JPH07118793A - High carbon steel excellent in workability and hardenability - Google Patents
High carbon steel excellent in workability and hardenabilityInfo
- Publication number
- JPH07118793A JPH07118793A JP5266797A JP26679793A JPH07118793A JP H07118793 A JPH07118793 A JP H07118793A JP 5266797 A JP5266797 A JP 5266797A JP 26679793 A JP26679793 A JP 26679793A JP H07118793 A JPH07118793 A JP H07118793A
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- Prior art keywords
- steel
- less
- workability
- high carbon
- hardenability
- Prior art date
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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】本発明は例えば構造鋼、工具鋼、
自動車部品等に用いられる高炭素鋼に係り、優れた冷間
加工性と短時間均熱による焼入れ性を有する高炭素鋼に
関する。BACKGROUND OF THE INVENTION The present invention relates to structural steel, tool steel,
The present invention relates to high carbon steel used for automobile parts and the like, and relates to high carbon steel having excellent cold workability and hardenability by soaking for a short time.
【０００２】[0002]
【従来の技術】構造鋼、工具鋼、自動車部品等に用いら
れる高炭素鋼は、一般にユーザーで所定の冷間加工ある
いは打ち抜き加工を施されたのち、焼入れ処理により所
望の硬度に調整され使用される。しかし高炭素鋼の組織
は、熱延ままでは主として硬質で低加工性のパーライト
で構成されるため、熱延後あるいはさらに冷間圧延した
後にＡｃ1 変態点以下に１０〜４０時間程度保持し、パ
ーライトを球状化して加工性を付与した後出荷される。
一方、近年高炭素鋼を素材とする製品の熱処理コスト低
減を目的として、最終熱処理（焼入れ）を短時間化する
というユーザーニーズが高まっており、優れた冷間加工
性と短時間均熱による焼入れ性を有する高炭素鋼の開発
が切望されている。高炭素鋼の短時間均熱による焼入れ
性の向上に対しては、炭化物の粒径を小さくし、均熱時
にいかに短時間でオーステナイト中に炭素を溶解させる
かが肝要である。このような観点から、これまで炭化物
の粒径を１μｍ以下とする高炭素鋼に関して、熱延鋼帯
を冷圧率２０％以上で冷間圧延した後、４５０〜６５０
℃のバッチ焼鈍を行う方法（特公平１−２５８１２号公
報）、ベイナイトあるいは焼戻しマルテンサイト組織を
有する熱延鋼帯を１０％以上の冷圧率で冷間圧延した
後、Ａ1 変態点以下に３０〜６００秒保持する方法（特
開平２−２５９０１３号公報）などの発明が開示されて
いる。しかし、炭化物の粒径を小さくすると必然的に硬
度が上昇するため、これらの発明による高炭素鋼は加工
性においてユーザーニーズを満足するものではない。2. Description of the Related Art High carbon steels used for structural steels, tool steels, automobile parts, etc. are generally used after being subjected to a predetermined cold working or punching by a user and then adjusted to a desired hardness by quenching. It However, since the structure of the high carbon steel is mainly composed of hard and low workability pearlite in the as-hot-rolled state, the hot-rolled steel is kept at the Ac 1 transformation point or lower for 10 to 40 hours or so after hot rolling or cold rolling. It is shipped after making pearlite spherical and giving it workability.
On the other hand, in recent years, there is an increasing need for users to shorten the final heat treatment (quenching) for the purpose of reducing the heat treatment cost of products made from high carbon steel, and it has excellent cold workability and quenching by soaking for a short time. The development of high-carbon steel with properties has been earnestly desired. In order to improve the hardenability of high-carbon steel by soaking for a short time, it is important to reduce the grain size of the carbide and dissolve the carbon in austenite in a short time during soaking. From such a viewpoint, regarding high carbon steel having a carbide grain size of 1 μm or less, a hot-rolled steel strip is cold-rolled at a cold rolling ratio of 20% or more and then 450 to 650.
