JP2001335880A - Steel for heat treatment suitable for working in subhot temperature region - Google Patents
Steel for heat treatment suitable for working in subhot temperature regionInfo
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- JP2001335880A JP2001335880A JP2000159815A JP2000159815A JP2001335880A JP 2001335880 A JP2001335880 A JP 2001335880A JP 2000159815 A JP2000159815 A JP 2000159815A JP 2000159815 A JP2000159815 A JP 2000159815A JP 2001335880 A JP2001335880 A JP 2001335880A
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Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、高速プレスによる
鍛造、特に７００〜１０００℃での亜熱間領域での鍛造
において鍛造割れを起こすことのない加工性に優れた焼
入れ・焼戻しなどの調質処理を必要とする調質用鋼に関
するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to tempering such as quenching and tempering which is excellent in workability without causing forging cracks in forging by high-speed pressing, particularly in forging in a sub-hot region at 700 to 1000.degree. It relates to tempering steel that requires treatment.
【０００２】[0002]
【従来の技術】近年熱間鍛造において、鍛造スピード向
上を目的として従来の縦型プレスに代えて高速プレスす
なわち高速横型プレスの採用が広まっている。そして、
これらの高速プレスでは、高位の生産性を保つために従
来のプレスに比べて、例えば、冷却能の高い離型剤を使
用するなどして、金型冷却を徹底的に行っている。この
結果、鍛造温度は７００〜１０００℃の亜熱間で行われ
ている。2. Description of the Related Art In recent years, in hot forging, a high-speed press, that is, a high-speed horizontal press has been widely used in place of a conventional vertical press in order to improve forging speed. And
In these high-speed presses, in order to maintain high productivity, mold cooling is thoroughly performed by using, for example, a release agent having a higher cooling ability than conventional presses. As a result, the forging is performed at a subheat of 700 to 1000 ° C.
【０００３】ところで、鍛造では必ずといっていいほど
金型同志のクリアランスがあり、従ってバリが発生す
る。そして高速プレスでは、上記のとおり金型冷却が徹
底されているので、発生したバリが急激に冷却されるた
めに変形能が悪くなり、このため鍛造割れが発生する傾
向がある。さらに鋼材は鍛造温度が、例えば７００〜１
０００℃の亜熱間などのように、低くなればなるほど変
形能が低下することも良く知られている事柄である。[0003] By the way, in forging, there is almost always a clearance between molds, and thus burrs are generated. In the high-speed press, since the mold is thoroughly cooled as described above, the generated burrs are rapidly cooled, so that the deformability is deteriorated, and forging cracks tend to occur. Further, the steel material has a forging temperature of, for example, 700 to 1
It is also a well-known fact that the lower the temperature, the lower the deformability, such as a sub-hot temperature of 000 ° C.
【０００４】上記の鍛造割れを低減する方法として、
（１）金型のクリアランスからバリを出さないようにす
ること、（２）７００〜１０００℃の亜熱間領域で鍛造
割れを起こさない鋼材の使用が考えられるが、（１）の
ためには金型のクリアランスをゼロにする必要がある
が、金型のクリアランスをゼロにすることは現実的には
不可能である。（２）に適する鋼材はいまだ開発されて
いない。As a method of reducing the forging cracks described above,
(1) Preventing burrs from being produced from the clearance of the mold, (2) Use of a steel material that does not cause forging cracks in a sub-hot region of 700 to 1000 ° C. is considered. It is necessary to make the clearance of the mold zero, but it is practically impossible to make the clearance of the mold zero. Steel materials suitable for (2) have not yet been developed.
【０００５】そこで、本発明者等はこのような７００〜
１０００℃の亜熱間領域での鍛造などの加工をする際
に、加工による割れ、例えば鍛造割れを起こさない鋼の
うち非調質鋼材に係る発明の出願を既にしている。Therefore, the present inventors have proposed such a 700-
An application has been filed for an invention relating to a non-heat-treated steel material among steels that do not cause cracking due to working, for example, forging cracking when working such as forging in a sub-hot region at 1000 ° C.
【０００６】[0006]
【発明が解決しようとする課題】本発明が解決しようと
する課題は、７００〜１０００℃の亜熱間領域での鍛造
などの加工において、加工による割れ、例えば鍛造割れ
を起こさない調質用鋼材を提供することである。An object of the present invention is to provide a steel material for refining which does not cause cracks due to working, for example, forging cracks in working such as forging in a sub-hot range of 700 to 1000 ° C. It is to provide.
