JPH0826404B2 - Method for producing high strength stainless steel with excellent overhang strength and toughness - Google Patents
Method for producing high strength stainless steel with excellent overhang strength and toughnessInfo
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- JPH0826404B2 JPH0826404B2 JP62153443A JP15344387A JPH0826404B2 JP H0826404 B2 JPH0826404 B2 JP H0826404B2 JP 62153443 A JP62153443 A JP 62153443A JP 15344387 A JP15344387 A JP 15344387A JP H0826404 B2 JPH0826404 B2 JP H0826404B2
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Description
【発明の詳細な説明】 〔産業上の利用分野〕 本発明は,180kg/mm2以上場合によっては200kg/mm2以
上の高強度を有しながら,優れた張り出し強度および勒
性を有し,割れ発生応力の高い高強力ステンレス鋼の製
造法に関する。本発明法によって得られるステンレス鋼
は,耐食性と共に高いばね特性の要求されるような板ば
ね,コイルばね,更には可及的薄くしても高強度を維持
することが必要な半導体ウエハーのスライス用のブレー
ド基板材などに好適に適用できるものである。DETAILED DESCRIPTION OF THE INVENTION [Industrial field of application] The present invention has a high strength of 180 kg / mm 2 or more, and in some cases, 200 kg / mm 2 or more, while having excellent overhang strength and chewing ability. The present invention relates to a method for producing high-strength stainless steel having high cracking stress. The stainless steel obtained by the method of the present invention is used for slicing semiconductor wafers that require corrosion resistance as well as high spring properties, and further high strength even if thinned as much as possible. It can be suitably applied to the blade substrate material and the like.
従来,ステンレス鋼をばね材に使用したり,ブレード
基板材に適用する場合には,マルテンサイト系ステンレ
ス鋼,加工硬化型オーステナイト系ステンレス鋼または
析出硬化型ステンレス鋼などが使用されてきた。Conventionally, when stainless steel is used as a spring material or a blade substrate material, martensitic stainless steel, work hardening austenitic stainless steel or precipitation hardening stainless steel has been used.
マルテンサイト系ステンレス鋼は,周知のように高温
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化させたもので,SUS410J1,420J2,
440A,Cなどの鋼種がこれにあたる。これらの鋼は焼き入
れ焼き戻しによりかなりの高強度と勒性が得られる。し
かし大きな板でかつ薄いものでは,熱処理により変形し
目的の形状のものを得ることは非常に困難である。As is well known, martensitic stainless steel is hardened by quenching from a high temperature austenite state and transforming it into martensite. SUS410J1, 420J2,
This includes steel grades such as 440A and C. Quenching and tempering of these steels gives them considerably higher strength and chewing properties. However, it is very difficult to obtain a desired shape by deforming by heat treatment if it is a large plate and is thin.
このため,そのような用途には加工硬化型オーステナ
イト系ステンレス鋼が使用されるのが通常である。この
鋼は冷間加工によりオーステナイト相とマルテンサイト
相の2相状態となるため,強度と延性に優れ,かつ耐食
性にも優れている。これらは,SUS301,SUS304などに代表
される。その強度は冷間加工量に依存するので,高強度
を得るためには冷間加工量を大きくする必要がある。こ
の場合延性が低下する。For this reason, work-hardening austenitic stainless steel is usually used for such applications. This steel has two phases, an austenite phase and a martensite phase, by cold working, so it has excellent strength and ductility, as well as excellent corrosion resistance. These are represented by SUS301 and SUS304. Since its strength depends on the cold working amount, it is necessary to increase the cold working amount in order to obtain high strength. In this case, ductility decreases.
析出硬化型ステンレス鋼は,析出硬化型元素を添加
し,時効処理により硬化させるものである。代表的なも
のには析出元素としてCuを添加したSUS630,Alを添加しS
US631があるが,前者は固溶化処理後時効処理により硬
化させたもので,強度は高々140kg/mm2である。一方,
後者は固溶化処理後準安定オーステナイト相を冷間加工
などの前処理で一部または全部をマルテンサイト相に変
態させその後時効処理することにより,Ni3Al金属間化
合物を析出させて硬化させるものでありかなり高強度の
ものが得られる。SUS631のオーステナイト相をマルテン
サイト相に変態させ,時効処理する方法としてはTH105
0,RH950,CH法などの周知の処理法がある。前2者の方法
により得られる強度は高々150kg/mm2であるが,CH処理で
は190kg/mm2程度のものが得られる。CH処理はまず前処
理として,加工硬化型オーステナイト系ステンレス鋼の
場合と同様に冷間加工を施してオーステナイト相とマル
テンサイト相の2相にし,その後時効処理を施すもので
ある。この時効処理により,マルテンサイト相にNi3Al
金属間化合物が析出して前述のような強度となる。Precipitation hardening type stainless steel is one in which precipitation hardening type elements are added and hardened by aging treatment. A typical example is SUS630 with Cu added as a precipitation element, and Al with S added.
There is US631, but the former is one that is hardened by solution treatment and aging treatment, and its strength is at most 140 kg / mm 2 . on the other hand,
The latter is one in which the metastable austenite phase after solution treatment is partially or wholly transformed into the martensite phase by pretreatment such as cold working and then aged to precipitate and harden the Ni 3 Al intermetallic compound. Therefore, a very high strength product can be obtained. TH105 is a method of aging treatment that transforms the austenite phase of SUS631 into the martensite phase.
There are well-known processing methods such as 0, RH950, CH method. The strength obtained by the former two methods is at most 150 kg / mm 2 , but with CH treatment about 190 kg / mm 2 can be obtained. As the CH treatment, first, as in the case of work-hardening austenitic stainless steel, cold working is performed to form two phases, an austenite phase and a martensite phase, and then an aging treatment. By this aging treatment, Ni 3 Al was added to the martensite phase.
The intermetallic compound precipitates and has the above-described strength.
例えばシリコン単結晶を切断してウエハーを製造する
ための切断刃は,板厚が0.05〜0.2mmのディスク基板の
内縁にダイヤモンド粉を被着させたInner diameter saw
blade(通称ID Saw Blade)が使用される。このブレー
ド基板は平坦度が良好であることはもとより,ウエハー
の切断ロスを出来るだけ少なくするために,厚みが薄く
且つ高強度のものでなければならない。そして切断機に
セットされる場合には強く張り出されるので十分な張り
出し強度(高い割れ発生応力)を有することが必要であ
る。つまり,高い強度と高い張り出し強度を有した勒性
に優れた材料であることが必要である。このような要求
を満足するには200kg/mm2級の抗張力を有しながら且つ
割れ発生応力の高い勒性の優れたステンレス鋼であるこ
と,そして精密な寸法と平坦度をもつ薄板に加工ができ
ることが望まれるが,従来のステンレス鋼ではこのよう
な過酷な要求を同時に満足することはできなかった。For example, a cutting blade for manufacturing a wafer by cutting a silicon single crystal is an inner diameter saw in which diamond powder is applied to the inner edge of a disk substrate having a thickness of 0.05 to 0.2 mm.
A blade (commonly called ID Saw Blade) is used. This blade substrate must have good flatness, and also must be thin and have high strength in order to reduce the cutting loss of the wafer as much as possible. When it is set in a cutting machine, it is strongly overhanged, so it is necessary to have sufficient overhanging strength (high cracking stress). In other words, it is necessary that the material has high strength and high overhang strength and is excellent in chewing ability. To meet these requirements, stainless steel with a tensile strength of 200 kg / mm 2 class, high cracking stress, and excellent ductility, and a thin plate with precise dimensions and flatness can be processed. Although it is desirable to be able to do so, conventional stainless steel was not able to simultaneously satisfy such severe requirements.
