JPS61106715A - Manufacture of steel plate having superior carburizing property - Google Patents
Manufacture of steel plate having superior carburizing propertyInfo
- Publication number
- JPS61106715A JPS61106715A JP22590184A JP22590184A JPS61106715A JP S61106715 A JPS61106715 A JP S61106715A JP 22590184 A JP22590184 A JP 22590184A JP 22590184 A JP22590184 A JP 22590184A JP S61106715 A JPS61106715 A JP S61106715A
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- Prior art keywords
- steel
- austenite
- carburizing
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- temperature
- Prior art date
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Abstract
Description
【発明の詳細な説明】
（産業上の利用分野）
本発明は、浸炭特性のすぐれた熱間圧延鋼板の製造法に
関する．さらに詳述すれば、本発明は、熱間圧延鋼板を
球状化焼鈍してから冷間加工、特に打抜加工後、浸炭焼
入れ処理を行う際、浸炭期間中のオーステナイト結晶粒
の粗大化を防止する方法に関する。DETAILED DESCRIPTION OF THE INVENTION (Field of Industrial Application) The present invention relates to a method for producing hot rolled steel sheets with excellent carburizing properties. More specifically, the present invention prevents coarsening of austenite crystal grains during the carburizing period when a hot rolled steel plate is subjected to carburizing and quenching after spheroidizing annealing, cold working, especially punching. Regarding how to.
（従来の技術）
多くの機械部品、例えばギヤーやスプロケフト等の製造
工程においては、通常、精密打抜加工が用いられる．し
かし、一般に精密打抜加工に用いられる打抜型は高価で
ある．したがって、型寿命をできるだけ長くするため加
工用素材は軟質なものを選択して変形抵抗を少なくし、
一方、製品に必要な硬さ、強度は以後の浸炭焼入れ処理
にて補うことが行われている．いわゆる肌焼き鋼の使用
である．例えばＪＩＳ ＳＣｒ ＳＳＣＭ 、 ＳＮＣ
Ｎなどの肌焼きε４では、まず鋼中の炭化物を球状化し
軟質化する球状化焼鈍を行って変形抵抗を十分小さくし
てから精密打抜加工を行い所定の形状とし、次いで浸炭
、焼入れ処理を行って最終製品とする。(Prior Art) Precision punching is usually used in the manufacturing process of many mechanical parts, such as gears and sprockets. However, the punching dies used for precision punching are generally expensive. Therefore, in order to extend the life of the mold as much as possible, we select a soft material for processing to reduce deformation resistance.
On the other hand, the hardness and strength required for the product are supplemented by a subsequent carburizing and quenching process. This is the use of so-called case hardened steel. For example, JIS SCr SSCM, SNC
For case hardening ε4 such as N, first perform spheroidizing annealing to spheroidize and soften the carbides in the steel to sufficiently reduce deformation resistance, then perform precision punching to obtain the desired shape, and then carburize and quench. to produce the final product.
一方、圧延材に前処理として球状化焼鈍を行った場合、
後で行う浸炭処理時に非浸炭部（つまり、母材部）のオ
ーステナイト結晶粒が粗大化し、内部硬さを必要以上に
高めたり、焼入れ歪や靭性の低下を沼きやすいことはよ
く知られている。上記のオーステナイト結晶粒の粗大化
を防止する方法としては、Ａｌ、Ｎｉを規制する方法が
例えば特開昭５９−１２３７１４号に開示されている。On the other hand, when the rolled material is subjected to spheroidizing annealing as a pretreatment,
It is well known that the austenite grains in the non-carburized part (i.e., the base metal part) become coarse during the subsequent carburizing process, which increases the internal hardness more than necessary and tends to cause quenching distortion and a decrease in toughness. . As a method for preventing the above-mentioned coarsening of austenite crystal grains, a method of regulating Al and Ni is disclosed in, for example, Japanese Patent Laid-Open No. 123714/1982.
