、上記範囲に限定した理由に
ついて説明する。 (Ｃ＋Ｎ)：0.04超〜0.10％ ＣおよびＮは、いずれも硬度を高め、耐摩耗性を向上さ
せるのに有効な元素であり、本発明のMn量の範囲におい
て、焼入れ時の硬度をＨＲＣ30〜40にするためには、
(Ｃ＋Ｎ)量は、0.04％を超え0.10％以下の範囲とする必
要がある。DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS The reason why the composition of the martensitic stainless steel of the present invention is limited to the above range will be described below. (C + N): more than 0.04 to 0.10% C and N are both effective elements for increasing the hardness and improving the wear resistance. Within the range of the Mn content of the present invention, the hardness at the time of quenching is HRC 30 to To get to 40,
The (C + N) amount needs to be in the range of more than 0.04% and 0.10% or less.
【００１４】Si：0.5％以下 Siは、高温においてフェライトを生成させる元素であ
る。しかし、0.5％を超えると焼入れ硬度を低下させる
のみならず、靱性に悪影響を与えるので、その上限を0.
50％とする。なお、Si量は少ないほど好ましい。Si: 0.5% or less Si is an element that forms ferrite at a high temperature. However, if it exceeds 0.5%, not only does the quenching hardness decrease, but it also has an adverse effect on toughness.
50%. Note that the smaller the amount of Si, the better.
【００１５】Mn：1.0〜2.5％ Mnは、高温におけるδ−フェライトの生成を抑制するの
に有効な元素である。1.0％未満の含有量ではδ−フェ
ライトを生成し、ＨＲＣ30〜40の焼入れ硬度が得られな
くなる。なお、ＨＲＣ30〜40の焼入れ硬度を、高(Ｃ＋
Ｎ)の成分系で達成しようとすると、(Ｃ＋Ｎ)量の適正
範囲が著しく狭くなるため、製造性が低下する。また、
Mn量が低すぎると、ＨＲＣ30〜40の焼入れ硬度を得るた
めの焼入れ熱処理の温度範囲が極端に狭小となるため、
温度管理も難しくなるので、その下限を1.0％とする。
一方、Mn量が2.5％を超えると、高温での耐酸化性が低
下し、鋼板の製造工程におけるスケール生成量が多くな
り、板面に肌荒を生じて、鋼板の寸法精度を著しく低下
させるので、その上限を2.5％に限定する。Mn: 1.0-2.5% Mn is an effective element for suppressing the formation of δ-ferrite at high temperatures. If the content is less than 1.0%, δ-ferrite is formed, and a quench hardness of HRC 30 to 40 cannot be obtained. In addition, the quenching hardness of HRC30-40 is high (C +
If an attempt is made to achieve this with the component system (N), the appropriate range of the (C + N) amount is significantly narrowed, resulting in reduced manufacturability. Also,
If the Mn content is too low, the temperature range of the quenching heat treatment for obtaining a quench hardness of HRC 30 to 40 becomes extremely narrow,
Since the temperature control becomes difficult, the lower limit is set to 1.0%.
On the other hand, if the Mn content exceeds 2.5%, the oxidation resistance at high temperatures decreases, the amount of scale generated in the steel plate manufacturing process increases, the surface of the plate becomes rough, and the dimensional accuracy of the steel plate decreases significantly. Therefore, the upper limit is limited to 2.5%.
【００１６】Cr：10.0超〜14.5％ Crは、耐食性を保持するために10.0％超の含有量が不可
欠である。しかし、14.5％を超えると、Mn，NiおよびCu
のそれぞれ上限量を添加しても、850〜1050℃の焼入れ
温度範囲でδ−フェライトが出現するようになり、ＨＲ
Ｃ30〜40の焼入れ硬度が得られなくなる。よって、Cr含
有量は10.0超〜14.5％の範囲とする。Cr: more than 10.0 to 14.5% Cr must have a content of more than 10.0% in order to maintain corrosion resistance. However, when it exceeds 14.5%, Mn, Ni and Cu
Δ-ferrite appears in the quenching temperature range of 850 to 1050 ° C.
