JPH0920923A - Production of high carbon stainless steel plate - Google Patents
Production of high carbon stainless steel plateInfo
- Publication number
- JPH0920923A JPH0920923A JP16981695A JP16981695A JPH0920923A JP H0920923 A JPH0920923 A JP H0920923A JP 16981695 A JP16981695 A JP 16981695A JP 16981695 A JP16981695 A JP 16981695A JP H0920923 A JPH0920923 A JP H0920923A
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- Prior art keywords
- stainless steel
- carbon stainless
- steel sheet
- temperature
- hot
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
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- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は、高硬度で優れた耐摩耗
性が必要とされる包丁、ナイフ、カッター、はさみ等の
おもに刃物用などの材料として用いられる高炭素ステン
レス鋼板の製造方法に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for producing a high-carbon stainless steel sheet used as a material for knives, knives, cutters, scissors, etc., which are required to have high hardness and excellent wear resistance. .
【０００２】[0002]
【従来の技術】高炭素ステンレス鋼は、焼入れによりマ
ルテンサイト組織に変態するので、高硬度、耐摩耗性が
要求される材料として用いられている。特に、刃物用な
どの材料としての用途が多い。2. Description of the Related Art High-carbon stainless steel is transformed into a martensitic structure by quenching and is therefore used as a material requiring high hardness and wear resistance. In particular, it has many uses as a material for blades and the like.
【０００３】これらの材料として用いられる高炭素ステ
ンレス鋼板は、一般に、熱間圧延によって得られた鋼帯
をコイルに巻き取り、焼鈍等の処理を施して、素材とし
て提供されている。鋼帯をコイルに巻き取る方法は、平
鋼板を製造する方法に比べて製造コストが著しく安いの
で、高炭素ステンレス鋼板の製造においても巻き取り工
程が採用されている。しかし、高炭素ステンレス鋼の熱
延鋼板（以下、鋼帯を含め板状の製品を広義の意味で鋼
板と称す）は靭性が低いために、熱延コイルを展開する
際に鋼板が破断することがあり、作業者に危険を及ぼす
恐れがある。また、その後の冷間圧延工程においても、
靱性が低いことに起因して、エッジクラックが発生する
こと、あるいはエッジクラックに伴って破断が生じるこ
と等のトラブルが生じる場合がある。このように、高炭
素ステンレス鋼は、品質上、製造上および安全上の解決
すべき課題が残されているのが実態である。The high carbon stainless steel sheets used as these materials are generally provided as a raw material by winding a steel strip obtained by hot rolling on a coil and subjecting it to annealing or the like. Since the method of winding the steel strip around the coil has a significantly lower manufacturing cost than the method of manufacturing the flat steel sheet, the winding step is also adopted in the production of the high carbon stainless steel sheet. However, high-carbon stainless steel hot-rolled steel sheets (hereinafter, plate-shaped products including steel strips are referred to as steel sheets in a broad sense) have low toughness, so that the steel sheets may break when the hot-rolled coil is deployed. There is a risk that it may pose a danger to workers. Also, in the subsequent cold rolling process,
Due to the low toughness, troubles such as occurrence of edge cracks or breakage accompanying edge cracks may occur. As described above, high carbon stainless steel has a problem that quality, manufacturing, and safety have to be solved.
【０００４】そのために、これらの課題の解決策とし
て、熱延鋼板の軟質化あるいは靱性の向上対策が講じら
れている。高炭素ステンレス鋼を軟質化するための処理
としては、従来は鋼帯を高温で巻き取り、徐冷する方法
が一般的であった。例えば、９００℃以下で熱間圧延を
終了し、８００℃以上で軟化処理を施し５０℃／時間以
下の冷却速度で徐冷する方法（特開昭５９−１５３８３
２号公報）がある。この他、軟質化方法として、特開昭
６２−１９６３２４号公報には、熱延鋼板に球状化焼鈍
を施し（フェライト＋炭化物）組織とすることにより軟
質化した後、Ａ1変態点〜１５０℃の温度範囲で温間圧
延する方法が開示されている。Therefore, as a solution to these problems, measures for softening or improving the toughness of hot rolled steel sheets have been taken. As a treatment for softening high-carbon stainless steel, conventionally, a method of winding a steel strip at a high temperature and gradually cooling it has been generally used. For example, a method in which hot rolling is completed at 900 ° C. or less, softening treatment is performed at 800 ° C. or more, and gradual cooling is performed at a cooling rate of 50 ° C./hour or less (JP-A-59-15383).
No. 2). In addition, as the softening process, in JP-A-62-196324, was softened by the performing spheroidizing annealing hot-rolled steel plate (ferrite + carbides) tissue, A 1 transformation point to 150 DEG ° C. A method of warm rolling in the temperature range of 1 is disclosed.