すなわち、熱間圧延に際しての加？、ｆＡ度、ならびに
Ａｌ／Ｎおよび（Ａｌ＋２Ｎ）の容置を規定して熱間圧
延後のＡｌＮ含有量を４０ ｐｐｓｓ以下に限定するこ
とにより浸炭処理期間中のオーステナイト結晶粒の粗大
化を阻止するのである。In other words, what about the addition during hot rolling? , fA degree, and the content of Al/N and (Al+2N) to prevent the coarsening of austenite grains during the carburizing process by limiting the AlN content after hot rolling to 40 ppss or less. It is.
しかし、本発明者らの研究結果によれば、熱間圧延鋼板
を素材とする場合には単にＡｌ、ＮＲを規制するだけで
はオーステナイト結晶粒の粗大化は防止できない。すな
わち、通常の熱間圧延条件下では、巻取時にＡｌＮはフ
ェライト粒界のみに析出し、次工程の球状化焼鈍時にＡ
ｌＮが粗大凝集化するため浸炭焼入れ時にオーステナイ
ト化すると、フェライト粒界から生成するオーステナイ
トには粒成長抑制効果を示すが、フェライト粒内から生
成するオーステナイトには何の抑ｖＩ効果を示さない、
したがって、粒内から生成したオーステナイトは容易に
粗大化してしまう、ＡｌＮより強いオーステナイト結晶
粒成長抑制効果を持つＴｉやＮｂの添加が必要となる。However, according to the research results of the present inventors, when a hot rolled steel plate is used as a material, coarsening of austenite crystal grains cannot be prevented simply by regulating Al and NR. That is, under normal hot rolling conditions, AlN precipitates only at the ferrite grain boundaries during coiling, and AlN precipitates only at the ferrite grain boundaries during the next process of spheroidizing annealing.
When IN is austenitized during carburizing and quenching due to coarse agglomeration, the austenite generated from the ferrite grain boundaries exhibits a grain growth inhibiting effect, but the austenite generated from within the ferrite grains does not exhibit any inhibitory effect.
Therefore, austenite generated from within the grains easily becomes coarse, and it is necessary to add Ti or Nb, which has a stronger effect of inhibiting austenite crystal grain growth than AlN.
しかし、これらの元素は高価であるとともに、母材の成
形性を著しく劣化させるという欠点を持つ。However, these elements are expensive and have the drawback of significantly deteriorating the formability of the base material.
（発明が解決しようとする問題点）
本発明の目的とするところは、上述のような問題点を特
殊な元素の添加を必要とせず、かつ通常の製造工程を大
幅に変えることなく解消する方法を提供することである
。(Problems to be Solved by the Invention) The purpose of the present invention is to provide a method for solving the above-mentioned problems without requiring the addition of special elements and without significantly changing the normal manufacturing process. The goal is to provide the following.
（問題点を解決するための手段）
本発明者らは、研究の結果、ＡｌとＮとの量を規制する
とともに、併せて熱間圧延条件を規制することで上述の
ような従来技術の問題点を一挙に解決することができる
ことを知り、本発明を完成した。(Means for Solving the Problems) As a result of research, the present inventors have solved the problems of the prior art as described above by regulating the amounts of Al and N and also regulating the hot rolling conditions. He realized that the problems could be solved all at once, and completed the present invention.
すなわち、本発明によれば、Ａｌ、Ｎｉｔを所定範囲内
に調節することによって所要量のＡｌＮを生成させて浸
炭時のオーステナイト結晶粒の粗大化を抑制するととも
に、＾ｒ３点以上の高温仕上げおよび３５０〜５５０℃
での巻取りを行うことによって、それらの相乗的効果を
利用してオーステナイト結晶粒の粗大化を！■制し、更
には圧延に先立つ加熱を比較的低温度で行ってオーステ
ナイト結晶粒の細粒化、つまり圧延後のフェライト結晶
粒の細粒化を図り、併せて板材の浸炭特性を著しく改善
しようとするのである。That is, according to the present invention, by adjusting Al and Ni within a predetermined range, a required amount of AlN is generated to suppress coarsening of austenite crystal grains during carburization, and also to achieve high-temperature finishing of 3 or more points. 350-550℃
By winding the austenite grains, the synergistic effect can be utilized to coarsen the austenite grains. ■By heating at a relatively low temperature prior to rolling, we aim to refine the austenite grains, that is, to refine the ferrite grains after rolling, and at the same time, significantly improve the carburizing properties of the plate material. That is to say.