C30-40 hardening hardness cannot be obtained. Therefore, the Cr content is in the range of more than 10.0 to 14.5%.
【００１７】Ｖ：0.40％以下、Ti：0.40％以下、Zr：0.
40％以下、Ta：0.40％以下、Hf：0.40％以下、かつこれ
らの合計量：0.02〜0.40％ Ｖ，Ti，Zr，Ta，Hfは、本発明においては極めて重要な
元素である。Ｖ，Ti，Zr，Ta，Hfの量を、単独で0.40％
以下、合計量で0.02〜0.40％含有することにより、鋼板
の結晶粒を微細化し、かつ再結晶後の粒成長を抑制する
効果を有する。V: 0.40% or less, Ti: 0.40% or less, Zr: 0.
40% or less, Ta: 0.40% or less, Hf: 0.40% or less, and their total amount: 0.02 to 0.40% V, Ti, Zr, Ta, and Hf are extremely important elements in the present invention. The amount of V, Ti, Zr, Ta, Hf is 0.40% alone
Hereinafter, by containing 0.02 to 0.40% in total, it has an effect of refining the crystal grains of the steel sheet and suppressing the grain growth after recrystallization.
【００１８】これら元素を少なくとも１種添加すること
により、結晶粒の細粒化が達成されて、焼き入れ前にお
ける打ち抜き加工の際のダレが改善され、同時に焼入れ
後の靱性も維持される。このような効果が得られる機構
は、必ずしも明らかではないが、以下によるものと考え
ている。 (1)結晶粒内の転位が結晶粒界に集積し易くなり、塑性
変形に対する抵抗力が大きくなる。そのため、打ち抜き
加工の際の塑性変形領域が、剪断面近傍に限定されてダ
レが小さくなる。 (2)粒界は、応力集中が大きく、亀裂の伝播経路になる
が、細粒化により粒界面積が増大し、単位粒界面積当り
の応力集中が緩和され、靱性が維持される。なお、この
ような細粒化に伴う硬質化の傾向があるにもかかわら
ず、焼入れ後の硬度が従来材並みの値を示している理由
として、Ｖ，Ti，Zr，Ta，Hfがフェライト生成を促進し
て、焼入れによる硬化を低減するので、細粒化の効果と
相殺されることが考えられる。こうしたＶ，Ti，Zr，T
a，Hfの作用は、合計量で0.02％以上の含有で得られる
が、単独、合計いずれでも0.40％を超えると、高温での
耐酸化性が低下し、鋼板製造工程におけるスケール起因
の表面欠陥を防止する上で不利となる。よって、上記範
囲に限定する。ところで、Ｖは、含有量が0.18％を超え
ると、焼入れ前における打ち抜き加工時の剪断面の割
れ、荒れが発生する場合があるため、0.18％以下とする
のが好ましい。0.09％以下とするとさらに好ましい。By adding at least one of these elements, grain refinement of the crystal grains is achieved, sag during punching before quenching is improved, and toughness after quenching is also maintained. The mechanism by which such an effect is obtained is not necessarily clear, but is considered to be as follows. (1) Dislocations in crystal grains are likely to accumulate at crystal grain boundaries, and resistance to plastic deformation is increased. Therefore, the plastic deformation region at the time of punching is limited to the vicinity of the shear surface, and the sag becomes small. (2) The grain boundary has a large stress concentration and becomes a crack propagation path. However, the grain boundary area is increased by the refinement, the stress concentration per unit grain boundary area is reduced, and the toughness is maintained. The reason that the hardness after quenching shows a value similar to that of the conventional material despite the tendency of hardening due to the grain refinement is that V, Ti, Zr, Ta, and Hf have ferrite formation. Is promoted, and hardening due to quenching is reduced, which is considered to be offset by the effect of grain refinement. V, Ti, Zr, T
The effects of a and Hf can be obtained with a total content of 0.02% or more. However, if the total content exceeds 0.40%, both alone and in total, the oxidation resistance at high temperatures decreases, and surface defects caused by scale in the steel sheet manufacturing process Is disadvantageous in preventing Therefore, it is limited to the above range. By the way, if the content of V exceeds 0.18%, the shear surface may be cracked or roughened at the time of punching before quenching, so V is preferably set to 0.18% or less. More preferably, the content is 0.09% or less.