【０００５】高炭素ステンレス鋼の熱延鋼板の靭性を改
善する方法として、特開平２−１０１１１９号公報に
は、熱間圧延後、７８０℃以上で３０分以上保持するこ
とにより、オーステナイト粒内にＣｒ炭化物を析出さ
せ、その炭化物を核としてフェライトを析出させる方
法、特開平６−６５６３９号公報には、双ロール法等に
よって急冷凝固させることにより靭性に優れた高炭素ス
テンレス鋼を得る方法が示されている。As a method of improving the toughness of a hot-rolled steel sheet of high carbon stainless steel, Japanese Patent Laid-Open No. 2-101119 discloses that after hot rolling, it is retained at 780 ° C. or higher for 30 minutes or more, so that the austenite grains are retained. A method of precipitating Cr carbide and precipitating ferrite by using the carbide as a nucleus, Japanese Patent Laid-Open No. 6-65639 discloses a method of obtaining high carbon stainless steel having excellent toughness by rapid solidification by a twin roll method or the like. Has been done.
【０００６】[0006]
【発明が解決しようとする課題】特開昭５９−１５３８
３２号公報および特開昭６２−１９６３２４号公報の方
法では、ある程度の延性を確保することができる。しか
し、熱延鋼板の常温での靭性を十分に向上させるまでに
は至っていない。Problems to be Solved by the Invention JP-A-59-1538
According to the methods disclosed in Japanese Patent Laid-Open No. 32 and Japanese Patent Laid-Open No. 62-196324, a certain degree of ductility can be secured. However, the toughness of the hot rolled steel sheet at room temperature has not been sufficiently improved.
【０００７】特開平２−１０１１１９号公報の方法は、
熱延鋼板の軟質化には効果があるが、常温での衝撃値
（ vＥ20）は２０Ｊ/cm2を超える程度であり、冷間圧延
工程における安全操業という観点からも、実用上満足で
きる方法とは言えない。The method disclosed in Japanese Patent Laid-Open No. 2-101119 is as follows.
Although it is effective in softening the hot rolled steel sheet, the impact value (vE 20 ) at room temperature is about 20 J / cm 2 or less, which is a practically satisfactory method from the viewpoint of safe operation in the cold rolling process. It can not be said.
【０００８】また、特開平６−６５６３９号公報の方法
は、再溶解と急冷凝固といったプロセスを採っているの
で、特殊な製造設備を必要とすることに加えて、工程が
複雑であるために、製造コストが高く、生産性が低いと
いった欠点がある。Further, since the method of Japanese Patent Laid-Open No. 6-65639 uses a process of remelting and rapid solidification, in addition to requiring special manufacturing equipment, the process is complicated, There are drawbacks such as high manufacturing cost and low productivity.
【０００９】このように、現状の技術では、高炭素ステ
ンレス鋼の持つ品質、生産性、安全性等、前述の問題点
を解決できていないのが実状である。As described above, the current state of the art is that the above-mentioned problems such as quality, productivity and safety of high carbon stainless steel cannot be solved.
【００１０】本発明は、このような課題を解決するため
になされたものであり、熱延コイル展開時に破断等の恐
れのない、靱性が高く、生産性に優れた高炭素ステンレ
ス鋼板の製造方法を提供することを目的としている。The present invention has been made to solve the above problems, and is a method for producing a high-carbon stainless steel sheet having high toughness and excellent productivity, which is free from the risk of breakage when the hot rolled coil is expanded. Is intended to provide.
【００１１】[0011]
【課題を解決するための手段】従来、高炭素ステンレス
鋼の靭性を向上させる手段としては、おもに鋳造時の凝
固過程で初晶オーステナイト粒界に晶出する巨大な共晶
Ｃｒ炭化物の生成を抑制することに注目した対策が採ら
れていた（例えば、特開昭６２−１９６３２４号公
報）。しかし、本発明者らは、ＣおよびＣｒ含有率を適
正な範囲に制限することにより、高炭素ステンレス鋼に
おいても、鋼塊を熱間圧延するための１２００℃程度の
加熱の際に、Ｃを鋼中に固溶させ、巨大炭化物を消失さ
せられることを明かにした。[Means for Solving the Problems] Conventionally, as a means for improving the toughness of high carbon stainless steels, the suppression of the formation of huge eutectic Cr carbides that crystallize at the primary austenite grain boundaries during the solidification process during casting Measures that take notice of this have been adopted (for example, JP-A-62-196324). However, the inventors of the present invention limit the C and Cr contents to an appropriate range so that even in high-carbon stainless steel, when heating at about 1200 ° C. for hot rolling a steel ingot, C It was clarified that it can be dissolved in steel to dissolve giant carbides.
【００１２】本発明者らは、上記の調査結果を基に、熱
間圧延中に生成するＣｒ炭化物の形態を制御することに
より、熱延鋼板の靭性を向上させることができると考え
た。Based on the above investigation results, the present inventors considered that the toughness of the hot-rolled steel sheet can be improved by controlling the morphology of Cr carbide formed during hot rolling.