ここに、本発明の要旨とするところは
重量％で、
Ｃ： ｏ、ｏｓ〜０．５０％、 Ｓｉ ： ０．４０
％以下、Ｍに〇、２０〜１．２０％、 Ａｌ ： ０
．０２％以上、ｒＪ ： ０．００５０〜０．０１６０
％でかつ（Ａｌ＋２Ｎ）≧０．０４０％、（Ａｌ＋５Ｎ
）５０．１１％、残部Ｆｅおよび不可避的不純物
からなる組成を有する鋼を、１２００℃以下に加熱して
から、Ａｒ３点以上の仕上温度、３５０〜５５０℃の巻
取温度で熱間圧延することを特徴とする）受炭特性のす
ぐれた鋼板の製造法である。なお、必要により、焼入れ
性をさらに改善するためにＣｒ ： １．５％以下、Ｍ
。Here, the gist of the present invention is expressed in weight%: C: o, os ~ 0.50%, Si: 0.40
% or less, 〇 to M, 20 to 1.20%, Al: 0
．． 02% or more, rJ: 0.0050 to 0.0160
% and (Al+2N)≧0.040%, (Al+5N
) 50.11%, the balance being Fe and unavoidable impurities, is heated to 1200°C or lower and then hot rolled at a finishing temperature of 3 points Ar or higher and a coiling temperature of 350 to 550°C. This is a method for manufacturing steel sheets with excellent coal-receiving properties. In addition, if necessary, in order to further improve the hardenability, Cr: 1.5% or less, M
.
： １．０％以下の少なくとも１種をさらに加えてもよ
い。: 1.0% or less of at least one kind may be further added.
（作用）
本発明において鋼組成および熱間圧延条件を上述の如く
限定した理由についてさらに詳述する。(Function) The reason why the steel composition and hot rolling conditions are limited as described above in the present invention will be explained in further detail.
Ｃ：Ｃは浸炭焼入れ後の母材部にも所定の硬度を確保す
るために、母材の組成として少なくとも０．０５％含有
させることが必要である。しかし、０．５０％以上含有
させるとむしろ焼入れ後の靭性を劣化させるので本発明
ではＣ量は０．５０％を上置とする。C: In order to ensure a predetermined hardness in the base material after carburizing and quenching, it is necessary to include at least 0.05% of C in the base material composition. However, if it is contained in an amount of 0.50% or more, the toughness after quenching will deteriorate, so in the present invention, the C content is set at 0.50%.
Ｓｉ ： Ｓｉは脱酸剤として添加するが、Ｓｉが０．
４０％以上含有させるとＢ系介在物が多くなり母材の加
工性を劣化させるので０．４０％を上限とする。Si: Si is added as a deoxidizing agent, but if Si is 0.
If the content exceeds 40%, the number of B-based inclusions increases and the workability of the base metal deteriorates, so the upper limit is set at 0.40%.
Ｍｎ ： Ｍｎは焼入れ性をｉし、母材部の硬度を高く
するために必要な元素であるが、Ｍｎ含有量が多すぎる
と靭性を劣化させるので本発明では０．２０〜１．２０
％の範囲とする。Mn: Mn is an element necessary to improve hardenability and increase the hardness of the base material, but if the Mn content is too large, the toughness will deteriorate, so in the present invention it is 0.20 to 1.20.
% range.
Ｃｒ、Ｍｏ ：これらの元素は焼入れ性を改善する元素
として有効であるが、含有量が多すぎると焼入れ性が増
しすぎ靭性を劣化させるのでＣｒ ； １．５％、Ｍ。Cr, Mo: These elements are effective as elements for improving hardenability, but if the content is too large, the hardenability increases too much and the toughness deteriorates, so Cr: 1.5%, M.
：１．０％をそれぞれ上限とする。: The upper limit of each is 1.0%.