【００１９】Al：0.100％以下 Alは、脱酸に有効な元素であるため、必要に応じて含有
してもよい。ただし、多すぎるとＮと結合して、成形
性、特に伸びを低下させるので、上限を0.100％とす
る。Al: 0.100% or less Al is an element effective for deoxidation, and may be contained as necessary. However, if the content is too large, it bonds with N and lowers the formability, particularly the elongation, so the upper limit is made 0.100%.
【００２０】Ni：0.6％以下、Cu：0.5％以下 NiおよびCuは、いずれもMnと同様に、高温におけるδフ
ェライトの生成を防止するのに有効である。本発明にお
いては、Mn量1.0〜2.5％の添加によってその目的を達せ
られるので、必要に応じて添加することができる。その
際、Niは、過度に添加すると、焼入れ後の硬度のばらつ
きを大きくし、またCuは、高温での熱間圧延時に表面疵
を発生し、歩留を低下させるので、Ni：0.6％以下、C
u：0.5％以下の範囲で含有させる。Ni: 0.6% or less, Cu: 0.5% or less Both Ni and Cu, like Mn, are effective in preventing the formation of δ ferrite at high temperatures. In the present invention, the purpose can be achieved by adding an Mn content of 1.0 to 2.5%, so that it can be added as needed. At that time, if Ni is added excessively, the hardness variation after quenching increases, and Cu generates surface defects at the time of hot rolling at high temperature and lowers the yield. Ni: 0.6% or less , C
u: 0.5% or less.
【００２１】Mo：0.012〜0.500％ Moは、ステンレス鋼の耐食性を付加的に高めるので、必
要に応じて、添加される元素である。耐食性向上の効果
を発揮させるには、0.012％以上の添加が必要である
が、過度に添加すると、焼入れ後の硬度のばらつきを大
きくし、また、コスト上昇の要因ともなるので、上限を
0.500％に限定する。Mo: 0.012 to 0.500% Mo is an element that is added as necessary, because it additionally increases the corrosion resistance of stainless steel. To exert the effect of improving corrosion resistance, 0.012% or more must be added. However, if added excessively, the variation in hardness after quenching becomes large, and it also causes a cost increase.
Limited to 0.500%.
【００２２】Ｂ：0.0002〜0.0050％ Ｂは、粒界濃縮により粒界強度を強化し、ステンレス鋼
の加工性を付加的に高めるため、必要に応じて添加され
る元素である。加工性向上の効果を発揮させるには、0.
0002％以上の添加が必要である。しかし、過度に添加す
ると、Crとの共晶を形成し、熱間加工性に悪影響を及ぼ
すので、上限を0.0050％に限定する。B: 0.0002 to 0.0050% B is an element added as necessary to enhance the grain boundary strength by grain boundary concentration and additionally enhance the workability of stainless steel. To achieve the effect of improving workability, use 0.
It is necessary to add 0002% or more. However, if added excessively, it forms a eutectic with Cr and adversely affects hot workability, so the upper limit is limited to 0.0050%.