【００１３】このような観点に立って、高炭素ステンレ
ス鋼の熱延鋼板の靭性を劣化させる原因について詳細に
調査するとともに、熱延鋼板の靭性を向上させることが
できる熱間圧延方法および焼鈍方法について様々な検討
を行った。その結果、下記の新しい知見を得た。From this point of view, the cause of deterioration of the toughness of the hot-rolled steel sheet of high carbon stainless steel is investigated in detail, and the toughness of the hot-rolled steel sheet can be improved and the hot rolling method and annealing method can be improved. About various things. As a result, the following new findings were obtained.
【００１４】（ａ）熱延鋼板の靭性を低下させる主因
は、熱間圧延およびその後の冷却過程でオーステナイト
粒界に析出する鎖状炭化物である。(A) The main cause of reducing the toughness of the hot-rolled steel sheet is a chain carbide that precipitates at the austenite grain boundaries during the hot rolling and the subsequent cooling process.
【００１５】（ｂ）上記のオーステナイト粒界に析出す
る鎖状炭化物の生成は、熱間圧延後の鋼帯の巻き取り温
度を７５０℃以下とする低温巻き取りによって防止でき
る。(B) The formation of chain-like carbides that precipitate at the austenite grain boundaries can be prevented by low-temperature winding in which the winding temperature of the steel strip after hot rolling is 750 ° C. or lower.
【００１６】（ｃ）低温巻き取り後、炭化物を球状化す
るための焼鈍（球状化焼鈍）を行うことによって、鋼板
に優れた靱性を付与することができる。(C) By performing low-temperature winding and then annealing for spheroidizing the carbide (spheroidizing annealing), excellent toughness can be imparted to the steel sheet.
【００１７】（ｄ）低温巻き取り後の鋼板（熱延コイ
ル）の球状化焼鈍は、ＡC1以上の温度で保持後、ＡC1以
下の温度で保持する２段焼鈍法が特に有効である。(D) As for the spheroidizing annealing of the steel sheet (hot rolled coil) after the low temperature winding, a two-stage annealing method in which the steel sheet is held at a temperature of A C1 or higher and then held at a temperature of A C1 or lower is particularly effective.
【００１８】本発明は、上記の知見を基に完成させたも
のであり、（１）重量割合で、Ｃ：０．４〜０．８％、
Ｃｒ：１１〜１６％を含む高炭素ステンレス鋼を熱間圧
延した後、７５０℃以下の温度で鋼帯を巻き取り熱延コ
イルとし、熱延コイルに球状化焼鈍処理を施す高炭素ス
テンレス鋼板の製造方法、および（２）重量割合で、
Ｃ：０．４〜０．８％、Ｃｒ：１１〜１６％を含む高炭
素ステンレス鋼を熱間圧延した後、７５０℃以下の温度
で鋼帯を巻き取り熱延コイルとし、この熱延コイルに、
ＡC1〜（ＡC1＋１００）℃の温度範囲で保持し、さらに
（ＡC1−１００）〜ＡC1℃の温度範囲で保持する２段焼
鈍処理を施す高炭素ステンレス鋼板の製造方法、を要旨
とする。The present invention has been completed based on the above findings. (1) C: 0.4 to 0.8% by weight,
After hot rolling a high carbon stainless steel containing Cr: 11 to 16%, a steel strip is wound at a temperature of 750 ° C. or less to form a hot rolled coil, and the hot rolled coil is subjected to spheroidizing annealing treatment. Manufacturing method, and (2) by weight ratio,
After hot rolling a high-carbon stainless steel containing C: 0.4 to 0.8% and Cr: 11 to 16%, a steel strip is wound at a temperature of 750 ° C. or less to form a hot rolled coil. To
And held at a temperature in the range of A C1 ~ (A C1 +100) ℃, further (A C1 -100) method for producing a high carbon stainless steel sheet subjected to two-stage annealing process of holding in the temperature range of to A C1 ° C., and the gist To do.
【００１９】なお、ここで、ＡC1とは、加熱過程で金属
組織がフェライトからオーステナイトに変態する温度で
あり、本発明が対象とするＣｒ含有率１１〜１６重量％
（以下、化学組成の％表示は重量％）の高炭素ステンレ
ス鋼の場合には下記の式（１）で表される。Here, A C1 is the temperature at which the metal structure transforms from ferrite to austenite in the heating process, and the Cr content of 11 to 16% by weight, which is the object of the present invention.
In the case of high-carbon stainless steel (hereinafter,% of chemical composition is represented by weight), it is represented by the following formula (1).
【００２０】 ＡC1＝８７０−５０［％Ｃ］ 式（１） ただし、［％Ｃ］：高炭素ステンレス鋼中のＣ含有率 測定時の昇温速度：１〜５℃／秒A C1 = 870-50 [% C] Formula (1) where [% C]: C content in high carbon stainless steel Temperature rising rate during measurement: 1 to 5 ° C./sec
【００２１】[0021]
【作用】本発明が対象としている高炭素ステンレス鋼の
化学組成範囲とその限定理由あるいは望ましい範囲、お
よび本発明の製造条件について、以下に説明する。The chemical composition range of the high carbon stainless steel which is the object of the present invention, the reason for the limitation or the desirable range thereof, and the production conditions of the present invention will be described below.