Method of carrying out batch annealing at ℃ (Japanese Patent Publication No. 1-25812), hot-rolled steel strip having bainite or tempered martensite structure is cold-rolled at a cold pressure ratio of 10% or more, and then to A 1 transformation point or less. Inventions such as a method of holding for 30 to 600 seconds (JP-A-2-259013) are disclosed. However, since the hardness inevitably increases as the grain size of carbides decreases, the high carbon steels according to these inventions do not satisfy the needs of users in terms of workability.
【０００３】[0003]
【発明が解決しようとする課題】本発明は上記のように
高炭素鋼に要求される相反する二つの特性としての優れ
た加工性と短時間均熱による焼入れ性を同時に満足させ
る。すなわち、加工時には軟質でありながら短時間均熱
による焼入れ処理後には所定の硬さが得られる高炭素鋼
を提供することを目的とするものである。As described above, the present invention simultaneously satisfies excellent workability and hardenability by short-time soaking, which are two contradictory characteristics required for high carbon steel. That is, it is an object of the present invention to provide a high-carbon steel that is soft during processing and that has a predetermined hardness after quenching by soaking for a short time.
【０００４】[0004]
【課題を解決するための手段】本発明者らは、上記の課
題を解決するため、高炭素鋼の加工性と短時間均熱によ
る焼入れ性に対してこれまで検討されてきた炭化物の粒
径のみならず、パーライト相、ベイナイト相、残留オー
ステナイト相の体積率をも考慮して鋭意検討した結果、
ポリゴナルフェライト相に平均粒径４μｍ以下の炭化物
が分散した組織を主体として、一部を体積率３〜２０％
の残留オーステナイトと体積率１５％以下のパーライト
とベイナイトで置換することにより、優れた加工性と短
時間均熱による焼入れ性が得られることを見いだした。
すなわち本発明は、重量％でＣ：０．３〜１．３％、Ｓ
ｉ：１％以下、Ｍｎ：０．１〜１％、Ｐ：０，０２％以
下、sol.Ａｌ：０．０５％以下、Ｎ：０．０２５％以下
を含有し、残部Ｆｅおよび不可避不純物からなる鋼で、
下記を満足するものである。 Ｖ（Ｐ）＋Ｖ（Ｂ）≦１５％、 Ｖ（γ）：３〜２０％、 残部：ポリゴナルフェライト＋平均粒径４μｍ以下の炭
化物 ただし、Ｖ（Ｐ）はパーライト体積率、Ｖ（Ｂ）はベイ
ナイト体積率、Ｖ（γ）は残留オーステナイト体積率で
ある。In order to solve the above problems, the inventors of the present invention have studied the grain size of carbides which have been studied so far with respect to the workability of high carbon steel and the hardenability by short-time soaking. In addition to the pearlite phase, the bainite phase, and the retained austenite phase, the volume ratio of the materials was also taken into consideration.
Mainly composed of a structure in which a carbide having an average particle size of 4 μm or less is dispersed in a polygonal ferrite phase, and a part of the volume ratio is 3 to 20%.
It was found that excellent workability and hardenability by soaking for a short time can be obtained by substituting the retained austenite of No. 1 with pearlite and bainite having a volume ratio of 15% or less.
That is, in the present invention, C: 0.3 to 1.3% by weight%, S
i: 1% or less, Mn: 0.1 to 1%, P: 0.02% or less, sol.Al: 0.05% or less, N: 0.025% or less, and the balance Fe and unavoidable impurities With steel,
The following is satisfied. V (P) + V (B) ≦ 15%, V (γ): 3 to 20%, balance: Polygonal ferrite + carbide having an average particle size of 4 μm or less, where V (P) is pearlite volume ratio, V (B) Is the bainite volume ratio, and V (γ) is the residual austenite volume ratio.