【００２３】Co：0.50％以下、Ｗ：0.30％以下 Co，Ｗは、結晶格子内の元素と置換されて、他元素の拡
散・移動を抑制し、耐酸化性を高める元素である。耐酸
化性が改善される詳細な機構については必ずしも明確で
はないが、高温酸化において形成され、耐酸化性を担っ
ているスピネル酸化物層(FeＯ・Cr2Ｏ3)外部へのCr元素
の離脱を抑制することによるものと思われる。このよう
な効果を発揮するためには、それぞれ0.01％以上の添加
が好ましい。しかし、過度に添加すると、逆に、地金内
部から酸化物層へのCrの供給を抑止する作用が大きくな
りすぎ、スピネル酸化物層が減衰してしまうので、上限
をCoは0.50％、Ｗは0.30％とする。Co: 0.50% or less, W: 0.30% or less Co and W are elements that are replaced by elements in the crystal lattice to suppress diffusion and movement of other elements and increase oxidation resistance. Although the detailed mechanism by which the oxidation resistance is improved is not always clear, the elimination of the Cr element to the outside of the spinel oxide layer (FeO.Cr 2 O 3 ) formed during high-temperature oxidation and responsible for the oxidation resistance It seems to be due to suppression. In order to exhibit such effects, it is preferable to add 0.01% or more of each. However, if added excessively, on the contrary, the effect of suppressing the supply of Cr from the inside of the base metal to the oxide layer becomes too large, and the spinel oxide layer is attenuated. Is set to 0.30%.
【００２４】Ca：0.0050％以下、Mg：0.0050％以下 Ca，Mgは、非金属介在物の形態と分布を制御して、切削
加工時の鋼の被削性を改善する。このような効果を発現
させるには、いずれも0.0002％以上含有させることが好
ましい。かかる効果が得られる理由は、必ずしも明確で
はないが、Ca，Mgの硫化物、珪酸塩、酸化物等が、工具
と母材の親和力を低下させるような形態で粒界に析出
し、溶着性構成刃先(工具刃先の近くで塑性変形を受け
て加工硬化した被削材の一部が、工具刃先に凝着し、二
次的に生成される新しい刃先)の成長を阻害することに
より、溶着性構成刃先脱落時の工具刃先のマイクロチッ
ピング(溶着性構成刃先が欠落する時に、同時に工具刃
先の先端が損傷を受ける現象)を抑止するからであると
思われる。しかし、Ca，Mgの量が、いずれも0.0050％を
超えると、Ca，Mgの硫化物、珪酸塩、酸化物を起点とし
た点錆が多発するため、耐食性維持の観点から、上限を
それぞれ0.0050％に限定する。Ca: 0.0050% or less, Mg: 0.0050% or less Ca and Mg improve the machinability of steel during cutting by controlling the form and distribution of nonmetallic inclusions. In order to exhibit such effects, it is preferable to contain 0.0002% or more. The reason why this effect is obtained is not clear, but sulfides, silicates and oxides of Ca and Mg precipitate at the grain boundaries in such a way as to reduce the affinity between the tool and the base material, and the weldability Welding by inhibiting the growth of the component cutting edge (a part of the work material that has undergone plastic deformation near the tool cutting edge and hardened due to work hardening adheres to the tool cutting edge and is created secondarily) This is because micro tipping of the tool edge when the component edge falls off (a phenomenon in which the tip of the tool edge is simultaneously damaged when the weldable component edge is missing) is suppressed. However, if the amounts of Ca and Mg both exceed 0.0050%, rusts originating from the sulfides, silicates and oxides of Ca and Mg occur frequently. Therefore, from the viewpoint of maintaining corrosion resistance, the upper limits are each 0.0050%. %.
【００２５】上述した以外の成分は、Feとそれに、不可
避的に含有される成分とする。なお、本発明において
は、不可避的に含有される成分のうち、Ｐ量は、耐食性
と加工性劣化防止の観点から、0.035％以下に抑制する
ことが望ましい。Ｓ量は、耐食性劣化防止の観点から、
0.020％以下に抑制することが望ましい。またＯ量は、
靱性および耐食性に対して有害であるので、0.010％以
下に抑制することが望ましい。また、希土類元素を硫化
物の形態制御による耐食性の向上の目的で添加すること
も可能である。The components other than those described above are Fe and components unavoidably contained therein. In the present invention, it is desirable that the P content of the components unavoidably contained be suppressed to 0.035% or less from the viewpoint of corrosion resistance and prevention of deterioration in workability. The amount of S is determined from the viewpoint of preventing corrosion resistance deterioration.
It is desirable to suppress it to 0.020% or less. The O amount is
Since it is harmful to toughness and corrosion resistance, it is desirable to suppress the content to 0.010% or less. It is also possible to add a rare earth element for the purpose of improving the corrosion resistance by controlling the form of the sulfide.