【００２２】Ｃ：下限を０．４％としたのは、０．４％
未満では刃物用材料として必要な高い硬度が得られない
からである。また、０．８％を超えると鋳造の際の凝固
時に巨大なＣｒ炭化物が析出し、熱間圧延後にもその影
響が残るので、熱延鋼板の靭性が低下する。さらにＣｒ
炭化物の量も多いので、耐食性も悪くなる。そのため
に、Ｃ含有量の上限は０．８％とした。C: The lower limit of 0.4% is 0.4%
If it is less than the above range, the high hardness required as a material for cutting tools cannot be obtained. On the other hand, if it exceeds 0.8%, a huge Cr carbide precipitates during solidification during casting, and the effect remains after hot rolling, so that the toughness of the hot rolled steel sheet deteriorates. Further Cr
Since the amount of carbides is large, the corrosion resistance is also poor. Therefore, the upper limit of the C content is 0.8%.
【００２３】Ｃｒ：Ｃｒは、鋼の一般的な耐食性を向上
させる上で必須の合金元素である。Cr: Cr is an essential alloying element for improving the general corrosion resistance of steel.
【００２４】その基本的な耐食性を確保するには１１％
以上必要である。また、１６％を超えると凝固時に巨大
なＣｒ炭化物が生成すると同時に、オーステナイト粒界
に炭化物が鎖状に生成しやすくなり、靭性が著しく劣化
する。そのため、上限は１６％と定めた。11% to ensure its basic corrosion resistance
The above is necessary. On the other hand, if it exceeds 16%, a large amount of Cr carbide is generated at the time of solidification, and at the same time, carbide is likely to be formed in a chain at the austenite grain boundary, and the toughness is significantly deteriorated. Therefore, the upper limit was set to 16%.
【００２５】Ｓｉ、Ｍｎ：いずれも溶鋼の脱酸用として
必要な元素である。しかし、Ｓｉ含有率が１％を超える
と熱間加工性および冷間加工性が悪くなる。また、Ｍｎ
含有率が１％を超えると焼き入れの際に残留オーステナ
イトが増加し、焼入硬度が低下する。したがって、Ｓｉ
およびＭｎ含有率の上限は１％とすることが望ましい。Si and Mn: Both are elements necessary for deoxidizing molten steel. However, if the Si content exceeds 1%, the hot workability and cold workability deteriorate. Also, Mn
If the content exceeds 1%, retained austenite increases during quenching, and quenching hardness decreases. Therefore, Si
The upper limit of the Mn content is preferably 1%.
【００２６】その他の元素：Ｐ、Ｓなどの不可避的に含
まれる元素は極力少ない方がよい。Other elements: Elements such as P and S that are inevitably contained are preferably as few as possible.
【００２７】通常の手段で工業的に製造可能なレベル
は、Ｐ：０．０３％以下、Ｓ：０．０１％以下程度であ
り、本発明が対象としている高炭素ステンレス鋼の場合
にも、そのレベル以下が好ましい。The level which can be industrially produced by ordinary means is about P: 0.03% or less and S: 0.01% or less, and even in the case of the high carbon stainless steel targeted by the present invention, Below that level is preferred.
【００２８】本発明において、熱間圧延後の鋼帯の巻き
取りを、７５０℃以下の低温巻き取りとする理由は次の
とおりである。In the present invention, the reason why the steel strip after hot rolling is wound at a low temperature of 750 ° C. or lower is as follows.
【００２９】鋼帯の巻き取り開始温度が７５０℃を超え
ている場合には、巻き取り後の冷却過程で、オーステナ
イト粒界に鎖状の炭化物が生成し、熱延鋼板の靭性を著
しく低下させる。したがって、鋼帯の巻き取り開始温度
の上限は７５０℃とした。また、巻き取り開始温度が低
い場合には、鋼板の靱性には問題がないが、鋼板の硬度
が高くなるので、巻取り作業に支障を来す場合がある。
したがって、巻き取り温度の下限は、５００℃以上とす
ることが望ましい。When the winding start temperature of the steel strip exceeds 750 ° C., chain carbides are formed in the austenite grain boundaries during the cooling process after winding, and the toughness of the hot rolled steel sheet is remarkably reduced. . Therefore, the upper limit of the winding start temperature of the steel strip is set to 750 ° C. Further, when the winding start temperature is low, the toughness of the steel sheet is not a problem, but the hardness of the steel sheet becomes high, which may hinder the winding operation.
Therefore, the lower limit of the winding temperature is preferably 500 ° C. or higher.
【００３０】なお、本発明の鋼帯の巻き取り温度は、式
（１）から求められるＡC1温度８３０〜８５０℃（本発
明の対象鋼のＣ含有率０．４〜０．８％より算出）に比
べて、８０℃以上低い温度となっている。[0030] Incidentally, the coiling temperature of the steel strip of the present invention, calculated from the C content 0.4 to 0.8 percent of the target steel A C1 temperature eight hundred thirty to eight hundred and fifty ° C. (present invention obtained from the equation (1) The temperature is 80 ° C. or more lower than that in (1).