例えば,マルテンサイト系ステンレス鋼は焼き入れの
際に高温(950〜1100℃)に加熱され,冷却過程でマル
テンサイト変態も急激に生じるので,形状を損ないやす
い。これはプレスクェンチのような特殊熱処理によって
防止することが可能であるが費用がかかる。また薄板で
かつ広幅鋼帯での熱処理はほとんど不可能である。更
に,180kg/mm2前後の強度にすると張り出し加工はほどん
ど不可能となる。For example, martensitic stainless steel is heated to a high temperature (950 to 1100 ° C) during quenching, and the martensitic transformation rapidly occurs during the cooling process, so that the shape is easily damaged. This can be prevented by a special heat treatment such as press quench, but it is expensive. Further, heat treatment with a thin plate and a wide steel strip is almost impossible. Furthermore, when the strength is around 180 kg / mm 2 , overhanging becomes almost impossible.
オーステナイト系ステンレス鋼の場合は高強度を得る
ためには冷間加工量を大きくしなければならない。しか
し,冷間加工によって高強度にすると延性が著しく阻害
されてしまう。また,製品が鋼帯や大板の場合,高度な
冷間加工によってそり等が発生し形状も損なわれること
が多い。In the case of austenitic stainless steel, the amount of cold working must be increased to obtain high strength. However, if the strength is increased by cold working, ductility is significantly impaired. In addition, when the product is steel strip or large plate, the shape is often lost due to warpage due to advanced cold working.
析出硬化型ステンレス鋼の場合には,SUS630では十分
な高強度が得られない。SUS631は酸素や窒素との親和力
の大きいAlを0.75〜1.50%添加しているので製鋼時にア
ルミナ系の非金属介在物を形成したり,鋳造時にAlNの
凝集した介在物を形成し,製品の表面肌が荒れたり,勒
性や延性が阻害される場合が多々ある。また薄板では,
張り出し応力負荷時に介在物を起点に低応力で割れると
いう現象が生じる。また張り出し強度を必要とする部材
への使用は本質的に不利であった。そして析出硬化型ス
テンレス鋼は製品に加工後に熱処理を施すことにより本
来の特性が得られるのが一般的であるが,加工後に熱処
理を施すことにより形状がくずれたり,費用も嵩むとい
う問題があった。In the case of precipitation hardening stainless steel, SUS630 does not have sufficient high strength. Since SUS631 contains 0.75 to 1.50% of Al, which has a high affinity for oxygen and nitrogen, it forms alumina-based non-metallic inclusions during steelmaking, and aggregates of AlN during casting. In many cases, the skin becomes rough and the groininess and ductility are impaired. In the case of thin plates,
When an overhanging stress is applied, a phenomenon occurs that cracks occur at a low stress starting from inclusions. In addition, the use in a member that requires overhanging strength is essentially disadvantageous. In addition, precipitation-hardening type stainless steel generally obtains its original properties by subjecting the product to heat treatment after processing, but there was a problem that the shape was distorted and the cost increased due to heat treatment after processing. .
本発明は,マルテンサイト相誘発および強化元素であ
るSiを1.0%を越え3.0%以下と従来鋼より高くするとと
もに,マルテンサイト相の強化元素であるC,Nを合計で
0.10%以上にして,Siの添加により軽度の冷間加工で固
溶化後の準安定オーステナイト相からマルテンサイト相
が容易に誘発されるようにすると共に,その誘発された
マルテンサイト相がSi,C,Nにより硬くされて,冷間加工
で形状,強度,延性に富んだ製品が得られるようにし,
そして析出硬化元素としては,時効硬化に対してSiと相
互作用を有し介在物の心配のないCuを添加して,時効処
理を追加することにより一層高強度を発現したものであ
る。また張り出し加工における加工高さあるいは張り出
し強度が,時効処理前の冷間加工量およびマルテンサイ
ト量に影響されることを知見し,冷間加工量と加工によ
って生ずるマルテンサイト量をバランスさせると共に,
内在する非金属介在物を最少限にとどめることにより,
従来鋼では困難であった高強度でかつ張り出し性のすぐ
れたステンレス鋼を得たものである。しかもこの場合,
時効処理は従来鋼のごとく長時間の時効処理を施すこと
なく短時間処理で高強度が得られる。この短時間時効で
よいことは鋼帯ままで連続時効処理ができることを意味
する。In the present invention, the content of Si, which is a martensite phase inducing and strengthening element, is higher than that of the conventional steel, which is more than 1.0% and 3.0% or less, and the total content of C and N, which are the strengthening elements of the martensite phase, is increased.
With the content of 0.10% or more, the addition of Si makes it easy to induce the martensite phase from the metastable austenite phase after solid solution by mild cold working, and the induced martensite phase is Si, C , N hardened by cold working so that products with excellent shape, strength and ductility can be obtained by cold working.
As a precipitation hardening element, Cu, which has an interaction with Si and has no fear of inclusions, is added to the age hardening, and the aging treatment is added to achieve higher strength. It was also found that the working height or overhanging strength in the overhanging process is affected by the cold working amount and martensite amount before aging treatment, and the cold working amount and the martensite amount generated by working are balanced, and
By minimizing the internal non-metallic inclusions,
It is a high-strength stainless steel with excellent bulging properties, which was difficult with conventional steel. And in this case,
As for aging treatment, high strength can be obtained by short-time treatment without performing long-term aging treatment as in conventional steel. The fact that this short-time aging is sufficient means that continuous aging treatment can be performed with the steel strip as it is.
すなわち本発明は,重量%において,C:0.10%以下,S
i:1.0%を越え3.0%以下,Mn:2.5%以下,Ni:4.0〜8.0%,
Cr:12.0〜18.0%,Cu:1.0〜3.5%,N:0.15%以下,S:0.008
%以下,CとNの合計が0.10%以上,必要に応じて,Moま
たはWの少なくとも一種を2.0%以下の量で更に含有せ
しめ,残部がFeおよび不可避的に混入してくる不純物よ
りなり,溶体化処理状態でオーステナイト組織を呈する
オーステナイト系ステンレス鋼を,溶体化処理後におい
て,40〜80容量%の加工誘起マルテンサイト量が生成す
るに十分な冷間加工率で冷間加工し,次いで,400〜600
℃で0.3〜5分の時効処理することからなる張り出し強
度および勒性に優れ且つ180kg/mm2以上,場合によって
は200kg/mm2以上の高強度を有するステンレス鋼の製造
方法を提供するものである。前記の鋼の化学成分範囲に
おいて,一層好ましくは,Si:2.0〜3.0%,Ni:5.0〜7.0
%,Cu:1.5〜2.5%,N:0.04〜0.1%以下,,Mn:0.5%未満,
S:0.004%以下とする。That is, in the present invention, in% by weight, C: 0.10% or less, S
i: 1.0% to 3.0% or less, Mn: 2.5% or less, Ni: 4.0 to 8.0%,
Cr: 12.0 to 18.0%, Cu: 1.0 to 3.5%, N: 0.15% or less, S: 0.008
% Or less, the sum of C and N is 0.10% or more, and if necessary, at least one of Mo and W is further contained in an amount of 2.0% or less, and the balance is Fe and impurities inevitably mixed, After the solution treatment, the austenitic stainless steel exhibiting an austenitic structure in the solution-treated state is cold-worked at a cold-working rate sufficient to generate a work-induced martensite amount of 40 to 80% by volume, and then, 400-600
The present invention provides a method for producing a stainless steel having excellent overhanging strength and toughness by aging treatment for 0.3 to 5 minutes at ℃ and having a high strength of 180 kg / mm 2 or more, and in some cases 200 kg / mm 2 or more. is there. Within the above chemical composition range of steel, more preferably Si: 2.0-3.0%, Ni: 5.0-7.0
%, Cu: 1.5 to 2.5%, N: 0.04 to 0.1% or less, Mn: less than 0.5%,
S: 0.004% or less.