【００２６】本発明によるマルテンサイト系ステンレス
鋼は、成分調整した溶鋼を、転炉または電気炉等の溶製
炉にて溶製したのち、真空脱ガス法（ＲＨ法）、ＶＯＤ
法、ＡＯＤ法等の公知の精錬方法で精錬し、ついで連続
鋳造法あるいは造塊法でスラブ等に鋳造して、鋼素材と
するのが好適である。The martensitic stainless steel according to the present invention is prepared by melting molten steel whose components have been adjusted in a melting furnace such as a converter or an electric furnace, and then subjecting the steel to vacuum degassing (RH) and VOD.
It is preferable that the steel material is refined by a known refining method such as an AOD method, and then cast into a slab or the like by a continuous casting method or an ingot-making method.
【００２７】[0027]
【実施例】表１、表２に示す成分の鋼を溶製し、連続鋳
造法により、厚さ200mmのスラブとし、1150℃に加熱し
たのち、熱間圧延して板厚5mmの熱延鋼板に仕上げ、800
℃で焼鈍した。この鋼板より、焼き入れ後のロックウェ
ル硬度、耐食性（塩水噴霧）測定のための試験片（厚
さ：5mm、幅：50mm、長さ：50mm）、JIS Z 2202に準拠
したサブサイズシャルピー衝撃試験片（厚さ：10mm、
幅：5mm、長さ：55mm）を採取した。また、焼き入れ前
の打抜性（打ち抜き時のダレ）、曲げ加工性、被削性
（穴あけ性）、加熱時の耐酸化性などを調べるための試
験片も採取した。曲げ試験には、JIS Z 2204に準拠した
３号曲げ試験片（厚さ：5mm、幅：20mm、長さ：150m
m）、加熱時の耐酸化性試験には厚さ5mm×幅100mm×長
さ100mmの試験片、耐食性試験にはJIS Z 2371に準拠し
た塩水噴霧試験片（厚さ：5mm、幅：60mm、長さ：80m
m）を用いた。EXAMPLE A steel having the components shown in Tables 1 and 2 was melted, formed into a slab having a thickness of 200 mm by a continuous casting method, heated to 1150 ° C., and then hot-rolled to a hot-rolled steel sheet having a thickness of 5 mm. Finish, 800
Annealed at ℃. Specimens (thickness: 5mm, width: 50mm, length: 50mm) for measuring Rockwell hardness and corrosion resistance (salt spray) after quenching from this steel sheet, sub-size Charpy impact test in accordance with JIS Z 2202 Piece (thickness: 10mm,
(Width: 5 mm, length: 55 mm). In addition, test pieces for examining the punching property before quenching (sagging at the time of punching), bending workability, machinability (drillability), oxidation resistance during heating, and the like were also collected. For the bending test, use a No. 3 bending test piece (thickness: 5 mm, width: 20 mm, length: 150 m) in accordance with JIS Z 2204
m), 5 mm thick x 100 mm wide x 100 mm long test piece for oxidation resistance test during heating, salt spray test piece (thickness: 5 mm, width: 60 mm, JIS Z 2371) for corrosion resistance test Length: 80m
m) was used.