【０００７】[0007]
【課題を解決するための手段】発明者らは鍛造割れの要
因を追求したところ、それは（１）鋼材自信の変形能に
起因するものと、（２）鋼材中の介在物を起点とした割
れに起因するものとにある。そして、割れに対する影響
は特に後者の（２）の影響が大きいことを知見した。と
ころで介在物には硫化物系介在物や酸化物系介在物が知
られているが、前者は切削性を改善させるものであり、
また後者に比べ変形能が高いことも知られていることか
ら、鍛造割れを改善するには後者を低減させることが有
効な手段と考えた。Means for Solving the Problems The inventors of the present invention pursued the factors of forging cracks, and found that (1) those caused by the deformability of the steel itself and (2) cracks originating from inclusions in the steel. It is due to. Then, it was found that the influence of the latter (2) was particularly large on the effect on cracking. By the way, sulfide-based inclusions and oxide-based inclusions are known as inclusions, but the former improves the machinability,
Since it is also known that the deformability is higher than the latter, it is considered that reducing the latter is an effective means to improve forging cracks.
【０００８】そこで、鋼材中に含有される酸素量を変化
させ、酸化物系介在物の大きさおよび数を変化させた表
１に示すＪＩＳ規格鋼のＳＣＭ４２０の鋼材を供試材と
し、８００〜１０００℃において８０％据え込みを実施
した際の側面の割れの有無を調査した。Therefore, the steel material of JIS standard steel SCM420 shown in Table 1 in which the amount of oxygen contained in the steel material is changed and the size and the number of the oxide-based inclusions are changed is used as a test material. The presence or absence of cracks on the side surface when 80% upsetting was performed at 1000 ° C. was examined.
【０００９】[0009]
【表１】 [Table 1]
【００１０】以上の結果を表２に示す。これらの実験の
結果から、酸素量１５ｐｐｍ以下、かつＡＳＴＭ−Ｄ法
におけるＤ系厚型（Ｈｅａｖｙ）の等級０．５が１０以
下であれば、鍛造割れの改善が認められることがわか
り、さらにその他のＪＩＳ規格鋼のＳＣ，ＳＣＲ，ＳＮ
Ｃ，ＳＮＣＭ，ＳＵＪおよびこれらの快削鋼成分を含有
する鋼でも同様の傾向が得られることを知見し、本発明
の調質鋼を開発した。The above results are shown in Table 2. From the results of these experiments, it was found that if the oxygen content was 15 ppm or less and the D-type thick type (Heavy) grade 0.5 in the ASTM-D method was 10 or less, improvement in forging cracking was observed. SC, SCR, SN of JIS standard steel
The inventors have found that the same tendency can be obtained with steels containing C, SNCM, SUJ and these free-cutting steel components, and developed the tempered steel of the present invention.
【００１１】[0011]
【表２】 [Table 2]
【００１２】そこで上記の課題を解決するための本発明
の手段は、請求項１の発明では、ＪＩＳ規格鋼のうち、
ステンレス鋼を除く、ＳＣ、ＳＣＲ、ＳＣＭ、ＳＮＣ
Ｍ、ＳＵＪおよびこれらの快削鋼の鋼成分からなり、か
つ、鋼成分に含まれる酸素量が質量割合で１５ｐｐｍ未
満、好ましくは１０ｐｐｍ以下であり、かつ、ＡＳＴＭ
−Ｄ法において、Ｄ系厚型（Ｈｅａｖｙ）の８μｍ以上
の酸化物系介在物の等級０．５が１０以下で、かつ、等
級１．０以上が０であることを特徴とする７００〜１０
００℃での亜熱間温度領域での加工に適した調質用鋼で
ある。Therefore, the means of the present invention for solving the above-mentioned problems is as follows.
Excluding stainless steel, SC, SCR, SCM, SNC
M, SUJ and the steel components of these free-cutting steels, and the amount of oxygen contained in the steel components is less than 15 ppm by mass, preferably 10 ppm or less, and ASTM
In the -D method, the oxide-based inclusions having a diameter of 8 μm or more of the D-type thick type (Heavy) have a grade of 0.5 or less and a grade of 1.0 or more and 0 of 700 to 10,
It is a tempering steel suitable for processing in the sub-hot temperature range of 00 ° C.