本発明鋼は,前記の範囲の組成を採用し,溶体化処理
状態でオーステナイト相とし,これを冷間加工状態で実
質的に40〜80%のマルテンサイト組織として,従来の加
工硬化型オーステナイト系ステンレス鋼や析出硬化型ス
テンレス鋼よりも,強度,延性に優れしかも短時間の時
効処理で高強度が得られかつ張り出し強度の高いステン
レス鋼を得たものである。また,窒化物等の介在物を生
成する強化元素を使用しないことにより,さらに表面肌
の面でも勝るようにしたものである。本発明鋼は固溶化
状態で準安定オーステナイト相を呈するように成分調整
してあるので,製造に特別の条件を必要とせず,溶体化
処理までの工程は従来の加工硬化型オーステナイト系ス
テンレス鋼や析出硬化型ステンレス鋼と同要領で製造す
ることができる。The steel according to the present invention adopts the composition within the above range, has an austenite phase in the solution heat treatment state, and has a martensite structure of substantially 40 to 80% in the cold work state, and has a conventional work hardening type austenite system. This is a stainless steel that is superior in strength and ductility to stainless steel and precipitation hardening type stainless steel, and that high strength can be obtained by aging treatment for a short time and high bulging strength. In addition, by not using a strengthening element that generates inclusions such as nitrides, the surface texture is further improved. Since the composition of the steel of the present invention is adjusted so that it exhibits a metastable austenite phase in a solid solution state, no special conditions are required for production, and the steps up to the solution treatment are the same as those of conventional work hardening type austenitic stainless steels. It can be manufactured in the same manner as precipitation hardening stainless steel.
以下に,先ず本発明鋼の成分範囲の限定理由の概要を
説明する。First, the outline of the reason for limiting the composition range of the steel of the present invention will be described below.
Cはオーステナイト生成元素で,高温で生成するδフ
ェライトの抑制,冷間加工で誘発されたマルテンサイト
相の強化に極めて有効であるが,本発明鋼ではSiが高い
ため,Cの固溶限が低下されてしまっている。このため,C
を高くすると,粒界に炭化物が析出し,耐粒界腐食や延
性低下の原因となるので,Cは0.1%以下とした。C is an austenite forming element and is extremely effective in suppressing δ ferrite generated at high temperature and strengthening the martensite phase induced by cold working. However, since the steel of the present invention has high Si, the solid solution limit of C is It has been lowered. Therefore, C
If the value is increased, carbide precipitates at the grain boundaries, causing intergranular corrosion resistance and reduced ductility, so C was made 0.1% or less.
Mnはオーステナイト相の安定度を支配する元素であ
り,その活用は他の元素とのバランスのもとに考慮され
る。本発明においては2.5%までのMn量でその活用が図
れる。ただ,本発明鋼ではMnがあまり高いと延性を低下
させる。したがって,特に延性を重視する場合には,Mn
量は0.5%未満とするのが好ましい。Mn is an element that controls the stability of the austenite phase, and its utilization is considered in balance with other elements. In the present invention, the utilization can be achieved with the Mn amount up to 2.5%. However, in the steel of the present invention, if Mn is too high, the ductility decreases. Therefore, when importance is attached to ductility, Mn
Preferably the amount is less than 0.5%.
Niは高温および室温でオーステナイト相を得るために
必須の成分であるが,本発明鋼の場合,室温で準安定オ
ーステナイト相にして冷間加工でマルテンサイト相を誘
発させるようにしなければならない。本発明鋼ではNiを
4.0%より低くすると高温で多量のδフェライト相が生
成し且つ室温でオーステナイト相が準安定状態になり難
くなる。また8.0%を越えると冷間加工でマルテンサイ
ト相が誘発され難くなる。このため,Ni量は4.0〜8.0%
とするが,より好ましくは,5.0〜7.0%とする。Ni is an essential component for obtaining an austenite phase at high temperature and room temperature, but in the case of the steel of the present invention, it must be made a metastable austenite phase at room temperature to induce the martensite phase in cold working. In the present invention steel, Ni
If it is lower than 4.0%, a large amount of δ ferrite phase is generated at high temperature and the austenite phase is hard to become metastable at room temperature. On the other hand, if it exceeds 8.0%, it becomes difficult to induce the martensite phase during cold working. Therefore, the Ni content is 4.0 to 8.0%.
However, it is more preferably 5.0 to 7.0%.
Crは耐食性上必須の成分である。意図する耐食性を賦
与するのには少なくとも12.0%のCrを必要とする。しか
し,Crはフェライト生成元素でもあるので,高くしすぎ
ると高温でδフェライト相が多量に生成してしまう。そ
こでδフェライト相抑制のためにオーステナイト生成元
素(C,N,Ni,Mn,Cuなど)をそれに見合った量で添加しな
ければならなくなるが,オーステナイト生成元素を多く
添加すると今度は室温でのオーステナイト相が安定して
しまって,準安定オーステナイト相にならず,冷間加工
後,時効処理しても高強度が得られなくなる。このよう
なことからCrの上限は18.0%とした。Cr is an essential component for corrosion resistance. At least 12.0% Cr is required to provide the intended corrosion resistance. However, Cr is also a ferrite forming element, so if it is made too high, a large amount of δ ferrite phase will be formed at high temperatures. Therefore, in order to suppress the δ ferrite phase, it is necessary to add austenite-forming elements (C, N, Ni, Mn, Cu, etc.) in an amount commensurate with that. However, if a large amount of austenite-forming elements is added, then austenite at room temperature The phase becomes stable and does not become a metastable austenite phase, and high strength cannot be obtained even after aging treatment after cold working. For this reason, the upper limit of Cr is set to 18.0%.
Cuは時効処理の際,前述のごとくSiとの相互作用によ
り硬化させるものであるが,少なすぎると,その効果は
小さく,多すぎると,割れの原因となる。このため1.0
〜3.5%とした。Cu is hardened by the interaction with Si as described above during the aging treatment, but if it is too small, its effect is small, and if it is too large, it causes cracking. For this reason 1.0
~ 3.5%.
Siは,冷間加工によるマルテンサイト相の誘発および
強化する上で重要な元素であると共に,時効処理による
硬化のうえでもCuと合わせて重要である。その効果を発
揮させるためには少なくとも1.0%以上を必要とする。
しかし,あまり高くするとδフエライト相の生成を助長
すると共に添加量の割りにはその効果が小さいのでその
上限を3.0%とした。Si is an important element for inducing and strengthening the martensite phase by cold working, and together with Cu for hardening by aging treatment. In order to exert its effect, at least 1.0% or more is required.
However, if it is made too high, the formation of the δ-ferrite phase is promoted and its effect is small relative to the amount added, so the upper limit was made 3.0%.
なお,時効処理後の強度は,特にマルテンサイト量お
よびSi量とCu量に支配され,これらをバランスさせる必
要がある。特に高強度を得るためには,Si量を2.0%以上
3.0%以下,Cu量を1.5%以上2.5%以下とするのがよい。The strength after aging treatment is dominated by the amount of martensite and the amount of Si and Cu, and these must be balanced. To obtain particularly high strength, the Si content should be 2.0% or more.
3.0% or less, and the amount of Cu should be 1.5% or more and 2.5% or less.