【００２８】[0028]
【表１】 [Table 1]
【００２９】[0029]
【表２】 [Table 2]
【００３０】打抜性、曲げ加工性、被削性、耐酸化性、
耐食性の各試験は、以下の方法で行った。 ・打抜性：熱延鋼板から150mmφ、50mmφの円板を打ち
抜き、側面から撮影した写真から、図１に示すダレ量を
測定した。 ・曲げ加工性：試験片を曲げ半径ｒ：2.5mmにて90°お
よび180°まで曲げ、割れがまったく発生しなかったも
のを○、0.5mm以下の割れに止まったものを△、0.5mmを
超える割れが発生したものを×として評価した。 ・被削性（穴あけ性）：ハイス製ドリル(φ12mm)によ
り、切削速度0.20m／sおよび0.35m／s、送り0.15mm／re
v、穴深さ20mm／回、切削油なしの条件で、繰り返し穴
あけを行い、１本のドリルで可能な積算穴あけ長さを測
定した。 ・耐酸化性：大気中で、850℃および1000℃の２水準で1
0時間加熱したときの、単位面積当たりの酸化増量を測
定した。 ・耐食性：JIS Z 2371に準拠し、４時間および12時間の
塩水噴霧試験を実施し、発銹の有無で評価した。発銹無
を○、発銹1〜4点有を△、実用上有害となる発銹5点以
上有を×とした。Punching property, bending workability, machinability, oxidation resistance,
Each test of corrosion resistance was performed by the following method. Punching property: 150 mmφ and 50 mmφ disks were punched from a hot-rolled steel sheet, and the sag amount shown in FIG. 1 was measured from a photograph taken from the side.・ Bending workability: The test piece was bent to 90 ° and 180 ° at a bending radius r of 2.5 mm, and 90% and 180 ° were obtained when no cracks were generated. Those having cracks exceeding the number were evaluated as x.・ Machinability (drillability): Cutting speed of 0.20m / s and 0.35m / s, feed rate of 0.15mm / re using high speed steel drill (φ12mm)
The drilling was repeated under the conditions of v, a hole depth of 20 mm / time, and no cutting oil, and the total drilling length possible with one drill was measured.・ Oxidation resistance: 1 at 2 levels of 850 ℃ and 1000 ℃ in air
The amount of increase in oxidation per unit area when heated for 0 hours was measured. -Corrosion resistance: In accordance with JIS Z 2371, a salt spray test was performed for 4 hours and 12 hours, and evaluated by the presence or absence of rust. The rusting was evaluated as ○, the rusting of 1 to 4 points was evaluated as Δ, and the rusting that was harmful for practical use was evaluated as ×.
【００３１】試験の結果を表３〜表８に示す。発明鋼は
いずれも、850℃以上の温度で焼入れすることにより、
比較鋼と同等以上の安定したロックウェル硬度を示し、
衝撃吸収エネルギーで表した靱性も、比較鋼と同等以上
であった。そして、発明鋼は、いずれもダレが少なく、
極めて良好な打抜性を有しており、また曲げ加工性も優
れていることがわかる。この曲げ加工性は、とくにＢ添
加により一層改善される。また、発明鋼は、大気中加熱
での酸化増量も少ない。さらに、発明鋼は、穴あけ性、
耐食性も良好であり、とくに、Moを添加した場合に優れ
た耐食性を示している。The test results are shown in Tables 3 to 8. By quenching all invention steels at a temperature of 850 ° C or higher,
Shows stable Rockwell hardness equal to or greater than comparative steel,
The toughness expressed by the impact absorption energy was also equal to or greater than that of the comparative steel. And invented steel has little dripping,
It can be seen that the material has extremely good punching properties and also has excellent bending workability. This bending workability is further improved especially by adding B. In addition, the invention steels also have a small increase in oxidation upon heating in the atmosphere. In addition, the invention steel has piercing properties,
The corrosion resistance is also good, and particularly when Mo is added, it shows excellent corrosion resistance.
【００３２】[0032]
【表３】 [Table 3]
【００３３】[0033]
【表４】 [Table 4]
【００３４】[0034]
【表５】 [Table 5]
【００３５】[0035]
【表６】 [Table 6]
【００３６】[0036]
【表７】 [Table 7]
【００３７】[0037]
【表８】 [Table 8]
【００３８】[0038]
【発明の効果】以上説明したように、本発明によれば、
所定の焼入れ硬度を安定して得られることに加えて、焼
き入れ前における、打ち抜き加工性、曲げ加工性などの
特性が改善されたマルテンサイト系ステンレス鋼を提供
することが可能になる。したがって、加工における製品
歩留りの向上、生産性の向上、製品コストの低減などに
大きく寄与することが期待できる。As described above, according to the present invention,
It is possible to provide a martensitic stainless steel with improved properties such as punching workability and bending workability before quenching, in addition to being able to stably obtain a predetermined quench hardness. Therefore, it can be expected to greatly contribute to improvement of the product yield in the processing, improvement of the productivity, reduction of the product cost, and the like.