【００３１】本発明は、鋼帯を低温で巻き取り熱延コイ
ルとし、それに続く箱型炉等による熱延コイルの焼鈍を
組み合わせることによってＣｒ炭化物の形態を制御し、
熱延鋼板の靭性を向上させることを特徴としている。そ
のために、球状化焼鈍が必要である。The present invention controls the morphology of Cr carbide by combining a steel strip at a low temperature to form a hot rolled coil and then annealing the hot rolled coil in a box furnace or the like.
It is characterized by improving the toughness of the hot rolled steel sheet. Therefore, spheroidizing annealing is necessary.
【００３２】本発明の球状化焼鈍としては、通常のＡC1
直上近傍の温度での焼鈍方法（例えば、ステンレス鋼便
覧；Ｐ．６８１、１９７４年）を採用することができ
る。この通常の焼鈍方法でも、本発明の目的とする靱性
を備えた高炭素ステンレス鋼板を得ることができる。さ
らに、好ましいのは、前記の２段焼鈍法である。２段焼
鈍法によれば、鋼板の靱性をいっそう向上させることが
できる。As the spheroidizing annealing of the present invention, a conventional A C1
An annealing method at a temperature in the vicinity of immediately above (for example, Stainless Steel Handbook; P. 681, 1974) can be adopted. Even with this normal annealing method, it is possible to obtain a high carbon stainless steel sheet having the toughness that is the object of the present invention. Further, the two-step annealing method is preferable. According to the two-step annealing method, the toughness of the steel sheet can be further improved.
【００３３】２段焼鈍法において、１段目の焼鈍温度
を、ＡC1〜（ＡC1＋１００）℃（本発明の対象鋼の場
合、ＡC1は８３０〜８５０℃、ただしＡC1温度測定時の
昇温速度は１〜５℃／秒）とする理由は、熱延鋼板の金
属組織をオーステナイトに逆変態させることにより、炭
化物をすばやく成長させ、球状化させるためである。し
かし、（ＡC1＋１００）℃を超えると固溶炭素が多くな
るので、炭化物を十分に成長させることができない。ま
た、製造コストが高くなる原因にもなる。したがって、
１段目の焼鈍温度は上記の範囲とした。１段目の焼鈍時
間は、炭化物を成長させ、十分に球状化させるために、
１時間以上とするのが望ましい。In the two-step annealing method, the annealing temperature of the first step is set to A C1 to (A C1 +100) ° C. (In the case of the subject steel of the present invention, A C1 is 830 to 850 ° C., provided that A C1 temperature is measured. The reason for setting the temperature rising rate to 1 to 5 ° C./sec) is that the metal structure of the hot-rolled steel sheet is inversely transformed into austenite to rapidly grow carbides and make them spherical. However, when the temperature exceeds (A C1 +100) ° C., the amount of solid solution carbon increases, so that the carbide cannot be grown sufficiently. In addition, it also causes an increase in manufacturing cost. Therefore,
The annealing temperature of the first step was within the above range. The annealing time of the first step is to grow the carbide and make it sufficiently spheroidized.
It is desirable to set it to 1 hour or more.
【００３４】２段目の焼鈍温度を、（ＡC1−１００）〜
ＡC1℃としたのは、１段目の焼鈍で球状化させた炭化物
をさらに成長させ、固溶炭素量を十分減少させて鋼板の
靭性を高くするためである。ＡC1温度以下とするのは、
Ｃの固溶率が低いフェライト相で保持する方が、固溶炭
素量を減らしやすいからである。また、焼鈍温度の下限
を（ＡC1−１００）℃とするのは、その温度以下では炭
化物の成長が遅過ぎるためである。２段目の焼鈍時間
は、十分に炭化物を成長させる観点から、５時間以上と
するのが望ましい。[0034] The second stage of the annealing temperature, (A C1 -100) ~
The reason for setting A C1 ° C. is to increase the toughness of the steel sheet by further growing the carbide spheroidized by the first annealing and sufficiently reducing the amount of solute carbon. The temperature below A C1 is
This is because it is easier to reduce the amount of solute carbon by holding the carbon in the ferrite phase having a low solid solubility. Further, the lower limit of the annealing temperature is set to (A C1 -100) ° C. because the growth of the carbide is too slow below that temperature. The second annealing time is preferably 5 hours or more from the viewpoint of sufficiently growing the carbide.
【００３５】[0035]
【実施例】実施例に基づいて本発明を具体的に説明す
る。EXAMPLES The present invention will be specifically described based on examples.
【００３６】表１に、用いた供試材の化学組成およびＡ
C1温度を示す。Table 1 shows the chemical composition and A of the test materials used.
Indicates C1 temperature.