なお、これら２種あ元素は所望元素であり、それらを添
加すると製造コストをかなり高めるため、必ずしも必要
としない。Note that these two types of elements are desired elements, and their addition considerably increases manufacturing costs, so they are not necessarily required.
鮫、Ｎ：本発明にあって、ＡｌとＮはＡｌＮを生成し、
ｉ３炭時のオーステナイト結晶粒の粗大化を抑制する効
果を持つが、Ａｌ ０．０２％未満、Ｎ Ｏ，００５０
％未満でかつ（Ａ（！＋２Ｎ） ０．０４０％未満では
オーステナイト結晶粒の粗大化を防ぐのに必要なＡｌＮ
Ｒが確１呆できない。Shark, N: In the present invention, Al and N generate AlN,
It has the effect of suppressing the coarsening of austenite crystal grains during i3 coal, but Al less than 0.02%, NO,0050
% and (A(!+2N)) less than 0.040%, the AlN necessary to prevent coarsening of austenite crystal grains
R is definitely not disappointed.
一方、（Ａｌ＋５Ｎ）が０．１１％超では後述する熱間
圧延時の加熱温度ではＡｌＮを固溶させることができず
、やはり浸炭処理時にオーステナイト結晶粒が１■大化
する。また、Ｎを０．０１６０％を超えて添加してもオ
ーステナイト結晶粒粗大化抑制効果が飽和し、かつ連続
鋳造時のスラブ表面疵を招く等の問題があるため、本発
明では０．０１６０％を上限とする。On the other hand, if (Al+5N) exceeds 0.11%, AlN cannot be dissolved as a solid solution at the heating temperature during hot rolling, which will be described later, and the austenite crystal grains also increase in size by 1 inch during carburization. Furthermore, even if N is added in excess of 0.0160%, the effect of suppressing austenite grain coarsening is saturated, and there are problems such as causing slab surface defects during continuous casting. is the upper limit.
その他、本発明が対象とする鋼には付随不純物が存在し
てもよく、例えば、ＳおよびＰなどはそれぞれｏ、ｏｉ
ｏ％以下、０．０２０％以下程度存在していてもよい。In addition, incidental impurities may be present in the steel targeted by the present invention, for example, S and P are o and oi, respectively.
It may be present in an amount of 0% or less, 0.020% or less.
加熱温度：浸炭焼入れ後の母材部の靭性を確保するため
には、熱間圧延に際しての加熱温度を１２００℃以下に
する必要がある。すなわち、母材部の靭性を良くするた
めには、圧延前のオーステナイト結晶粒が細かい状態で
まず熱間圧延を行い、このため、加熱１度を１２００℃
以下とし、これにより熱間圧延後のフェライト粒を細粒
にし、このようにフェライト結晶粒を微細化することに
よって浸炭時のオーステナイト結晶粒を微細化する必要
があるためである。か（してオーステナイト結晶粒の粗
大化が阻止され、母材部の靭性が確保されるだけでなく
、浸炭焼入時の焼入れ歪も少なくなる。Heating temperature: In order to ensure the toughness of the base material after carburizing and quenching, the heating temperature during hot rolling must be 1200°C or less. In other words, in order to improve the toughness of the base material, hot rolling is first performed in a state where the austenite crystal grains are fine before rolling, and for this reason, the heating temperature is 1200°C.
This is because it is necessary to make the ferrite grains after hot rolling finer, and by making the ferrite crystal grains finer in this way, the austenite crystal grains during carburization are made finer. (This prevents austenite crystal grains from becoming coarser, which not only ensures the toughness of the base material but also reduces quenching distortion during carburizing and quenching.
仕上温度：Ａｒ３点より低い温度で仕上圧延を行うと母
材の加工性が劣化するばかりでなく、圧延中にＡｌＮが
析出し浸炭時にオーステナイト結晶粒が粗大化してしま
うので、仕上げ温度はＡｒ３点以上に規定する。Finishing temperature: Performing finish rolling at a temperature lower than Ar3 point not only deteriorates the workability of the base metal, but also precipitates AlN during rolling and coarsens austenite grains during carburization, so the finishing temperature is set at Ar3 point. As stipulated above.