Nはオーステナイト生成元素であると共に,オーステ
ナイト相およびマルテンサイト相を硬化させるのに極め
て有効な元素でもあるが,多量になると鋳造時にブロー
ホールの原因となるので0.15%以下とした。N is an element that forms austenite and is also an element that is extremely effective in hardening the austenite phase and martensite phase. However, if a large amount of N causes blowholes during casting, it was set to 0.15% or less.
SはMnと共存のもとにMnSを生成し,延性の低下をた
らすので,0.008%以下とした。なお,特に薄板で介在物
が延性,張り出し強度に影響する領域では,MnおよびS
は低い方が好ましく,Mn量は0.5%未満,S量は0.004%以
下が適当である。S forms MnS in the presence of Mn and causes a decrease in ductility, so S was made 0.008% or less. In particular, in the area where inclusions affect ductility and overhang strength in thin plates, Mn and S
Is preferably low, the Mn content is less than 0.5%, and the S content is 0.004% or less.
MoとWは鋼のベース硬さを上昇させるとともに時効処
理後の硬さを上昇させ短時間時効で高強度を得る上で有
効に作用する。しかし,いずれもフェライトフォーマー
であるために多量に添加するとδフェライト相を晶出さ
せ,かえって強度低下の要因ともなるので上限を2.0%
までとした。Mo and W effectively increase the base hardness of the steel and also increase the hardness after aging treatment to obtain high strength with short-time aging. However, all of them are ferrite formers, so if added in a large amount, they will crystallize the δ ferrite phase and rather cause a decrease in strength. Therefore, the upper limit is 2.0%.
Up to
なおCとNとは同様な作用効果を示し,互換性があ
り,上限はそれぞれ上記のように限定したが本発明で意
図する作用効果を十分に発揮させるには合計量で0.10%
以上とする必要がある。Note that C and N show similar effects and are compatible with each other, and the upper limits are limited respectively as described above, but in order to fully exert the effects intended by the present invention, the total amount is 0.10%.
It is necessary to do above.
なお,本発明の製造法に用いられる鋼には前述の成分
以外に脱酸材として添加されるAlやTi,脱硫剤として添
加されるCaやREM,熱間加工性改善効果のあるB(0.01%
以下)の他,不可避的に混入する不純物を含有すること
が出来る。In the steel used in the production method of the present invention, in addition to the above-mentioned components, Al and Ti added as deoxidizing agents, Ca and REM added as desulfurizing agents, and B (0.01 with an effect of improving hot workability). %
In addition to the following), impurities that are inevitably mixed can be contained.
以上の範囲に各化学成分値を調整した本発明に従う鋼
はその組織状態が溶体化処理状態でオーステナイト組織
を呈する。そして,このオーステナイト組織は準安定な
組織であり,冷間加工によってマルテンサイト相を誘起
する。本発明においては,溶体化処理を行ってオーステ
ナイト組織としたあと,70%以下の加工率(圧延率)で
冷間加工(冷間圧延)し,その際に生成する加工誘起マ
ルテンサイト量を40〜80%の範囲とする。そして,400〜
600℃で0.3〜5分の範囲の短時間の時効処理を施す。後
記の実施例で実証するように,この冷間加工と短時間の
時効処理によって,目的とする高い張り出し強度をもつ
勒性に優れた高力ステンレス鋼を得ることができる。The steel according to the present invention, in which the chemical composition values are adjusted within the above ranges, exhibits an austenitic structure in the solution treatment state. And this austenite structure is a metastable structure and induces a martensite phase by cold working. In the present invention, after solution treatment to form an austenite structure, cold working (cold rolling) is performed at a working rate (rolling rate) of 70% or less, and the amount of work-induced martensite produced at that time is 40%. The range is up to 80%. And 400 ~
Aging treatment is performed at 600 ° C for a short time in the range of 0.3 to 5 minutes. As will be demonstrated in the examples described below, this cold working and short-term aging treatment makes it possible to obtain the desired high-strength stainless steel with high overhang strength and excellent in chewing property.
例えば,IDブレード基板等の型ぬき(中央に円形の開
口をもつ円形デイスクの型ぬき)を行うには,鋼帯コイ
ルからエッチング法で行うことが通常である。このエッ
チング法による型ぬきは作業工程中に150℃〜250℃前
後,材料温度が上昇する。このため冷間加工を施して強
化したものはこの温度上昇により寸法変化をきたすこと
になりこのためエッチング法による型ぬき作業前に時効
処理を施しておくことが必要である。しかし,従来鋼SU
S301では時効による時効硬化度(ΔHv)が低いので(後
記実施例1の第2表に示すように特に短時間時効ではΔ
Hが低いので),高強度を得るためには高い圧延率と長
時間の時効処理を必要とした。このようなことから、従
来鋼SUS301ではコイルから切板した単板で長時間時効し
たあと,IDブレード基板材として加工されるのが常法で
あった。単板による長時間の時効は周知のように作業も
大変であるし費用も嵩む。For example, in order to perform die-cutting of an ID blade substrate or the like (die-cutting of a circular disk having a circular opening in the center), it is usual to perform etching from a steel strip coil. The material temperature rises around 150 to 250 ° C during the working process of die removal by this etching method. For this reason, those which have been strengthened by cold working will undergo dimensional changes due to this temperature rise, and therefore it is necessary to perform an aging treatment before the die cutting work by the etching method. However, conventional steel SU
Since S301 has a low age hardening (ΔHv) due to aging (as shown in Table 2 of Example 1 to be described later, particularly in the case of short-time aging,
Since H is low), high rolling ratio and long-term aging treatment were required to obtain high strength. For this reason, in the conventional steel SUS301, it has been a usual method to process a single plate cut from a coil as an ID blade substrate material after aging for a long time. As is well known, long-term aging with a single plate is difficult and costly.
しかるに本発明によれば,短時間の時効処理でも高い
時効硬化度(ΔHv)が得られるので,この時効処理を連
続処理(アンコイラーからコイラーへの鋼帯の連続流れ
の途中に熱処理帯を設けた鋼帯の連続熱処理)で実施し
ても,十分な強度を得ることが出来る。そして,得られ
た時効処理後の鋼帯からIDブレード基板材を型抜するこ
とができる。本発明による場合には従来鋼では困難であ
った張り出し強度,勒性の高いしかも高強度のステンレ
ス鋼板を製造でき,また寸法精度や平坦度においても従
来の場合に比べて非常に良好なIDブレード基板を経済的
に得ることができる。However, according to the present invention, a high age-hardening degree (ΔHv) can be obtained even with a short time aging treatment. Therefore, this aging treatment is a continuous treatment (a heat treatment zone is provided in the middle of the continuous flow of the steel strip from the uncoiler to the coiler). Sufficient strength can be obtained even if it is carried out by continuous heat treatment of steel strip). Then, the ID blade substrate material can be die-cut from the obtained steel strip after the aging treatment. According to the present invention, it is possible to manufacture a stainless steel plate having a high overhanging strength and a high bending strength, which is difficult with the conventional steel, and has a very good dimensional accuracy and flatness as compared with the conventional case. The substrate can be obtained economically.