【００３７】[0037]
【表１】 [Table 1]
【００３８】真空溶解法により、表１の化学組成を持つ
高炭素ステンレス鋼を溶製し、５０ｋｇ鋼塊に鋳造し
た。この鋼塊を鍛造し、厚さ４０ｍｍ、幅１００ｍｍ、
長さ１５０ｍｍの熱間圧延用素材を作製した。次に、こ
の熱間圧延用素材を１２３０℃に加熱した後、厚さ４０
ｍｍから５ｍｍまで、最終パス温度９５０℃以上の条件
で熱間圧延し、鋼帯（鋼板）を得た。次に、その鋼帯を
巻き取り開始温度としての９００〜４００℃の各温度か
ら、熱延コイルとする場合と同じ冷却条件で巻き取り処
理を施した。この場合の温度降下速度は約４０℃／ｈで
ある。さらに、この熱延鋼板に、下記の３つの条件で球
状化焼鈍を施した。A high carbon stainless steel having the chemical composition shown in Table 1 was melted by a vacuum melting method and cast into a 50 kg steel ingot. This steel ingot is forged to have a thickness of 40 mm, a width of 100 mm,
A material for hot rolling having a length of 150 mm was produced. Next, after heating the material for hot rolling to 1230 ° C., a thickness of 40
From 5 mm to 5 mm, hot rolling was performed under the condition that the final pass temperature was 950 ° C. or higher to obtain a steel strip (steel plate). Next, the steel strip was subjected to a winding treatment from each temperature of 900 to 400 ° C. as a winding start temperature under the same cooling conditions as in the case of forming a hot rolled coil. The temperature drop rate in this case is about 40 ° C./h. Furthermore, this hot rolled steel sheet was subjected to spheroidizing annealing under the following three conditions.
【００３９】 ８６０℃×１０時間＋炉冷（本発明に
用いる通常の焼鈍法） ９００℃×１時間＋７８０℃×６時間＋空冷（本発
明の２段焼鈍法） ９００℃×１時間＋７００℃×６時間＋空冷（比較
例の２段焼鈍法） 上記の処理によって得られた試験材から、厚さ１０ｍ
ｍ、幅５ｍｍ、長さ５５ｍｍ、ノッチ形状Ｖ型（深さ２
ｍｍ）のシャルピー衝撃試験片を作製し、この試験片を
用いて、温度２５℃の条件で衝撃試験を行った。860 ° C. × 10 hours + furnace cooling (normal annealing method used in the present invention) 900 ° C. × 1 hour + 780 ° C. × 6 hours + air cooling (two-step annealing method of the present invention) 900 ° C. × 1 hour + 700 ° C. × 6 hours + air cooling (two-step annealing method of comparative example) From the test material obtained by the above treatment, a thickness of 10 m
m, width 5 mm, length 55 mm, notch shape V type (depth 2
mm) Charpy impact test piece was prepared, and an impact test was performed under the condition of a temperature of 25 ° C. using this test piece.
【００４０】（実施例１）供試材Ａ、ＢおよびＣを対象
に、鋼帯の巻き取り開始温度と鋼板の衝撃値との関係を
確認した。なお、熱延鋼板の球状化焼鈍は、本発明の２
段焼鈍法（上記の条件）とした。図１に試験結果を示
す。Example 1 With respect to the test materials A, B and C, the relationship between the winding start temperature of the steel strip and the impact value of the steel sheet was confirmed. In addition, the spheroidizing annealing of the hot rolled steel sheet is performed according to
The step annealing method (the above conditions) was adopted. The test results are shown in FIG.
【００４１】図１から明かなように、供試材Ａ、Ｂ、Ｃ
ともに、巻き取り開始温度７５０℃までは、衝撃値が３
０Ｊ／ｃｍ2 を超えており、鋼板は十分な靱性を持って
いる。それに対し、巻き取り温度が７５０℃を超えると
衝撃値が急激に低下する。したがって、巻き取り開始温
度は、７５０℃以下とする必要があることが確認され
た。また、巻き取り開始温度が４００℃程度と低い場合
には、衝撃値の面では問題はないが、鋼板の硬度が高い
ために、鋼帯の巻き取り作業に難がある。したがって、
巻き取り開始温度の下限は、５００℃以上が好ましいと
いえる。なお、衝撃値のレベルは、供試材Ａが高く、
Ｂ、Ｃの順に低くなっている。これは、Ｃ含有率の影響
によるものであり、本実施例でもＣ含有率が低い程靱性
が高い傾向が認められた。As is apparent from FIG. 1, the test materials A, B and C
In both cases, the impact value is 3 up to the winding start temperature of 750 ° C.
It exceeds 0 J / cm 2 , and the steel sheet has sufficient toughness. On the other hand, when the winding temperature exceeds 750 ° C, the impact value sharply decreases. Therefore, it was confirmed that the winding start temperature needs to be 750 ° C. or lower. Further, when the winding start temperature is as low as about 400 ° C., there is no problem in terms of impact value, but since the hardness of the steel sheet is high, the winding work of the steel strip is difficult. Therefore,
It can be said that the lower limit of the winding start temperature is preferably 500 ° C. or higher. In addition, the level of impact value is high for the test material A,
It becomes lower in the order of B and C. This is due to the influence of the C content, and in this example as well, it was recognized that the lower the C content, the higher the toughness.