【０００５】[0005]
【作用】本発明に係る加工性と焼入れ性に優れた高炭素
鋼が、加工時には軟質でありながら短時間均熱による焼
入れ処理後には所定の硬さが得られるものであることに
ついて以下に説明する。先ず、本発明鋼の成分量（重量
％）の限定理由について説明する。 Ｃ：０．３〜１．３％ Ｃ添加量は焼入れ後の硬さに最も影響するため、目的と
する硬さに応じて添加するが、０．３％未満では効果が
微弱であり、１．３％を超えて過剰に添加しても、硬さ
が飽和するばかりか鋼の加工性も低下する。 Ｓｉ：１％以下 Ｓｉは１％を超えて添加すると表面性状が劣化するとと
もにフェライト相が硬質化し、加工性が劣化し好ましく
ない。 Ｍｎ：０．１〜１％ Ｍｎは鋼の焼入れ性を向上させる廉価な元素で、本発明
鋼においては必要不可欠である。下限の０．１％は焼入
れ性の確保に必要な最低限量で、上限の１％はこれを超
えて添加しても効果が飽和するばかりか、鋼が硬質化し
て加工性が劣化する。 Ｐ：０．０２％以下 Ｐは鋼を脆化させる元素であり、０．０２％以下に規定
する。 Ｓ：０．０１％以下 Ｓは添加量が増加すると圧延方向に伸びた介在物（Ｍｎ
Ｓ）が増加して、加工性を劣化させるため０．０１以下
に規定する。 sol.Ａｌ：０．０５％以下 Ａｌは鋼の脱酸に用いられる元素であるが、sol.Ａｌで
０．０５％を超えると表面疵が増加し好ましくないので
０．０５％以下に規定する。 Ｎ：０．０２５％以下 Ｎは含有量が多いと鋼を硬質化するため０．０２５％以
下に規定する。その他、本願発明の目的のため、あるい
は他の目的を付加するために、０．１％以下のＮｂ，Ｔ
ｉ、０．３％以下のＶ、０．００３％以下のＢ、０．０
２％以下のＳｎ、あるいはＪＩＳ規格のＳＣＲ，ＳＮ
Ｃ，ＳＮＣＭなどのように０．５％以下のＣｕ，Ｍｏ，
Ｉ、１．５％以下のＣｒ、３％以下のＮｉなどの元素を
添加することも本願発明の範囲内で、本発明の効果を損
なわない。The following is a description of the fact that the high carbon steel according to the present invention, which is excellent in workability and hardenability, is soft at the time of working but can obtain a predetermined hardness after quenching treatment by soaking for a short time. To do. First, the reason for limiting the component amount (% by weight) of the steel of the present invention will be described. C: 0.3 to 1.3% Since the amount of C added most affects the hardness after quenching, it is added according to the desired hardness, but if it is less than 0.3%, the effect is weak and 1 Even if added in excess of 0.3%, not only the hardness is saturated but also the workability of the steel is deteriorated. Si: 1% or less If Si is added in an amount of more than 1%, the surface properties are deteriorated, the ferrite phase is hardened, and the workability is deteriorated, which is not preferable. Mn: 0.1 to 1% Mn is an inexpensive element that improves the hardenability of steel, and is essential in the steel of the present invention. The lower limit of 0.1% is the minimum amount necessary to ensure hardenability, and the upper limit of 1% not only saturates the effect even if added in excess, but also hardens the steel and deteriorates the workability. P: 0.02% or less P is an element that embrittles steel and is specified to be 0.02% or less. S: 0.01% or less S is an inclusion (Mn that extends in the rolling direction when the addition amount increases).
Since S) increases and the workability deteriorates, it is specified to be 0.01 or less. sol.Al: 0.05% or less Al is an element used for deoxidation of steel, but if sol.Al exceeds 0.05%, surface defects increase and it is not preferable, so it is specified to be 0.05% or less. . N: 0.025% or less N is specified to 0.025% or less because if the content is large, the steel is hardened. In addition, for the purpose of the present invention or to add other purposes, Nb, T of 0.1% or less is used.
i, V of 0.3% or less, B of 0.003% or less, 0.0
2% or less Sn or JIS standard SCR, SN
C, SNCM, etc., 0.5% or less of Cu, Mo,
It is within the scope of the present invention to add elements such as I, 1.5% or less of Cr, and 3% or less of Ni without impairing the effects of the present invention.