巻取温度：巻取温度が５５０℃を超えると、巻取時にフ
ェライト粒界のみにＡｌＮが析出し、粒内から生成する
オーステナイト結晶粒の成長抑制効果を示さない、すな
わち、５５０℃以下の低温巻取りでは熱間圧延ままの状
態のときＡｌＮは固溶しており次工程の球状化焼鈍時に
ＡｌＮがフェライト粒界および粒内に微細析出しオース
テナイト結晶粒の粗大化が抑制されるのである。Winding temperature: If the winding temperature exceeds 550°C, AlN will precipitate only at the ferrite grain boundaries during winding, and will not have the effect of suppressing the growth of austenite crystal grains generated from within the grains. In other words, at a low temperature of 550°C or less During winding, AlN is in solid solution in the as-hot-rolled state, and during the next step of spheroidizing annealing, AlN is finely precipitated at the ferrite grain boundaries and inside the grains, thereby suppressing the coarsening of austenite crystal grains.
一方、巻取温度が３５０℃未満となるとベイナイト、マ
ルテンサイト等の変態組織がみられ熱間圧延鋼板の強度
が高くなりすぎ、たとえ球状化焼鈍しても精密打抜加工
用素材として必要な軟質化が図れない。On the other hand, if the coiling temperature is less than 350℃, transformation structures such as bainite and martensite will be observed, and the strength of the hot rolled steel sheet will be too high. cannot be achieved.
よって、本発明にあっては巻取温度を３５０〜５５０℃
の範囲内に制限する。Therefore, in the present invention, the winding temperature is 350 to 550°C.
Limit within the range of.
なお、球状化焼鈍条件としては特に制約はなく、１１１
℃當行なわれている如く、精密打抜加工用素材として必
要な硬度の上限、例えばＷ＊６８０を得る条件であれば
良い。Note that there are no particular restrictions on the spheroidizing annealing conditions, and 111
It is sufficient that the hardness is the upper limit of hardness required as a material for precision punching, for example, W*680, as is currently practiced at ℃.
次に本発明を実施例によりさらに具体的に説明する。Next, the present invention will be explained in more detail with reference to Examples.
１丘１０＝
本例はオーステナイト結晶粒の粗大化に及ぼす巻取温度
の影響をみる。1 hill 10 = This example examines the effect of coiling temperature on coarsening of austenite crystal grains.
まず、第１表に示す鋼組成を有する本発明において規定
する範囲内の鋼を用いて、１１５０℃に加熱し、ＳｔＯ
℃で仕上圧延を行い、次いで６８０℃×１０ｈの球状化
処理後浸炭焼入れを行ったときのオーステナイト結晶粒
粗大化状況を添付図面にグラフにまとめて示す０図示結
果より明らかなように、５５０℃以下の巻取時にオース
テナイト結晶粒の粗大化が大幅に抑制されるのが分かる
。浸炭処理はカーボンポテンシャル０．９％の浸炭ガス
を使い９００℃×９０分行い、次いで油浴中で焼入れし
た。なお、オーステナイトの粗大化率は粒度陽６以上の
結晶粒の面積率で示す。First, a steel having the steel composition shown in Table 1 and within the range specified in the present invention is heated to 1150°C, and StO
The accompanying drawing shows the coarsening of austenite grains when finish rolling was performed at 550°C, followed by carburizing and quenching at 680°C for 10 hours. It can be seen that the coarsening of austenite crystal grains is significantly suppressed during the following winding process. Carburizing treatment was performed at 900° C. for 90 minutes using carburizing gas with a carbon potential of 0.9%, and then quenching was performed in an oil bath. Note that the coarsening rate of austenite is expressed as the area ratio of crystal grains with a grain size of +6 or more.