また,IDブレードは切断装置に装着して張り上げるさ
いに,チャック部で高い張り出し応力を受ける。この張
り上げ時に張り出し部が破断しないためには高い張り出
し応力を必要とする。本発明に従って得られた鋼は,後
記の実施例で実証するように大きな張り出し応力を加え
ても割れず,エリクセン試験による割れ発生応力がSが
低いものでは140kg/mm2以上を示す。一般に高強度材料
では張り出し応力は表面欠陥の影響を受けやすく表面欠
陥のない鋼板であることが必要である。本発明鋼では表
面性状が良好となるような鋼成分に規制するものではあ
るが,溶体化処理(焼鈍)後の酸洗等によって表面肌荒
れなどが不可避的に生ずることもある。このような肌荒
れが生じた鋼帯を冷間圧延した場合には,張り出し加工
時に割れの起点となる欠陥を生ずることがある。したが
って,本発明の製造法において,加工誘起マルテンサイ
トを生成させる冷間圧延前に,その鋼の表面を研磨する
処理を施すのが好ましい。この研磨処理は通常の研磨紙
やバフ研磨処理を行えばよい。Moreover, when the ID blade is attached to the cutting device and pulled up, a high overhanging stress is applied to the chuck. A high overhang stress is required so that the overhang part does not break during this uplift. The steel obtained according to the present invention does not crack even if a large overhanging stress is applied as will be demonstrated in the examples described later, and the crack initiation stress by Erichsen test is 140 kg / mm 2 or more. Generally, in high strength materials, the bulging stress is susceptible to surface defects, and it is necessary that the steel plate has no surface defects. In the steel of the present invention, the steel components are regulated so that the surface properties are good, but surface roughening and the like may inevitably occur due to pickling after solution treatment (annealing). When a steel strip having such a rough surface is cold-rolled, a defect that causes a crack may occur during the overhanging process. Therefore, in the production method of the present invention, it is preferable to perform a treatment of polishing the surface of the steel before cold rolling to generate the work-induced martensite. This polishing treatment may be performed by using ordinary polishing paper or buffing treatment.
したがって,本発明はまた,IDブレード基板のように
高い張り出し強度を必要とする用途向きの高強度且つ高
勒性のステンレス鋼帯の製造法として,重量%におい
て,C:0.10%以下,Si:1.0%を越え3.0%以下,Mn:2.5%以
下,Ni:4.0〜8.0%,Cr:12.0〜18.0%,Cu:1.0〜3.5%,N:
0.15%以下,S:0.008%以下,CとNの合計が0.10%以上,
必要に応じて,MoまたはWの少なくとも一種を2.0%以下
の量で更に含有せしめ,残部がFeおよび不可避的に混入
してくる不純物よりなるオーステナイト組織を有するス
テンレス鋼帯を,表面研磨処理のあと40〜80容量%の加
工誘起マルテンサイト量が生成するに十分な冷間圧延率
で冷間圧延し,次いで得られた冷延鋼帯を熱処理炉に連
続的に通板して400〜600℃の温度で0.3〜5分の連続時
効処理を施すことからなる高い張り出し強度と勒性を有
する高強度ステンレス鋼帯の製造法を提供するものであ
る。本方法によると,従来の切り板材の時効処理のごと
く真空中あるいは不活性ガス中での長時間時効と異なり
安価な時効処理品が提供出来る。またエッチング法によ
る型ぬき等のように熱が加わることによる変形等も心配
のないものがコイル状で提供でき,生産性の向上を図る
ことができる。しかも張り出し強度,勒性に優れている
ためIDブレード等張り出し応力が負荷されるような用途
ではさらにその効果が現われる。Therefore, the present invention is also a method for producing a high-strength and high-strength stainless steel strip for an application such as an ID blade substrate that requires a high overhanging strength. More than 1.0% and 3.0% or less, Mn: 2.5% or less, Ni: 4.0 to 8.0%, Cr: 12.0 to 18.0%, Cu: 1.0 to 3.5%, N:
0.15% or less, S: 0.008% or less, the sum of C and N is 0.10% or more,
If necessary, at least one type of Mo or W is further contained in an amount of 2.0% or less, and the stainless steel strip having an austenite structure composed of Fe and the unavoidably mixed impurities is used after surface polishing treatment. Cold rolling was carried out at a cold rolling rate sufficient to generate a work-induced martensite content of 40 to 80% by volume, and then the cold-rolled steel strip obtained was continuously threaded through a heat treatment furnace at 400 to 600 ° C. The present invention provides a method for producing a high-strength stainless steel strip having high overhanging strength and chewing ability, which comprises performing continuous aging treatment for 0.3 to 5 minutes at the above temperature. According to this method, unlike the conventional aging treatment for cut plate materials, unlike the long-term aging in vacuum or in an inert gas, an inexpensive aging-treated product can be provided. In addition, it is possible to provide a coil-shaped product that does not cause deformation due to heat, such as die-cutting by an etching method, so that productivity can be improved. Moreover, since it has excellent overhanging strength and flexibility, its effect is further exhibited in applications such as ID blades where overhanging stress is applied.
以下に実施例によって本発明の効果を具体的に示す。 The effects of the present invention will be specifically described below with reference to examples.
第1表に示す成分の本発明鋼(S1〜S8),従来鋼(A,
B)および比較鋼(a〜c)を常法により熱間圧延を施
した後,冷延,焼鈍(溶体化処理),酸洗を行った材料
を第2表に示す圧延率で冷間圧延した。得られた冷延鋼
板の冷間圧延により誘発されたマルテンサイト量(α′
量)を測定し,また各鋼板の硬さ,引張強さおよび伸び
を調べた。その結果を第2表に示した。また,各冷延鋼
板を530℃×1分の短時間の時効処理し,時効後の硬
さ,引張強さ,伸びエリクセン試験による割れ発生応力
(割れ発生荷重を板厚およびポンチ径で割った値)を調
べ,その結果を第2表に併記した。なお,第2表中のΔ
Hvは時効前後の硬さの差である。Inventive steels (S1 to S8) and conventional steels (A,
B) and comparative steels (a to c) were hot-rolled by a conventional method, and then cold-rolled, annealed (solution treatment) and pickled, and cold-rolled at the rolling ratios shown in Table 2. did. The amount of martensite (α 'induced by cold rolling of the obtained cold rolled steel sheet
The amount) was measured, and the hardness, tensile strength and elongation of each steel sheet were examined. The results are shown in Table 2. In addition, each cold-rolled steel sheet was aged at 530 ° C for a short time of 1 minute, and hardness, tensile strength, and elongation after aging Cracking stress by Erichsen test (cracking load was divided by sheet thickness and punch diameter The value) was investigated and the results are also shown in Table 2. In addition, Δ in Table 2
Hv is the difference in hardness before and after aging.
また,第1図に,前記の鋼についてのマルテンサイト
量とエリクセン試験による割れ発生応力の関係(●
印),マルテンサイト量と切欠引張強さ(JIS13B号引張
片の平行部中央に両サイドから幅180μ,深さ1.5mmの切
欠を挿入した切欠引張片による切欠引張強さ)試験結果
との関係を示す。第1図において, は切欠引張強さ/引張強さの比を,○印は引張強さを示
す。また丸印で表示したものは本発明鋼,四角印のもの
は比較鋼である。In addition, Fig. 1 shows the relationship between the amount of martensite and the crack initiation stress in the Erichsen test for the above steels (●
Mark), martensite amount and notch tensile strength (notch tensile strength by notch tensile pieces with notches with width 180μ and depth 1.5mm inserted from both sides in the center of parallel part of JIS 13B tensile pieces) test results Indicates. In Figure 1, Indicates the notch tensile strength / tensile strength ratio, and ○ indicates tensile strength. Further, those marked with circles are the present invention steels, and those marked with squares are comparative steels.
第2表および第1図の結果から次のことがわかる。 The following can be seen from the results shown in Table 2 and FIG.