【００１３】請求項２の発明では、質量割合で、Ｃ：
０．１〜０．６％、Ｓｉ：０．０５〜２．００％、Ｍ
ｎ：０．３〜２．５％、Ｓ：≦０．１５％、Ｃｒ：≦
２．０％、Ｍｏ：≦１．０％、Ｖ：≦０．５０％を含有
し、残部がＦｅおよび不可避不純物である鋼成分からな
り、かつ、鋼中に含まれる全酸素量が質量割合で１５ｐ
ｐｍ未満、好ましくは１０ｐｐｍ以下であり、かつ、Ａ
ＳＴＭ−Ｄ法においてＤ系厚型（Ｈｅａｖｙ）の８μｍ
以上の酸化物系介在物の等級０．５が１０以下で、か
つ、等級１．０以上が０であることを特徴とする７００
〜１０００℃での亜熱間温度領域での加工に適した調質
用鋼である。According to the second aspect of the present invention, C:
0.1-0.6%, Si: 0.05-2.00%, M
n: 0.3 to 2.5%, S: ≤ 0.15%, Cr: ≤
2.0%, Mo: ≦ 1.0%, V: ≦ 0.50%, the balance being Fe and steel components which are unavoidable impurities, and the total oxygen content in the steel is the mass ratio 15p
pm, preferably 10 ppm or less, and A
8 μm of D type thick type (Heavy) in STM-D method
700 wherein the oxide inclusions have a grade of 0.5 or less and a grade of 1.0 or more and 0.
It is a tempering steel suitable for processing in the sub-hot temperature range of up to 1000 ° C.
【００１４】ここで、ＡＳＴＭ−Ｄ法の介在物の等級付
けについて説明する。表３に示すようにＡＳＴＭ−Ｄ法
は介在物の幅を薄型（Ｔｈｉｎ）と厚型（Ｈｅａｖｙ）
に区別し、ＡないしＣ系介在物では１視野中に確認され
る介在物の総長さにより等級付けし、Ｄ系酸化物系介在
物では１視野中に確認される介在物の数によって等級付
けする。これは顕微鏡にて確認される視野において、表
４に示す等級付けを行い、視野が重ならないようにして
総視野面積１８０．５ｍｍ2で評価するものである。Here, the grading of inclusions in the ASTM-D method will be described. As shown in Table 3, in the ASTM-D method, the width of the inclusion is reduced to a thin type (Thin) and a thick type (Heavy).
A-C inclusions are graded according to the total length of inclusions observed in one visual field, and D-based oxide inclusions are graded according to the number of inclusions observed in one visual field. In the visual field confirmed with a microscope, the grading shown in Table 4 is performed, and the visual field is evaluated with a total visual field area of 180.5 mm 2 without overlapping.
【００１５】[0015]
【表３】 [Table 3]
【００１６】[0016]
【表４】 [Table 4]
【００１７】次いで、本発明における鋼成分について説
明する。なお鋼成分における％は質量％で示している。 Ｃ：０．１〜０．６％ Ｃは、パーライト量を増大させて鍛造品の強度を高める
のに必須の元素であり、少なくとも０．１％を必要とす
る。しかし、０．６％を超えて存在すると靱性を低下さ
せ加工性が悪くなるので、０．１〜０．６％とする。Next, the steel composition in the present invention will be described. In addition,% in the steel component is shown by mass%. C: 0.1 to 0.6% C is an element essential for increasing the amount of pearlite and increasing the strength of a forged product, and requires at least 0.1%. However, if the content exceeds 0.6%, the toughness is reduced and the workability is deteriorated.
【００１８】Ｓｉ：０．０５〜２．００％ Ｓｉは、溶製時の脱酸剤であるが、鍛造、放冷後のフェ
ライトを強化する元素であり、少なすぎるとその効果が
なく、Ｓｉの過度の含有は靱性および靱性を劣化するの
で、０．０５〜２．００％以下とする。Si: 0.05-2.00% Si is a deoxidizing agent at the time of smelting, but is an element that strengthens ferrite after forging and cooling, and if it is too small, it has no effect. Is excessive, the toughness and toughness are degraded, so the content is made 0.05 to 2.00% or less.