【図１】打ち抜き加工時に発生したダレ量を説明するた
めの図である。FIG. 1 is a diagram for explaining the amount of sag generated during punching.
Claims (6)
i：0.5％以下、Mn：1.0〜2.5％、Cr：10.0超〜14.5％、
Al：0.100％以下を含み、かつＶ：0.40％以下、Ti：0.4
0％以下、Zr：0.40％以下、Ta：0.40％以下、Hf：0.40
％以下から選ばれる１種または２種以上を合計で0.02〜
0.40％含有し、残部はFeおよび不可避的不純物から成る
ことを特徴とする加工性に優れたマルテンサイト系ステ
ンレス鋼。[Claim 1] In mass%, C + N: more than 0.04 to 0.10%, S
i: 0.5% or less, Mn: 1.0 to 2.5%, Cr: more than 10.0 to 14.5%,
Al: 0.100% or less, V: 0.40% or less, Ti: 0.4
0% or less, Zr: 0.40% or less, Ta: 0.40% or less, Hf: 0.40
% Or more of one or more selected from 0.02% or less
A martensitic stainless steel with excellent workability characterized by containing 0.40% and the balance being Fe and unavoidable impurities.
量％で、Ni：0.6％以下、Cu：0.5％以下から選ばれる１
種または２種を含むことを特徴とする加工性に優れたマ
ルテンサイト系ステンレス鋼。2. In addition to the component according to claim 1, further selected from Ni: 0.6% or less and Cu: 0.5% or less by mass%.
A martensitic stainless steel excellent in workability, characterized by containing one or two kinds.
らに、質量％で、Mo：0.012〜0.500％を含むことを特徴
とする加工性に優れたマルテンサイト系ステンレス鋼。3. A martensitic stainless steel excellent in workability, characterized by further comprising Mo: 0.012 to 0.500% by mass in addition to the component according to claim 1 or 2.
分に加えさらに、質量％で、Ｂ：0.0002〜0.0050％を含
むことを特徴とする加工性に優れたマルテンサイト系ス
テンレス鋼。4. A martensitic stainless steel excellent in workability, characterized by further containing, by mass%, B: 0.0002 to 0.0050% in addition to the component according to any one of claims 1 to 3. .
分に加えさらに、質量％で、Co：0.50％以下、Ｗ：0.30
％以下から選ばれる１種または２種を含むことを特徴と
する加工性に優れたマルテンサイト系ステンレス鋼。5. The composition according to claim 1, further comprising, by mass%, Co: 0.50% or less, W: 0.30%.
% Martensitic stainless steel excellent in workability, characterized in that it contains one or two kinds selected from the group consisting of at most 1%.
分に加えさらに、質量％で、Ca：0.0050％以下、Mg：0.
0050％以下から選ばれる１種または２種を含むことを特
徴とする加工性に優れたマルテンサイト系ステンレス
鋼。6. The composition according to claim 1, further comprising, by mass%, 0.0050% or less of Ca, and 0.2% of Mg.
A martensitic stainless steel excellent in workability, characterized by containing one or two selected from 0050% or less.
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| WO2014148015A1 (en) * | 2013-03-19 | 2014-09-25 | Ｊｆｅスチール株式会社 | Stainless steel sheet |
| CN105452515A (en) * | 2013-06-25 | 2016-03-30 | 特纳瑞斯连接有限责任公司 | High-chromium heat-resistant steel |
| JP2017146187A (en) * | 2016-02-17 | 2017-08-24 | 学校法人大同学園 | Half-blanking processing test method |
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| CN107532259A (en) * | 2015-04-21 | 2018-01-02 | 杰富意钢铁株式会社 | Martensitic stain less steel |
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| JP4496659B2 (en) * | 2001-03-27 | 2010-07-07 | Ｊｆｅスチール株式会社 | Martensitic stainless steel with excellent punchability |
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