【００４２】（実施例２）供試材Ａ、Ｂ、Ｃを対象に、
鋼帯の巻き取り開始温度と球状化焼鈍条件との組み合わ
せおよび熱延鋼板の衝撃値の関係を確認した。熱延鋼板
の球状化焼鈍は、前記の、およびの３条件とし
た。表２に試験結果を示す。(Example 2) For test materials A, B and C,
The relationship between the coiling start temperature of the steel strip and the spheroidizing annealing conditions and the impact value of the hot rolled steel sheet were confirmed. The spheroidizing annealing of the hot-rolled steel sheet was performed under the above three conditions. Table 2 shows the test results.
【００４３】[0043]
【表２】 [Table 2]
【００４４】本発明例の試験Ｎｏ．１〜６については、
巻き取り開始温度が本発明の範囲内（６００℃または７
００℃）であるので、本発明に用いる通常の焼鈍方法
（、試験Ｎｏ．１〜３）の場合でも、本発明の２段焼
鈍法（、試験Ｎｏ．４〜６）の場合でも、衝撃値が３
０Ｊ／ｃｍ2 を超えており、鋼板が十分な靱性を持って
いることが分かる。中でも、本発明の２段焼鈍法による
処理では、供試材Ｃの場合でも衝撃値が４０Ｊ／ｃｍ2
を超えており、鋼板が優れた靱性を備えていることが裏
付けられた。Test No. of the present invention example For 1 to 6,
The winding start temperature is within the range of the present invention (600 ° C or 7
00 ° C.), the impact value can be obtained both in the case of the normal annealing method (, Test Nos. 1 to 3) used in the present invention and in the case of the two-step annealing method of the present invention (, Test Nos. 4 to 6). Is 3
It exceeds 0 J / cm 2, and it can be seen that the steel sheet has sufficient toughness. Among them, in the treatment by the two-step annealing method of the present invention, even in the case of the sample material C, the impact value was 40 J / cm 2
, Which proves that the steel sheet has excellent toughness.
【００４５】一方、比較例については、鋼帯の巻き取り
開始温度が本発明の範囲より高い試験Ｎｏ．７、８、１
０では、球状化焼鈍条件が適切（前記または）であ
っても、衝撃値が３０Ｊ／ｃｍ2 以下で、鋼板の靱性が
不十分であることが分かる。On the other hand, in the comparative example, the test No. in which the winding start temperature of the steel strip is higher than the range of the present invention. 7, 8, 1
At 0, the impact value was 30 J / cm 2 or less and the toughness of the steel sheet was insufficient even if the spheroidizing annealing conditions were appropriate (the above or).
【００４６】また、巻き取り開始温度が６００℃で本発
明の範囲内であっても、２段焼鈍法による球状化焼鈍条
件が本発明の範囲外の場合（試験Ｎｏ．９）には、衝撃
値が極めて低く、鋼板の靱性に問題があることが確認さ
れた。Even when the winding start temperature is 600 ° C. and is within the range of the present invention, impact is generated when the spheroidizing annealing condition by the two-step annealing method is outside the range of the present invention (Test No. 9). It was confirmed that the value was extremely low and there was a problem in the toughness of the steel sheet.
【００４７】[0047]
【発明の効果】本発明の製造方法で得られる高炭素ステ
ンレス鋼板は、鋼板の靱性が高いので、熱延コイルを展
開する際に鋼板が破断する恐れがない。また、冷間圧延
を行っても、エッジクラックの発生あるいは鋼板の破断
等の懸念もない。したがって、靱性が高く品質のよい高
炭素ステンレス鋼板を歩留まりよく、安全に製造するこ
とができる。さらに、本発明の製造方法は、従来用いら
れている製造設備を利用して、高炭素ステンレス鋼板を
連続的に製造することができるので、低い製造コストで
大量に生産することができる等優れた特長を有してい
る。Since the high carbon stainless steel sheet obtained by the production method of the present invention has high toughness, there is no risk of the steel sheet breaking when the hot rolled coil is deployed. Further, even if cold rolling is performed, there is no concern that edge cracks will occur or the steel sheet will break. Therefore, it is possible to safely manufacture a high carbon steel sheet having high toughness and high quality with a high yield. Furthermore, the production method of the present invention is capable of continuously producing high-carbon stainless steel sheets by utilizing the production equipment that has been conventionally used, and thus is excellent in that it can be mass-produced at a low production cost. It has features.
【図１】鋼帯の巻き取り開始温度と得られた熱延鋼板の
衝撃値との関係を示す図である。FIG. 1 is a diagram showing a relationship between a winding start temperature of a steel strip and an impact value of a hot rolled steel sheet obtained.