【００１９】Ｍｎ：０．３〜２．５ Ｍｎは、Ｓｉと同様に鋼の脱酸効果のため必然的に含有
するが、鍛造品の強度及び靱性を確保する元素である。
少なすぎるとその効果はなく、過度の含有は被削性を低
下させ、靱性を逆に低下させ加工性を劣化するので、
０．３〜２．５％以下とする。Mn: 0.3 to 2.5 Mn is inevitably contained for the deoxidizing effect of steel like Si, but is an element for ensuring the strength and toughness of a forged product.
If the content is too small, there is no effect, and excessive content lowers machinability, conversely lowers toughness and deteriorates workability,
0.3 to 2.5% or less.
【００２０】Ｓ：≦０．１５％ Ｓは、切削性を改善させる元素である。しかし、多すぎ
ると靱性が極度に低下し、疲労強度も低下するので、上
限を０．１５％とする。S: ≦ 0.15% S is an element that improves machinability. However, if the content is too large, the toughness is extremely reduced and the fatigue strength is also reduced. Therefore, the upper limit is set to 0.15%.
【００２１】Ｃｒ：≦２．０％ Ｃｒは、鍛造品の強度を増し、靱性を向上させる元素で
あるが、多すぎると疲労強度と靱性を低下させるので上
限を２．０％とする。Cr: ≦ 2.0% Cr is an element that increases the strength of a forged product and improves toughness. However, if the content is too large, the fatigue strength and toughness are reduced, so the upper limit is made 2.0%.
【００２２】Ｍｏ：≦１．０％ Ｍｏは、Ｃｒと同様に焼入性確保し鍛造品の強度を増す
ために必要な元素であるが多すぎるとその効果は飽和
し、コストを増大するので、上限を１．０％とする。Mo: ≦ 1.0% Mo is an element necessary for securing hardenability and increasing the strength of a forged product as in the case of Cr. However, if too much, the effect is saturated and the cost increases. , And the upper limit is 1.0%.
【００２３】Ｖ：≦０．５０％ Ｖは、鋼中に固溶し、調質時の焼戻し時に炭窒化物を析
出して強度および靱性を確保するのに必要な元素である
が、多すぎると効果は飽和し、コストアップとなるので
上限を０．５０％とする。V: ≤0.50% V is an element necessary for ensuring solid strength and toughness by forming a solid solution in steel and precipitating carbonitride during tempering at the time of tempering. The effect is saturated and the cost increases, so the upper limit is made 0.50%.
【００２４】Ｏ：１５ｐｐｍ未満、好ましくは１０ｐｐ
ｍ以下O: less than 15 ppm, preferably 10 pp
m or less
【００２５】本発明では、鋼中の全酸素量を１５ｐｐｍ
未満、好ましくは１０ｐｐｍ以下として酸化物系介在物
を極限まで低下させるものであり、かくすることにより
亜熱間温度領域での脆性割れを防止する。即ち、ＡＳＴ
Ｍ−Ｄ法において、Ｄ系厚型（Ｈｅａｖｙ）の８μｍ以
上の球状酸化物からなる酸化物系介在物の等級０．５が
１０以下で、かつ、等級１．０以上が０である調質用鋼
とする。In the present invention, the total oxygen content in steel is adjusted to 15 ppm
The content is less than 10 ppm, preferably less than 10 ppm, to reduce oxide-based inclusions to the utmost, thereby preventing brittle cracking in the sub-hot temperature range. That is, AST
In the MD method, the tempering of a D-type thick (Heavy) oxide-based inclusion composed of a spherical oxide of 8 μm or more having a grade of 0.5 or less and a grade of 1.0 or more being 0 is 0 or less. Steel.
【００２６】上記したとおり、硫化物系介在物は切削性
を改善させるものであり、また酸化物系介在物に比べ変
形能が高いので、鍛造割れを改善するには酸化物系介在
物を低減させることが有効な手段である。特に、亜熱間
領域での鍛造では、高い加工性を実現するためには、た
だ単にＯ量を低減することではなく、鋼中に存在するあ
る大きさ以上の酸化物系介在物の数を制限するものであ
る。As described above, sulfide-based inclusions improve the machinability and have higher deformability than oxide-based inclusions. This is an effective means. In particular, in forging in the sub-hot region, in order to achieve high workability, not only simply reduce the amount of O, but also limit the number of oxide-based inclusions having a certain size or more in the steel. Things.