第１表 （重量％）
０．２１ ０．１Ｂ ０．７２ １．０１ ０．０３
２ ０．００９２ ７８０℃裏止皿ｌ
第２表に示す組成の鋼を１１５０℃加熱、８１０℃仕上
、５００℃巻取の圧延条件で圧延し、これを６８０℃×
１５ｈの球状化焼鈍した後、９００℃に昇温しその温度
で９０分保持した後のオーステナイト粒の粗大化率を同
表に示す。Table 1 (% by weight) 0.21 0.1B 0.72 1.01 0.03
2 0.0092 780℃ backing plate l Steel with the composition shown in Table 2 was rolled under the following rolling conditions: heating at 1150℃, finishing at 810℃, and winding at 500℃.
The same table shows the coarsening rate of austenite grains after spheroidizing annealing for 15 hours, raising the temperature to 900° C. and holding at that temperature for 90 minutes.
同表に示す結果より明らかなように、Ａｌ≧０．０２％
、Ｎ≧ｏ、ｏｏｓｏ％、（Ａｌ＋２Ｎ）≧０．０４Ｑ％
、（Ａ（２＋５Ｎ）５０．１１％を満たす成分系のみオ
ーステナイトの粗大化が抑制されているのが分かる。As is clear from the results shown in the same table, Al≧0.02%
, N≧o, ooso%, (Al+2N)≧0.04Q%
It can be seen that coarsening of austenite is suppressed only in the component system satisfying , (A(2+5N)50.11%).
裏止皿主
次に第２表のＡ鋼（Ａｒ ３点７９５℃）を種々の圧延
条件で熱間圧延し、これを６９０℃Ｘ １５ｈの球状化
焼鈍した後、９００℃で９０分加熱してガス浸炭−泊焼
入れを行−１た。その際の各工程での条件および得られ
た鋼板の特性を第３表にまとめて示す、浸炭焼入れ条件
は実施例１に同しであった。Next, the A steel shown in Table 2 (Ar 3 points 795°C) was hot rolled under various rolling conditions, and after spheroidizing annealing at 690°C for 15 hours, it was heated at 900°C for 90 minutes. Gas carburizing and overnight quenching were performed. The conditions in each step and the properties of the obtained steel sheets are summarized in Table 3. The carburizing and quenching conditions were the same as in Example 1.
同表に示す結果より明らかなように、本発明の規定する
範囲内の条件下では車にオーステナイト結晶の１■大化
が抑制されるだけでなく、禎密打抜加工用素（１として
軟質でかつ最終製品としても優れた特性を示している。As is clear from the results shown in the same table, under the conditions within the range specified by the present invention, not only is the austenite crystal in the car suppressed from increasing to 1. Moreover, it also shows excellent properties as a final product.
、ｉ、Ｖｌ而の部上な一見明
添付図面はオーステナイトの粒成長に与える熱間圧Ｌｆ
ｅ取温広温度響を示すグラフである。, i, Vl and the attached drawings, which are clearly visible at first glance, show the hot pressure Lf exerted on the grain growth of austenite.
It is a graph showing e-temperature wide temperature effects.
出願人 住友金泥工業株式会社
代理人 弁理士 広 瀬 童 −（他１名）巻取長り
度（“Ｃ）Applicant Sumitomo Kindo Industries Co., Ltd. Agent Patent Attorney Do Hirose - (1 other person) Winding length (“C”)
Claims (2)
ｎ：０．２０〜１．２０％、Ａｌ：０．０２％以上、Ｎ
：０．００５０〜０．０１６０％でかつ （Ａｌ＋２Ｎ）≧０．０４０％、（Ａｌ＋５Ｎ）≦０．
１１％、残部Ｆｅおよび不可避的不純物 からなる組成を有する鋼を、１２００℃以下に加熱して
から、Ａｒ＿３点以上の仕上温度、３５０〜５５０℃の
巻取温度で熱間圧延することを特徴とする浸炭特性のす
ぐれた鋼板の製造法。(1) In weight%, C: 0.05 to 0.50%, Si: 0.40% or less, M
n: 0.20-1.20%, Al: 0.02% or more, N
: 0.0050 to 0.0160%, and (Al+2N)≧0.040%, (Al+5N)≦0.