【０００６】次に本発明の組織限定理由について説明す
る。本発明では炭化物の一部をパーライト、ベイナイ
ト、残留オーステナイトで置換させることが重要で、組
織を以下のように限定する。 Ｖ（Ｐ）＋Ｖ（Ｂ）≦１５％、 Ｖ（γ）：３〜２０％、 残部：ポリゴナルフェライト＋平均粒径４μｍ以下の炭
化物 ただし、Ｖ（Ｐ）はパーライト体積率、Ｖ（Ｂ）はベイ
ナイト体積率、Ｖ（γ）は残留オーステナイト体積率で
ある。主体となる組織は、平均粒径４μｍ以下の炭化物
が分散したポリゴナルフェライト組織であるが、これは
未再結晶フェライトでは硬質で加工性が劣るためで、ま
た炭化物の平均粒径が４μｍを超えると短時間加熱での
焼入れ性が著しく劣化するためである。しかし炭化物が
微細になりすぎると鋼が硬質化するので、平均粒径を
０．５μｍ以上とすることが好ましい。また加工性の観
点から炭化物は球状であることが望ましいが、針状炭化
物が存在するのを許容する。なお針状炭化物の粒径換算
は、（長さ＋幅）÷２と定義する。炭化物の１部をパー
ライト、ベイナイト、残留オーステナイトで置換させる
のは、これらの組織が炭化物よりも短時間の均熱でオー
ステナイトに変態するためであるが、この中でも残留オ
ーステナイトを含有させることは本発明において非常に
重要となる。これは残留オーステナイトがセメンタイト
に比べ軟質であるためで、これを含有させることによ
り、全面炭化物組織よりも軟質で加工性が良好な材質が
得られる。また複雑な形状に成形する場合にはＴＲＩＰ
（変態誘起塑性）が生じてより加工性が向上することも
好ましい点である。このような理由により残留オーステ
ナイトを体積率で３〜２０％含有させる。下限は所望の
考課が得られる最低限度で、上限はこれを超えると加工
時にＴＲＩＰによる加工硬化が著しくなり好ましくない
ので規定する。またパーライトとベイナイトが増加する
と、鋼が硬質化して加工性が劣化するため体積率の合計
を１５％以下に規定する。このように組織を限定する範
囲に制御することにより、加工性と短時間均熱による焼
入れ性の優れた高炭素鋼を得ることができる。Next, the reasons for limiting the structure of the present invention will be described. In the present invention, it is important to partially replace the carbide with pearlite, bainite, and retained austenite, and the structure is limited as follows. V (P) + V (B) ≦ 15%, V (γ): 3 to 20%, balance: Polygonal ferrite + carbide having an average particle size of 4 μm or less, where V (P) is pearlite volume ratio, V (B) Is the bainite volume ratio, and V (γ) is the residual austenite volume ratio. The main structure is a polygonal ferrite structure in which carbides having an average particle size of 4 μm or less are dispersed. This is because unrecrystallized ferrite is hard and inferior in workability, and the average particle size of carbides exceeds 4 μm. This is because the hardenability after heating for a short period of time significantly deteriorates. However, if the carbide becomes too fine, the steel becomes hard, so it is preferable to set the average grain size to 0.5 μm or more. From the viewpoint of workability, it is desirable that the carbide be spherical, but needle carbide is allowed to exist. The particle size conversion of needle-shaped carbide is defined as (length + width) / 2. The reason why a part of the carbide is replaced with pearlite, bainite, and retained austenite is that these structures are transformed into austenite by soaking in a shorter time than that of the carbide. Is very important in. This is because the retained austenite is softer than the cementite, and by containing it, a material softer than the entire surface carbide structure and having good workability can be obtained. In addition, TRIP is used for molding into complicated shapes.
It is also a preferable point that (transformation-induced plasticity) occurs and workability is further improved. For this reason, the retained austenite is contained in a volume ratio of 3 to 20%. The lower limit is the minimum limit at which the desired evaluation can be obtained, and the upper limit is defined because work hardening due to TRIP during processing is unfavorable if the upper limit is exceeded, which is not preferable. Further, if the amount of pearlite and bainite increases, the steel becomes hard and the workability deteriorates, so the total volume ratio is specified to be 15% or less. By controlling the microstructure in such a range as described above, it is possible to obtain a high carbon steel excellent in workability and hardenability by soaking for a short time.