【００２７】[0027]
【発明の実施の形態】本発明の実施の形態を、本発明に
係る鋼である開発鋼および比較例として比較鋼を対比し
て実施例を通じて説明する。本発明の開発鋼１〜３は電
気炉で溶製し、炉外精錬（ＬＦ）を行い、次いで脱ガス
（ＲＨ）を行って精錬した溶鋼を連続鋳造にてＪＩＳ規
格鋼Ｓ４５Ｃ鋳片を製造した。その際にＬＦ−ＲＨ時
間、耐火物の種類、鋳造温度を変化させることにより、
トータル酸素量および酸化物系介在物の大きさを表５に
示すようにコントロールした。DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS Embodiments of the present invention will be described through examples by comparing a developed steel which is a steel according to the present invention and a comparative steel as a comparative example. The developed steels 1 to 3 of the present invention are smelted in an electric furnace, subjected to out-of-furnace refining (LF), and then degassed (RH) to produce smelted steel by continuous casting to produce JIS standard steel S45C slabs. did. At that time, by changing the LF-RH time, the type of refractory, and the casting temperature,
The total oxygen content and the size of the oxide inclusions were controlled as shown in Table 5.
【００２８】[0028]
【表５】 [Table 5]
【００２９】[0029]
【実施例】上記で得られた鋼鋳片から分解圧延し、さら
にφ６０へ圧延して鍛造母材を製造した。この鍛造母材
を１０００℃にて加熱し、高速横型プレスにより図１に
示す（ａ）の母材から（ｂ）、（ｃ）、（ｄ）に示す形
状に３段からなるつば出し鍛造を行い製品（ｅ）とし
た。この鍛造では金型のクリアランスは一定にして行
い、そのときのバリ部１の割れの個数を観察した。バリ
部１における割れの個数の発生割合を％で表６に示す。
すなわち割れの発生割合は（割れの個数／試験数）×１
００である。なお、最終製品（ｅ）とする時のつば出し
部のバリ部１の温度は７００〜８００℃であった。EXAMPLE A steel slab obtained as described above was subjected to decomposition rolling, and further rolled to φ60 to produce a forged base material. The forged base material is heated at 1000 ° C., and a high-speed horizontal press is performed to form a three-stage forging from the base material shown in FIG. 1A into the shapes shown in (b), (c) and (d). The product (e) was obtained. In this forging, the mold clearance was kept constant, and the number of cracks in the burr portion 1 at that time was observed. Table 6 shows the occurrence ratio of the number of cracks in the burr portion 1 in%.
That is, the crack generation ratio is (number of cracks / number of tests) × 1
00. In addition, the temperature of the burr part 1 of the flange part when it was set as the final product (e) was 700-800 degreeC.
【００３０】[0030]
【表６】 [Table 6]
【００３１】表５に見られるとおり、本発明の開発鋼１
〜３と比較鋼１〜４の酸化物系介在物のＡＳＴＭ−Ｄ法
による等級番号及びＤ（Ｈｅａｖｙ）の数を示す。本発
明の開発鋼１はトータル酸素が１４ｐｐｍで、Ｄ系厚型
（Ｈｅａｖｙ）の等級０．５が７で等級１．０が０であ
り、開発鋼２はトータル酸素が１１ｐｐｍで、等級０．
５が３で、等級１．０が０であり、開発鋼３はトータル
酸素が７ｐｐｍで等級０．５が１で、等級１．０が０で
ある。これに対し比較鋼１はトータル酸素が２２ｐｐｍ
で、等級０．５が２５で、等級１．０が１であり、比較
鋼２はトータル酸素が１５ｐｐｍで、等級０．５が１５
で、等級１．０が０であり、比較鋼３はトータル酸素が
１４ｐｐｍで、等級０．５が９で、等級１．０が１であ
り、比較鋼４はトータル酸素が１１ｐｐｍで、等級０．
５が１２で、等級１．０が０である。As can be seen from Table 5, the developed steel 1 of the present invention
The grade number and the number of D (Heavy) by the ASTM-D method of the oxide-based inclusions of Comparative Steels Nos. 1 to 4 are shown. The developed steel 1 of the present invention has a total oxygen of 14 ppm, the grade of D type heavy type (Heavy) 0.5 is 7 and the grade 1.0 is 0, and the developed steel 2 has a total oxygen of 11 ppm and a grade of 0.1.