本発明に従う短時間時効処理後の鋼S1〜S8(冷間圧延
30〜70%,マルテンサイト量40〜80%,時効処理530℃
×1分の本発明の製造条件の範囲にある鋼)は,エリク
セン試験による割れ発生応力は,Sが0.007%と高いS2鋼
およびマルテンサイト量が本発明で規定する上限(80
%)に近い76%のS6鋼を除いて,全て140kg/mm2以上と
高い値を示し,従来鋼および比較鋼に比べ,張り出し応
力を受けたさいに高い割れ抵抗を示す。そして,強度レ
ベルはほぼ190〜205kg/mm2の範囲にある。Steels S1 to S8 after cold aging according to the invention (cold rolling
30-70%, martensite amount 40-80%, aging treatment 530 ℃
The steel with the production condition range of the present invention of x 1 minute) has a crack initiation stress in the Erichsen test with an upper limit of 80% for S2 steel with a high S of 0.007% and martensite content (80%).
%), Except for S6 steel, which is close to 76%, and shows a high value of 140 kg / mm 2 or more, and shows higher crack resistance when subjected to overhanging stress than conventional steel and comparative steel. The strength level is approximately 190-205 kg / mm 2 .
従来鋼AのSUS301では本発明と同一強度レベルを得よ
うとすれば,短時間時効でのΔHv(時効後硬さ−時効前
硬さ)が小さいので,時効前に高い冷間圧延を加えて高
強度としておく必要がある。さらにMnおよびSが高いた
め時効処理後の延性も低く,張り出し加工時に低い応力
で割れが発生する。Conventional steel A, SUS301, has a small ΔHv (hardness after aging-hardness before aging) in short-time aging if the same strength level as that of the present invention is to be obtained. Therefore, if high cold rolling is added before aging, It is necessary to keep high strength. Furthermore, since Mn and S are high, the ductility after aging treatment is also low, and cracks occur at low stress during overhang processing.
また,従来鋼BのSUS631でも割れ発生応力が本発明鋼
より低い。これは析出強化元素としてAlを多量に使用す
るため,Alの窒化物等の非金属介在物が多量に存在し,
薄板で高強度とした場合に,張り出し加工時それを起点
に割れを発生しやすくなるからである。In addition, even in the case of SUS631 of conventional steel B, the stress of cracking is lower than that of the steel of the present invention. Since a large amount of Al is used as a precipitation strengthening element, there are a large amount of non-metallic inclusions such as Al nitrides.
This is because when a thin plate with high strength is used, cracks tend to occur starting from it during overhang processing.
比較鋼Cでは時効前のマルテンサイト量が多いため勒
性が低く割れが発生しやすい。In Comparative Steel C, since the amount of martensite before aging is large, the ductility is low and cracking easily occurs.
また,第1図に見られるように,マルテンサイト量が
80%を超えると,たとえ引張強さが190〜205kg/mm2の範
囲にあっても,割れ発生応力および切欠引張強さ/引張
強さが急激に低下し,鋼の化学成分値が本発明で規定す
る範囲にあっても加工誘起マルテンサイト量は80%以下
としなければ良好な張り出し強度が達成できない。Also, as seen in Fig. 1, the amount of martensite is
If it exceeds 80%, even if the tensile strength is in the range of 190 to 205 kg / mm 2 , the crack initiation stress and the notch tensile strength / tensile strength sharply decrease, and the chemical composition value of steel is Even if it is within the range specified in, good overhang strength cannot be achieved unless the amount of work-induced martensite is 80% or less.
このため本発明による製造法ではマルテンサイト量が
80%以下となるように冷間圧延率と圧延温度を調整する
ことが必要であり,またあまりマルテンサイト量が低い
と十分な強度が得られないためその下限を40%とするの
がよい。Therefore, in the production method according to the present invention, the amount of martensite is
It is necessary to adjust the cold rolling rate and rolling temperature so that it is 80% or less, and if the amount of martensite is too low, sufficient strength cannot be obtained, so the lower limit should be 40%.
第2図は,第1表の本発明鋼S4について,溶体化処理
後の冷間圧延率を種々変化させて冷間圧延し,次いで53
0℃×1分間の短時間時効処理を施した場合の,該冷間
圧延率と引張強さ,切欠引張強さ,エリクセン試験によ
る割れ発生応力との関係を示したものである。なお,冷
間圧延は強度レベルを195kg/mm2前後とするために,冷
間圧延率が高いもの程高い温度で実施した(15℃〜170
℃の範囲)。各冷間圧延温度を割れ発生応力の値を示す
△印のデータの脇に表示した。FIG. 2 shows that the invention steel S4 in Table 1 was cold-rolled by variously changing the cold-rolling rate after solution treatment, and then 53
It shows the relationship between the cold rolling ratio and the tensile strength, the notch tensile strength, and the crack generation stress by the Erichsen test when a short-time aging treatment at 0 ° C for 1 minute is performed. The cold rolling was performed at a higher temperature as the cold rolling rate increased (15 ° C to 170 ° C) in order to set the strength level to around 195 kg / mm 2.
C range). Each cold rolling temperature is displayed beside the data marked with Δ, which indicates the value of stress generated by cracking.
第2図から明らかなように,強度レベル(○印)がほ
ぼ一定でも,冷間圧延率が70%を越えると切欠勒性およ
び割れ発生応力が低下し始める。このため,本発明によ
る製造法では圧延率は70%以下とするのがよい。しかし
あまり圧延率が低いと強度が得られないので,その下限
は30%とするのがよい。As is clear from Fig. 2, even when the strength level (marked with "○") is almost constant, the notch fracturing property and crack initiation stress start to decrease when the cold rolling ratio exceeds 70%. Therefore, in the manufacturing method according to the present invention, the rolling rate is preferably 70% or less. However, if the rolling ratio is too low, strength cannot be obtained, so the lower limit should be 30%.
第3図は,第2表の結果のうち,530℃×1分の短時間
時効を施した場合の時効前後の時効硬化度ΔHvとマルテ
ンサイト量との関係を示したものである。第3図より,
本発明の鋼(○印S1〜8)は,マルテンサイト量の増加
とともΔHvは高くなり,時効硬化度がマルテンサイト量
の影響を受けることが認められる。一方,成分範囲外の
比較鋼aおよび従来鋼SUS301ではΔHvは小さく本発明の
目的を達成しがたい。本発明法では短時間の時効処理で
十分な時効硬化度が得られるから,この時効処理を鋼帯
を熱処理炉に連続的に通板する連続処理で実施すること
ができる。これに対しSUS301では時効による時効硬化度
(ΔHv)低いため,特に短時間時効では低いため,高強
度を得るためには高い圧延率と長時間の時効処理を必要
とする。本発明に従う短時間の時効処理で十分な高強度
を得るという目的を達成するためには冷間圧延によって
誘起させるマルテンサイト量は40%以上とするのがよ
い。FIG. 3 shows the relationship between the amount of martensite and the age hardening degree ΔHv before and after aging in the case of short-term aging at 530 ° C. for 1 minute among the results in Table 2. From Figure 3,
In the steels of the present invention (○ marks S1 to S8), ΔHv increases with an increase in the amount of martensite, and it is recognized that the age hardening degree is affected by the amount of martensite. On the other hand, the comparative steel a and the conventional steel SUS301 which are out of the composition range have small ΔHv and it is difficult to achieve the object of the present invention. In the method of the present invention, a sufficient age-hardening degree can be obtained by aging treatment for a short time, so this aging treatment can be carried out by a continuous treatment in which the steel strip is continuously passed through a heat treatment furnace. On the other hand, SUS301 has a low age hardening degree (ΔHv) due to aging, and is particularly low for short-time aging. Therefore, high rolling ratio and long-term aging treatment are required to obtain high strength. In order to achieve the purpose of obtaining a sufficiently high strength by aging treatment for a short time according to the present invention, the amount of martensite induced by cold rolling is preferably 40% or more.