【０００７】[0007]
実施例１．表１に示す成分の鋼を転炉で出鋼した後、熱
間圧延においてＡｒ3 変態点以上で仕上げ、６５０〜３
００℃の種々の温度で巻き取った熱延板を酸洗し、１部
は６００〜７００℃で１０〜４０時間の中間焼鈍を施し
た後、０〜６０％の冷圧率で冷間圧延し、その後、表２
に示す条件でバッチ焼鈍あるいはロール冷却設備を有す
る連続焼鈍設備にて連続焼鈍し、炭化物の平均粒径、パ
ーライト、ベイナイト、残留オーステナイトの体積率を
種々変化させた鋼板を製造した。図１はこれらの鋼板に
ついて、板面硬度（ＨRB）と短時間均熱後（８５０℃×
１０sec ）に油焼入れしたときの板面硬度（ＨRC）に及
ぼす組織の影響を示したものである。図１から明らかな
ように、組織を本発明範囲内に制御することにより、Ｃ
＝０．８３％という高炭素鋼でありながら、焼鈍板の硬
度（ＨRB）が７９〜８４と低いにもかかわらず、８５０
℃×１０sec 均熱後の油焼入れ時の板面硬度（ＨRC）が
６２という高い値が得られ、加工性と短時間焼入れ性が
優れた高炭素鋼が得られた。Example 1. After the steel having the components shown in Table 1 was tapped in a converter, it was finished by hot rolling at a transformation point of Ar 3 or higher, and then 650 to 3
The hot-rolled sheet wound at various temperatures of 00 ° C is pickled, one part is subjected to intermediate annealing at 600 to 700 ° C for 10 to 40 hours, and then cold rolled at a cold pressure ratio of 0 to 60%. And then Table 2
Under the conditions shown in (1), batch annealing or continuous annealing in a continuous annealing equipment having a roll cooling equipment was performed to manufacture steel sheets in which the average grain size of carbides, pearlite, bainite, and volume ratio of retained austenite were variously changed. Figure 1 shows the hardness of these steel sheets (H RB ) and after soaking for a short time (850 ° C x
10 shows the influence of the structure on the plate surface hardness (H RC ) when oil-quenched for 10 seconds). As is clear from FIG. 1, by controlling the tissue within the scope of the present invention, C
= Yet high carbon steel as 0.83%, even though the hardness of the annealed steel sheet (H RB) is low and 79-84, 850
The plate surface hardness (H RC ) at the time of oil quenching after soaking at ℃ × 10 sec was as high as 62, and high carbon steel excellent in workability and short-time quenchability was obtained.
【０００８】[0008]
【表１】 [Table 1]
【０００９】[0009]
【表２】 [Table 2]
【００１０】実施例２．表３に示す種々の成分の鋼を転
炉にて出鋼し、仕上げ温度Ａｒ3 点以上で熱延した後、
４００〜６００℃で巻き取った熱延板を準備し、一部は
６００〜７００℃で１０〜４０時間の中間焼鈍を行った
後、冷間圧延し、ロール冷却設備を有する連続焼鈍設備
にて表４に示す条件で焼鈍した。これらの焼鈍板の組
織、板面硬度（ＨRB）と短時間均熱後（８５０℃×１０
sec)に油焼入れしたときの板面硬度（ＨRC) を表４に併
せて示す。表４から明らかなように、例えば鋼 No.４，
５，１０，１１などのように、組織が本発明範囲外であ
る鋼は軟質でかつ短時間焼入れ性が優れているのがわか
る。Embodiment 2. After steel with various components shown in Table 3 was tapped in a converter and hot rolled at a finishing temperature Ar 3 or higher,
A hot-rolled sheet wound at 400 to 600 ° C is prepared, part of which is subjected to intermediate annealing at 600 to 700 ° C for 10 to 40 hours, then cold rolled, and then in a continuous annealing facility having a roll cooling facility. Annealing was performed under the conditions shown in Table 4. Microstructure of these annealed plates, plate surface hardness ( HRB ) and after soaking for a short time (850 ° C x 10
Table 4 also shows the plate hardness (H RC ) when oil-quenched for sec). As is clear from Table 4, for example, steel No. 4,
It can be seen that steels having structures outside the scope of the present invention, such as Nos. 5, 10, and 11, are soft and have excellent short-time hardenability.