5 is 3, the grade 1.0 is 0, and the developed steel 3 has a total oxygen of 7 ppm, the grade 0.5 is 1, and the grade 1.0 is 0. In contrast, Comparative Steel 1 had a total oxygen content of 22 ppm.
The grade 0.5 was 25, the grade 1.0 was 1, and the comparative steel 2 had a total oxygen of 15 ppm and a grade of 0.5
The grade 1.0 is 0, the comparative steel 3 has a total oxygen of 14 ppm, the grade 0.5 is 9 and the grade 1.0 is 1, and the comparative steel 4 has a total oxygen of 11 ppm and a grade 0. .
5 is 12 and grade 1.0 is 0.
【００３２】表６に見られるとおり、本発明の開発鋼１
はバリ部の割れの発生割合が１９％であり、開発鋼２は
バリ部の割れの発生割合が１４％であり、開発鋼３はバ
リ部の割れの発生割合が７％であり、極めて少ない。こ
れに対し、比較鋼１は９７％、比較鋼２は８８％、比較
鋼３は７６％、比較鋼４は６６％全ての比較鋼で高い割
れ頻度を示した。As shown in Table 6, the developed steel 1 of the present invention
Indicates that the burr cracking rate is 19%, the developed steel 2 has a burr cracking rate of 14%, and the developed steel 3 has a burr cracking rate of 7%, which is extremely small. . On the other hand, the comparative steel 1 showed 97%, the comparative steel 2 88%, the comparative steel 3 76%, and the comparative steel 4 showed a high crack frequency in all comparative steels of 66%.
【００３３】上記の結果、酸素量１５ｐｐｍ以下、かつ
ＡＳＴＭ−Ｄ法におけるＤ（Ｈｅａｖｙ）の等級０．５
が１０以下であれば、７００℃〜１０００℃の鍛造割れ
が本発明の開発鋼が比較鋼に比して大幅に改善されてい
ることが認められる。なお、等級１．０以上を含む場合
は必然的に割れ頻度が高くなるのは容易に推察できる。As a result, the oxygen content was 15 ppm or less, and the D (Heavy) grade of the ASTM-D method was 0.5.
Is 10 or less, it is recognized that forging cracks at 700 ° C to 1000 ° C are significantly improved in the developed steel of the present invention as compared with the comparative steel. In addition, it can be easily inferred that the crack frequency is inevitably increased when the grade contains 1.0 or more.
【００３４】[0034]
【発明の効果】以上に説明したとおり、本発明は、鋼中
に含まれる全酸素量が質量割合で１５ｐｐｍ未満、好ま
しくは１０ｐｐｍ以下であり、かつ、ＡＳＴＭ−Ｄ法に
おいてＤ系厚型（Ｈｅａｖｙ）の８μｍ以上の酸化物系
介在物の等級０．５が１０以下で、かつ、等級１．０以
上が０である調質用鋼であるならば、７００℃〜１００
０℃の亜熱間領域での鍛造で、鍛造割れを起こす頻度が
極めて低いので、縦型プレスに比し金型冷却を徹底的に
行って高速プレスする高速横型プレスの７００℃〜１０
００℃の亜熱間領域での鍛造に適用でき、従って、自動
車のロアアームやハブなどの足回り部品その他の多種多
用の製品を高品位かつ高速で製造することができるな
ど、従来にない優れた効果を奏する。As described above, according to the present invention, the total oxygen content in steel is less than 15 ppm by mass, preferably 10 ppm or less by mass, and the D type thick type (Heavy) in the ASTM-D method. )) If the tempering steel has a grade of 0.5 or less and a grade of 1.0 or more of the oxide-based inclusions of 8 µm or more of 0 or more, 700 ° C to 100 ° C
Since the frequency of forging cracks in forging in the sub-hot range of 0 ° C is extremely low, 700 ° C to 10 ° C of a high-speed horizontal press that performs high-speed pressing by thoroughly cooling the die compared to a vertical press
It can be applied to forging in the sub-hot range of 00 ° C, and therefore can produce high-quality and high-speed products such as undercarriage parts such as lower arms and hubs of automobiles. It works.