Steel having a composition consisting of 11%, the balance Fe and unavoidable impurities is heated to 1200°C or lower, and then hot rolled at a finishing temperature of Ar_3 points or higher and a coiling temperature of 350 to 550°C. A method for manufacturing steel sheets with excellent carburizing properties.
ｎ：０．２０〜１．２０％、Ａｌ：０．０２％以上、Ｎ
：０．００５０〜０．０１６０％でかつ （Ａｌ＋２Ｎ）≧０．０４０％、（Ａｌ＋５Ｎ）≧０．
１１％、Ｃｒ：１．５％以下およびＭｏ：１．０％以下
の少なくとも１種、 残部Ｆｅおよび不可避的不純物 からなる組成を有する鋼を、１２００℃以下に加熱して
から、Ａｒ＿３点以上の仕上温度、３５０〜５５０℃の
巻取温度で熱間圧延することを特徴とする浸炭特性のす
ぐれた鋼板の製造法。(2) In weight%, C: 0.05 to 0.50%, Si: 0.40% or less, M
n: 0.20-1.20%, Al: 0.02% or more, N
: 0.0050 to 0.0160%, and (Al+2N)≧0.040%, (Al+5N)≧0.
11%, Cr: 1.5% or less and Mo: 1.0% or less, the balance being Fe and unavoidable impurities. After heating the steel to 1200°C or less, Ar_3 points or more. A method for producing a steel plate with excellent carburizing properties, characterized by hot rolling at a finishing temperature of 350 to 550°C.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP22590184A JPS61106715A (en) | 1984-10-29 | 1984-10-29 | Manufacture of steel plate having superior carburizing property |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP22590184A JPS61106715A (en) | 1984-10-29 | 1984-10-29 | Manufacture of steel plate having superior carburizing property |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS61106715A true JPS61106715A (en) | 1986-05-24 |
| JPH0568527B2 JPH0568527B2 (en) | 1993-09-29 |
Family
ID=16836656
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP22590184A Granted JPS61106715A (en) | 1984-10-29 | 1984-10-29 | Manufacture of steel plate having superior carburizing property |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS61106715A (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS63137145A (en) * | 1986-11-29 | 1988-06-09 | Nippon Steel Corp | Steel for carburizing |
| JPS6447838A (en) * | 1987-08-13 | 1989-02-22 | Nippon Steel Corp | Curburizing steel |
| JP6587038B1 (en) * | 2018-10-02 | 2019-10-09 | 日本製鉄株式会社 | Carburizing steel sheet and method for manufacturing carburizing steel sheet |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS591632A (en) * | 1982-06-28 | 1984-01-07 | Sumitomo Metal Ind Ltd | Manufacture of hot-rolled high-tension steel sheet with superior workability |
| JPS59150018A (en) * | 1983-02-17 | 1984-08-28 | Sumitomo Metal Ind Ltd | Production of ti-added hot rolled high tension steel sheet having good processability |
-
1984
- 1984-10-29 JP JP22590184A patent/JPS61106715A/en active Granted
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS591632A (en) * | 1982-06-28 | 1984-01-07 | Sumitomo Metal Ind Ltd | Manufacture of hot-rolled high-tension steel sheet with superior workability |
| JPS59150018A (en) * | 1983-02-17 | 1984-08-28 | Sumitomo Metal Ind Ltd | Production of ti-added hot rolled high tension steel sheet having good processability |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS63137145A (en) * | 1986-11-29 | 1988-06-09 | Nippon Steel Corp | Steel for carburizing |
| JPH049858B2 (en) * | 1986-11-29 | 1992-02-21 | ||
| JPS6447838A (en) * | 1987-08-13 | 1989-02-22 | Nippon Steel Corp | Curburizing steel |
| JP6587038B1 (en) * | 2018-10-02 | 2019-10-09 | 日本製鉄株式会社 | Carburizing steel sheet and method for manufacturing carburizing steel sheet |
| WO2020070810A1 (en) * | 2018-10-02 | 2020-04-09 | 日本製鉄株式会社 | Steel sheet for carburizing, and production method for steel sheet for carburizing |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0568527B2 (en) | 1993-09-29 |
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