【００１１】[0011]
【表３】 [Table 3]
【００１２】[0012]
【表４】 [Table 4]
【００１３】[0013]
【発明の効果】以上のように本発明によれば、加工時に
は軟質で成形あるいは打ち抜き性が優れる一方で、その
後の焼入れ処理においては、短時間の均熱で焼入れが完
了できるという優れた高炭素鋼が得られる。したがって
本発明は高炭素鋼の適用範囲の拡大あるいは製品コスト
の低減に大きく貢献するもので、工業的意義の大きいも
のである。As described above, according to the present invention, while being soft during processing, it is excellent in moldability or punchability, but in the subsequent quenching treatment, it is possible to complete quenching by soaking in a short period of time. Steel is obtained. Therefore, the present invention greatly contributes to the expansion of the range of application of high carbon steel or the reduction of product cost, and has great industrial significance.
【図１】本発明の加工性と焼入れ性に優れた高炭素鋼の
一実施例に係る加工性と短時間焼入れ性に及ぼす鋼組織
の影響を示す図である。FIG. 1 is a diagram showing an influence of a steel structure on workability and short-time hardenability according to an embodiment of the high carbon steel excellent in workability and hardenability of the present invention.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 大北 智良 東京都千代田区丸の内一丁目１番２号 日 本鋼管株式会社内 ─────────────────────────────────────────────────── ─── Continuation of the front page (72) Inventor Tomoyoshi Okita 1-2-1, Marunouchi, Chiyoda-ku, Tokyo Nihon Steel Pipe Co., Ltd.
Claims (1)
１％以下、Ｍｎ：０．１〜１％、Ｐ：０，０２％以下、
sol.Ａｌ：０．０５％以下、Ｎ：０．０２５％以下を含
有し、残部Ｆｅおよび不可避不純物からなる鋼で、下記
を満足することを特徴とする加工性と焼入れ性に優れた
高炭素鋼。 Ｖ（Ｐ）＋Ｖ（Ｂ）≦１５％、 Ｖ（γ）：３〜２０％、 残部：ポリゴナルフェライト＋平均粒径４μｍ以下の炭
化物 ただし、Ｖ（Ｐ）はパーライト体積率、Ｖ（Ｂ）はベイ
ナイト体積率、Ｖ（γ）は残留オーステナイト体積率で
ある。1. C: 0.3-1.3% by weight, Si:
1% or less, Mn: 0.1 to 1%, P: 0.02% or less,
sol.Al: 0.05% or less, N: 0.025% or less, a balance Fe and unavoidable impurities, high carbon with excellent workability and hardenability, characterized by satisfying the following: steel. V (P) + V (B) ≦ 15%, V (γ): 3 to 20%, balance: Polygonal ferrite + carbide having an average particle size of 4 μm or less, where V (P) is pearlite volume ratio, V (B) Is the bainite volume ratio, and V (γ) is the residual austenite volume ratio.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP5266797A JPH07118793A (en) | 1993-10-26 | 1993-10-26 | High carbon steel excellent in workability and hardenability |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP5266797A JPH07118793A (en) | 1993-10-26 | 1993-10-26 | High carbon steel excellent in workability and hardenability |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH07118793A true JPH07118793A (en) | 1995-05-09 |
Family
ID=17435823
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP5266797A Pending JPH07118793A (en) | 1993-10-26 | 1993-10-26 | High carbon steel excellent in workability and hardenability |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH07118793A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2016222990A (en) * | 2015-06-02 | 2016-12-28 | 新日鐵住金株式会社 | High carbon steel sheet and production method therefor |
-
1993
- 1993-10-26 JP JP5266797A patent/JPH07118793A/en active Pending
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2016222990A (en) * | 2015-06-02 | 2016-12-28 | 新日鐵住金株式会社 | High carbon steel sheet and production method therefor |
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