第4図は,本発明鋼S6と従来鋼A(SUS301の60%冷間
圧延材)の短時間時効処理温度と硬さの関係を示す。本
発明による冷間圧延率範囲内の従来鋼SUS301(A)では
時効後の硬さ上昇が低く高強度が得られず本発明の目的
は達成出来ない。FIG. 4 shows the relationship between the short-time aging temperature and hardness of Steel S6 of the present invention and Conventional Steel A (60% cold rolled material of SUS301). The conventional steel SUS301 (A) in the range of the cold rolling ratio according to the present invention has a small increase in hardness after aging and cannot obtain high strength, and the object of the present invention cannot be achieved.
一方,本発明の成分範囲内の材料では温度と時間の関
係で硬さは変化するが,400℃×0.5分ですでに高い硬さ
が得られ600℃でも高い硬さを示している。したがっ
て,時効処理は400〜600℃の温度において0.3〜5分の
時間で十分である。On the other hand, in the materials within the composition range of the present invention, the hardness changes depending on the temperature and time, but a high hardness is already obtained at 400 ° C x 0.5 minutes, and a high hardness is exhibited even at 600 ° C. Therefore, for the aging treatment, a time of 0.3 to 5 minutes at a temperature of 400 to 600 ° C is sufficient.
表3に最終調質圧延前に研磨を施こしたものとそうで
ないもののエリクセン試験による割れ発生応力との関係
を示した。表面研磨を施したものではマルテンサイト量
が本発明で規定する範囲外のものでもその割れ発生はあ
る程度改善され,研磨の効果が認められる。これは,冷
間圧延前に研磨を施さないものでは酸洗等による表面肌
荒れや欠陥が存在し,そのまま圧延した場合にその欠陥
が張り出し加工時に切欠となって低応力で破断したもの
である。この場合,特にマルテンサイト量の高いもので
その影響が顕著に現われる。このため切欠勒性の低いも
のでは特に冷間圧延前の研磨の効果が大きく現れる。Table 3 shows the relationship between the stress generated by the Erichsen test and the stress generated by the Erichsen test before and after polishing before final temper rolling. With the surface-polished product, even if the amount of martensite is out of the range specified in the present invention, the occurrence of cracks is improved to some extent, and the polishing effect is recognized. This is because, without polishing before cold rolling, surface roughness and defects are present due to pickling, etc., and when rolling as it is, the defects become notches during overhanging and fracture with low stress. In this case, the effect is particularly pronounced for those with a high amount of martensite. For this reason, the effect of polishing before cold rolling becomes particularly significant in the case of a material having a low notch fracturing property.
第1図は本発明法による実施例鋼S1〜S8(○印)および
比較例(□印)のマルテンサイト量と時効処理後(530
℃×1分)の引張強さ,切欠引張強さと引張強さの比,
エリクセン試験による割れ発生応力との関係を示す図
で,白ヌキは引張強さ,半黒は切欠引張強さと引張強さ
の比,黒はエリクセン試験による割れ発生応力を示す。 第2図は本発明の実施例鋼S4の冷間圧延率と時効処理後
の引張強さおよび切欠引張強さエリクセン試験による割
れ発生応力の関係を示す図であり,○印は引張強さ,●
印は切欠引張強さ,△印はエリクセン試験による割れ発
生応力を示す。 第3図は本発明の実施例鋼S1〜8(○印),比較鋼(□
印)および従来鋼A(SUS301△印)のマルテンサイト量
と時効硬化度ΔHv(時効後硬さ−時効処理前硬さ)との
関係を示す図である。 第4図は本発明の実施例鋼S6と比較鋼A(SUS301の60%
冷間圧延材)について,時効処理温度および時効処理時
間が時効処理後の硬さに及ぼす影響を示した図である。FIG. 1 shows the amount of martensite of Example steels S1 to S8 (circle) and the comparative example (square) according to the method of the present invention and after aging treatment (530
Tensile strength (° C x 1 minute), ratio of notch tensile strength and tensile strength,
In the figure showing the relationship with the crack initiation stress by the Erichsen test, white blank shows the tensile strength, semi-black shows the notch tensile strength-tensile strength ratio, and black shows the crack initiation stress by the Erichsen test. FIG. 2 is a diagram showing the relationship between the cold rolling rate of Example Steel S4 of the present invention and the tensile strength after aging treatment and the crack initiation stress by the notch tensile strength Erichsen test. ●
The mark indicates the notch tensile strength, and the mark indicates the crack initiation stress by the Erichsen test. FIG. 3 shows example steels S1 to 8 (circle) of the present invention, comparative steels (□).
(Mark) and conventional steel A (SUS301Δ mark) and a diagram showing the relationship between the amount of martensite and age hardening ΔHv (hardness after aging-hardness before aging treatment). FIG. 4 shows an example steel S6 of the present invention and a comparative steel A (60% of SUS301).
FIG. 3 is a diagram showing the influence of an aging temperature and an aging time on the hardness after aging treatment for a cold rolled material).
Claims (6)
越え3.0%以下,Mn:2.5%以下,Ni:4.0〜8.0%,Cr:12.0〜
18.0%,Cu:1.0〜3.5%,N:0.15%以下,S:0.008%以下,C
とNの合計が0.10%以上,残部がFeおよび不可避的に混
入してくる不純物よりなり,溶体化処理状態でオーステ
ナイト組織を呈するオーステナイト系ステンレス鋼を,
溶体化処理後において,40〜80容量%の加工誘起マルテ
ンサイト量が生成するに十分な冷間加工率で冷間加工
し,次いで,400〜600℃で0.3〜5分の時効処理すること
からなる,張り出し強度および勒性に優れ且つ180kg/mm
2以上の高強度を有するステンレス鋼の製造方法。1. In% by weight, C: 0.10% or less, Si: 1.0% to 3.0% or less, Mn: 2.5% or less, Ni: 4.0 to 8.0%, Cr: 12.0 to
18.0%, Cu: 1.0 to 3.5%, N: 0.15% or less, S: 0.008% or less, C
And N are 0.10% or more, the balance is Fe and impurities inevitably mixed in, and an austenitic stainless steel that exhibits an austenitic structure in the solution-treated state,
After solution treatment, cold working is performed at a cold working rate sufficient to generate a work-induced martensite amount of 40 to 80% by volume, and then aging treatment is performed at 400 to 600 ° C for 0.3 to 5 minutes. Excellent in overhanging strength and chewing ability and 180kg / mm
A method for producing stainless steel having high strength of 2 or more.
5%,N:0.04〜0.1%,Mn:0.5%未満,S:0.004%以下である
特許請求の範囲第1項記載のステンレス鋼の製造法。2. Si: 2.0 to 3.0%, Ni: 5.0 to 7.0%, Cu: 1.5 to 2.
The method for producing stainless steel according to claim 1, wherein 5%, N: 0.04 to 0.1%, Mn: less than 0.5%, and S: 0.004% or less.