【図１】本発明の開発鋼と比較鋼の７００〜１０００℃
での高速横型プレスによるつば出し鍛造におけるバリ部
の割れを模式的に示す図である。FIG. 1: 700-1000 ° C. of developed steel of the present invention and comparative steel
It is a figure which shows typically the crack of the burr | burr part in the forging by the high-speed horizontal type press in forging.
１ バリ部 1 Burr section
Claims (2)
ＳＮＣＭ、ＳＵＪおよびこれらの快削鋼の鋼成分からな
り、かつ、鋼中に含まれる全酸素量が質量割合で１５ｐ
ｐｍ未満であり、かつ、ＡＳＴＭ−Ｄ法においてＤ系厚
型（Ｈｅａｖｙ）の８μｍ以上の酸化物系介在物の等級
０．５が１０以下で、かつ、等級１．０以上が０である
ことを特徴とする７００〜１０００℃での亜熱間温度領
域での加工に適した調質用鋼。1. SC, SCR, SCM, JIS standard steel
It consists of SNCM, SUJ and the steel components of these free-cutting steels, and the total oxygen content in the steel is 15 p by mass.
less than pm, and in the ASTM-D method, grade 0.5 of oxide-based inclusions of 8 μm or more of D type thick type (Heavy) is 10 or less, and grade 1.0 or more is 0. A tempering steel suitable for processing in a sub-hot temperature range of 700 to 1000C.
ｉ：０．０５〜２．００％、Ｍｎ：０．３〜２．５％、
Ｓ：≦０．１５％、Ｃｒ：≦２．０％、Ｍｏ：≦１．０
％、Ｖ：≦０．５０％を含有し、残部がＦｅおよび不可
避不純物である鋼成分からなり、かつ、鋼中に含まれる
全酸素量が質量割合で１５ｐｐｍ未満であり、かつ、Ａ
ＳＴＭ−Ｄ法においてＤ系厚型（Ｈｅａｖｙ）の８μｍ
以上の酸化物系介在物の等級０．５が１０以下で、か
つ、等級１．０以上が０であることを特徴とする７００
〜１０００℃での亜熱間温度領域での加工に適した調質
用鋼。2. C: 0.1 to 0.6% by mass, S
i: 0.05 to 2.00%, Mn: 0.3 to 2.5%,
S: ≦ 0.15%, Cr: ≦ 2.0%, Mo: ≦ 1.0
%, V: ≦ 0.50%, the balance being Fe and a steel component that is an unavoidable impurity, the total oxygen content in the steel is less than 15 ppm by mass, and A
8 μm of D type thick type (Heavy) in STM-D method
700 wherein the oxide inclusions have a grade of 0.5 or less and a grade of 1.0 or more and 0.
Tempering steel suitable for processing in the sub-hot temperature range of ~ 1000 ° C.
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|---|---|---|---|
| JP2000159815A JP4135852B2 (en) | 2000-05-30 | 2000-05-30 | Tempering steel suitable for machining in sub-hot temperature range |
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2000159815A JP4135852B2 (en) | 2000-05-30 | 2000-05-30 | Tempering steel suitable for machining in sub-hot temperature range |
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| Publication Number | Publication Date |
|---|---|
| JP2001335880A true JP2001335880A (en) | 2001-12-04 |
| JP4135852B2 JP4135852B2 (en) | 2008-08-20 |
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Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| FR3055340A1 (en) * | 2014-06-10 | 2018-03-02 | Safran Aircraft Engines | PIECE IN LOW ALLOY STEEL |
-
2000
- 2000-05-30 JP JP2000159815A patent/JP4135852B2/en not_active Expired - Lifetime
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| FR3055340A1 (en) * | 2014-06-10 | 2018-03-02 | Safran Aircraft Engines | PIECE IN LOW ALLOY STEEL |
| US10364479B2 (en) | 2014-06-10 | 2019-07-30 | Safran Aircraft Engines | Method for producing a low-alloy steel ingot |
| US11560612B2 (en) | 2014-06-10 | 2023-01-24 | Safran Aircraft Engines | Method for producing a low-alloy steel ingot |
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| Publication number | Publication date |
|---|---|
| JP4135852B2 (en) | 2008-08-20 |
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