Claims (2)
ｒ：１１〜１６％を含む高炭素ステンレス鋼板の製造方
法において、熱間圧延後、７５０℃以下の温度で鋼帯を
巻き取り熱延コイルとした後、前記熱延コイルに球状化
焼鈍処理を施すことを特徴とする高炭素ステンレス鋼板
の製造方法。1. A weight ratio of C: 0.4 to 0.8%, C
In the method for producing a high carbon stainless steel sheet containing r: 11 to 16%, after hot rolling, a steel strip is wound at a temperature of 750 ° C. or lower to form a hot rolled coil, and the hot rolled coil is subjected to spheroidizing annealing treatment. A method for producing a high-carbon stainless steel sheet, which comprises applying the steel sheet.
ｒ：１１〜１６％を含む高炭素ステンレス鋼板の製造方
法において、熱間圧延後、７５０℃以下の温度で鋼帯を
巻き取り熱延コイルとした後、前記熱延コイルに、ＡC1
〜（ＡC1＋１００）℃温度範囲で保持し、さらに（ＡC1
−１００）〜ＡC1℃の温度範囲で保持する２段焼鈍処理
を施すことを特徴とする高炭素ステンレス鋼板の製造方
法。2. A weight ratio of C: 0.4 to 0.8%, C
In a method for producing a high carbon stainless steel sheet containing r: 11 to 16%, after hot rolling, a steel strip is wound into a hot rolled coil at a temperature of 750 ° C. or lower, and then the hot rolled coil has A C1
~ (A C1 +100) and held at ℃ temperature range, further (A C1
-100) to A C1 ° C, the method for producing a high-carbon stainless steel sheet, which comprises performing a two-step annealing treatment.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP16981695A JPH0920923A (en) | 1995-07-05 | 1995-07-05 | Production of high carbon stainless steel plate |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP16981695A JPH0920923A (en) | 1995-07-05 | 1995-07-05 | Production of high carbon stainless steel plate |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH0920923A true JPH0920923A (en) | 1997-01-21 |
Family
ID=15893440
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP16981695A Pending JPH0920923A (en) | 1995-07-05 | 1995-07-05 | Production of high carbon stainless steel plate |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0920923A (en) |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2011514438A (en) * | 2008-01-31 | 2011-05-06 | デュモント スイッツァランド アクチェンゲゼルシャフト | Single cylinder type thrust rolling method, apparatus for the single cylinder type thrust rolling method, and products manufactured using the single cylinder type thrust rolling method |
| WO2013047237A1 (en) * | 2011-09-26 | 2013-04-04 | 日立金属株式会社 | Stainless steel for cutlery and manufacturing process therefor |
| JP2014070229A (en) * | 2012-09-27 | 2014-04-21 | Hitachi Metals Ltd | Manufacturing method of band steel for blade |
| WO2014156806A1 (en) * | 2013-03-25 | 2014-10-02 | 日立金属株式会社 | Intermediate material for stainless steel for knives |
| WO2018212155A1 (en) * | 2017-05-18 | 2018-11-22 | 日立金属株式会社 | Method for manufacturing steel strip for blade, and steel strip for blade |
-
1995
- 1995-07-05 JP JP16981695A patent/JPH0920923A/en active Pending
Cited By (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2011514438A (en) * | 2008-01-31 | 2011-05-06 | デュモント スイッツァランド アクチェンゲゼルシャフト | Single cylinder type thrust rolling method, apparatus for the single cylinder type thrust rolling method, and products manufactured using the single cylinder type thrust rolling method |
| WO2013047237A1 (en) * | 2011-09-26 | 2013-04-04 | 日立金属株式会社 | Stainless steel for cutlery and manufacturing process therefor |
| JP5333695B1 (en) * | 2011-09-26 | 2013-11-06 | 日立金属株式会社 | Stainless steel for blades and method for producing the same |
| CN103827339A (en) * | 2011-09-26 | 2014-05-28 | 日立金属株式会社 | Stainless steel for cutlery and manufacturing process therefor |
| CN103827339B (en) * | 2011-09-26 | 2015-04-01 | 日立金属株式会社 | Stainless steel for cutlery and manufacturing process therefor |
| JP2014070229A (en) * | 2012-09-27 | 2014-04-21 | Hitachi Metals Ltd | Manufacturing method of band steel for blade |
| WO2014156806A1 (en) * | 2013-03-25 | 2014-10-02 | 日立金属株式会社 | Intermediate material for stainless steel for knives |
| CN104838031A (en) * | 2013-03-25 | 2015-08-12 | 日立金属株式会社 | Intermediate material for stainless steel for knives |
| WO2018212155A1 (en) * | 2017-05-18 | 2018-11-22 | 日立金属株式会社 | Method for manufacturing steel strip for blade, and steel strip for blade |
| JPWO2018212155A1 (en) * | 2017-05-18 | 2020-03-26 | 日立金属株式会社 | Method of manufacturing steel strip for blade and steel strip for blade |
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