越え3.0%以下,Mn:2.5%以下,Ni:4.0〜8.0%,Cr:12.0〜
18.0%,Cu:1.0〜3.5%,N:0.15%以下,S:0.008%以下,C
とNの合計が0.10%以上,MoまたはWの少なくとも一種:
2.0%以下,残部がFeおよび不可避的に混入してくる不
純物よりなり,溶体化処理状態でオーステナイト組織を
呈するオーステナイト系ステンレス鋼を,溶体化処理後
において,40〜80容量%の加工誘起マルテンサイト量が
生成するに十分な冷間加工率で冷間加工し,次いで,400
〜600℃で0.3〜5分の時効処理することからなる,張り
出し強度および勒性に優れ且つ190kg/mm2以上の高強度
を有するステンレス鋼の製造方法。3. In% by weight, C: 0.10% or less, Si: more than 1.0% and 3.0% or less, Mn: 2.5% or less, Ni: 4.0 to 8.0%, Cr: 12.0 to
18.0%, Cu: 1.0 to 3.5%, N: 0.15% or less, S: 0.008% or less, C
And N total 0.10% or more, at least one of Mo and W:
An austenitic stainless steel with an austenite structure in the solution-treated state, containing 2.0% or less, the balance of which is Fe and inevitably mixed impurities, has a work-induced martensite content of 40-80% by volume after solution treatment. Cold-worked at a cold-working rate sufficient to produce
A method for producing stainless steel, which is excellent in overhanging strength and chewing ability and has a high strength of 190 kg / mm 2 or more, which comprises aging treatment at 〜600 ° C for 0.3-5 minutes.
5%,N:0.04〜0.1%,Mn:0.5%未満,S:0.004%以下である
特許請求の範囲第3項記載のステンレス鋼の製造法。4. Si: 2.0 to 3.0%, Ni: 5.0 to 7.0%, Cu: 1.5 to 2.
The method for producing stainless steel according to claim 3, wherein 5%, N: 0.04 to 0.1%, Mn: less than 0.5%, and S: 0.004% or less.
越え3.0%以下,Mn:2.5%以下,Ni:4.0〜8.0%,Cr:12.0〜
18.0%,Cu:1.0〜3.5%,N:0.15%以下,S:0.008%以下,C
とNの合計が0.10%以上,残部がFeおよび不可避的に混
入してくる不純物よりなるオーステナイト組織を有する
鋼帯を,表面研磨処理のあと40〜80容量%の加工誘起マ
ルテンサイト量が生成するに十分な冷間圧延率で冷間圧
延し,次いで得られた冷延鋼帯を熱処理炉に連続的に通
板して400〜600℃の温度で0.3〜5分の連続時効処理を
施すことからなる高い張り出し強度と勒性を有する高強
度ステンレス鋼帯の製造法。5. In wt%, C: 0.10% or less, Si: 1.0% to 3.0% or less, Mn: 2.5% or less, Ni: 4.0 to 8.0%, Cr: 12.0 to
18.0%, Cu: 1.0 to 3.5%, N: 0.15% or less, S: 0.008% or less, C
A steel strip having an austenite structure consisting of 0.10% or more of Ni and 0.1% or more, the balance being Fe and impurities inevitably mixed in, produces a work-induced martensite content of 40 to 80% by volume after surface polishing. Cold rolling at a sufficient cold rolling rate, then continuously pass the cold-rolled steel strip through a heat treatment furnace and subject it to continuous aging treatment at a temperature of 400 to 600 ° C for 0.3 to 5 minutes. A method for producing a high-strength stainless steel strip having a high overhang strength and toughness.
越え3.0%以下,Mn:2.5%以下,Ni:4.0〜8.0%,Cr:12.0〜
18.0%,Cu:1.0〜3.5%,N:0.15%以下,S:0.008%以下,C
とNの合計が0.10%以上,MoまたはWの少なくとも一種:
2.0%以下,残部がFeおよび不可避的に混入してくる不
純物よりなるオーステナイト組織を有する鋼帯を,表面
研磨処理のあと40〜80容量%の加工誘起マルテンサイト
量が生成するに十分な冷間圧延率で冷間圧延し,次いで
得られた冷延鋼帯を熱処理炉に連続的に通板して400〜6
00℃の温度で0.3〜5分の連続時効処理を施すことから
なる高い張り出し強度と勒性を有する高強度ステンレス
鋼帯の製造法。6. In% by weight, C: 0.10% or less, Si: 1.0% to 3.0% or less, Mn: 2.5% or less, Ni: 4.0 to 8.0%, Cr: 12.0 to
18.0%, Cu: 1.0 to 3.5%, N: 0.15% or less, S: 0.008% or less, C
And N total 0.10% or more, at least one of Mo and W:
Steel strips with an austenite structure of 2.0% or less, the balance of which is Fe and impurities that are inevitably mixed in, are cold enough to produce 40-80% by volume of work-induced martensite after surface polishing. After cold rolling at the rolling rate, the cold-rolled steel strip obtained was continuously passed through a heat treatment furnace for 400 to 6
A method for producing a high-strength stainless steel strip having high overhanging strength and chewing ability, which comprises performing continuous aging treatment for 0.3 to 5 minutes at a temperature of 00 ° C.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP62153443A JPH0826404B2 (en) | 1987-06-22 | 1987-06-22 | Method for producing high strength stainless steel with excellent overhang strength and toughness |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP62153443A JPH0826404B2 (en) | 1987-06-22 | 1987-06-22 | Method for producing high strength stainless steel with excellent overhang strength and toughness |
Publications (2)
Publication Number | Publication Date |
---|---|
JPS63317628A JPS63317628A (en) | 1988-12-26 |
JPH0826404B2 true JPH0826404B2 (en) | 1996-03-13 |
Family
ID=15562654
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JP62153443A Expired - Lifetime JPH0826404B2 (en) | 1987-06-22 | 1987-06-22 | Method for producing high strength stainless steel with excellent overhang strength and toughness |
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Families Citing this family (10)
Publication number | Priority date | Publication date | Assignee | Title |
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JP2537679B2 (en) * | 1989-02-27 | 1996-09-25 | 日新製鋼株式会社 | High-strength stainless steel and its steel material |
JPH0742550B2 (en) * | 1990-10-09 | 1995-05-10 | 新日本製鐵株式会社 | Stainless steel with excellent strength and ductility |
JPH04202643A (en) * | 1990-11-30 | 1992-07-23 | Nkk Corp | Stainless steel having high strength and high toughness and its production |
JP2677910B2 (en) * | 1991-03-20 | 1997-11-17 | 神鋼鋼線工業株式会社 | Stainless steel for springs with excellent dimensional stability during low temperature annealing |
US5496514A (en) * | 1993-03-08 | 1996-03-05 | Nkk Corporation | Stainless steel sheet and method for producing thereof |
US5407493A (en) * | 1993-03-08 | 1995-04-18 | Nkk Corporation | Stainless steel sheet and method for producing thereof |
US5314549A (en) * | 1993-03-08 | 1994-05-24 | Nkk Corporation | High strength and high toughness stainless steel sheet and method for producing thereof |
DE4406040A1 (en) * | 1993-11-30 | 1995-06-01 | Nippon Kokan Kk | Stainless steel sheet having high fracture resistance |
WO2011062152A1 (en) * | 2009-11-18 | 2011-05-26 | 住友金属工業株式会社 | Austenite stainless steel sheet and method for producing same |
JP6738671B2 (en) * | 2016-07-01 | 2020-08-12 | 日鉄ステンレス株式会社 | Stainless steel plate |
Citations (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5677364A (en) * | 1979-11-29 | 1981-06-25 | Kawasaki Steel Corp | Spring stainless steel with superior manufacturability, forming workability and fatigue characteristic after aging |
JPS5719738A (en) * | 1980-06-05 | 1982-02-02 | Mitsubishi Paper Mills Ltd | Diffusion transfer material containing developing agent |
-
1987
- 1987-06-22 JP JP62153443A patent/JPH0826404B2/en not_active Expired - Lifetime
Patent Citations (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5677364A (en) * | 1979-11-29 | 1981-06-25 | Kawasaki Steel Corp | Spring stainless steel with superior manufacturability, forming workability and fatigue characteristic after aging |
JPS5719738A (en) * | 1980-06-05 | 1982-02-02 | Mitsubishi Paper Mills Ltd | Diffusion transfer material containing developing agent |
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