JPS61104030A - Manufacture of steel sheet having superior carburization hardenability - Google Patents
Manufacture of steel sheet having superior carburization hardenabilityInfo
- Publication number
- JPS61104030A JPS61104030A JP22384584A JP22384584A JPS61104030A JP S61104030 A JPS61104030 A JP S61104030A JP 22384584 A JP22384584 A JP 22384584A JP 22384584 A JP22384584 A JP 22384584A JP S61104030 A JPS61104030 A JP S61104030A
- Authority
- JP
- Japan
- Prior art keywords
- hardenability
- temperature
- aln
- steel
- present
- 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.)
- Granted
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
Abstract
Description
【発明の詳細な説明】
（産業上の利用分野）
本発明は、連続鋳造で製造される低炭素熱間圧延鋼板、
特に加工性と浸炭処理時の焼入れ性にすぐれた、いわゆ
る脱燐用鋼板を製造する方法に関する。Detailed Description of the Invention (Industrial Application Field) The present invention provides low carbon hot rolled steel sheets manufactured by continuous casting;
In particular, the present invention relates to a method for producing a steel plate for dephosphorization, which has excellent workability and hardenability during carburization.
従来、自動車や産業機械の部品用として多量に製造され
ている熱間圧延鋼板の一部には、成形加工後、浸炭−焼
入れ処理、つまり乳層処理をして表面硬さや耐摩耗性を
改善することが要求される場合がある。通常、これらの
部品は高い製品寸法精度が要求されるため、上述のよう
な表面硬さや耐摩耗性改善のために浸炭、熱処理を行う
場合にも、８００〜９００℃の低温で浸炭したのち１６
０℃前後の油浴中で焼入れして、変形を可及的に防止し
ｔいる。したがって、従来より、かかる目的に使用する
炭素鋼としては、比較的遅い冷却速度の浸炭−焼入れに
よっても硬化しやすいリムド鋼が多く用いられてきた。Conventionally, some of the hot rolled steel sheets manufactured in large quantities for parts of automobiles and industrial machinery are subjected to carburizing and quenching treatment, or milk layer treatment, to improve surface hardness and wear resistance after forming. may be required to do so. Normally, these parts require high product dimensional accuracy, so even when carburizing and heat treating to improve surface hardness and wear resistance as described above, the parts are carburized at a low temperature of 800 to 900°C and then heated to 16°C.
It is hardened in an oil bath at around 0°C to prevent deformation as much as possible. Therefore, conventionally, as carbon steel used for such purposes, rimmed steel, which is easily hardened even by carburizing and quenching at a relatively slow cooling rate, has been widely used.
ところで、他方、生産性の向上、特に連鋳比の
。By the way, on the other hand, it is important to improve productivity, especially the continuous casting ratio.
.
向上が求められている今日的状況からは、これらの多量
に生産されてきたリムド鋼は徐々にアルミキルド鋼に代
替されつつある。しかし、ここで問題となるのは、通常
の低炭素アルミキルト鋼はＡｌを０．０２％以上含有し
ており、Ａ（２Ｎが存在しているため浸炭時のオーステ
ナイトがＡｌＮにより微細化し、焼入れ性が低下し十分
な硬化層深さが得られないということである。つまり、
従来の熱処理法を採用する限り所要の表面硬さおよび耐
摩耗性が得られないのである。Given the current situation where improvements are required, these rimmed steels, which have been produced in large quantities, are gradually being replaced by aluminum killed steels. However, the problem here is that ordinary low-carbon aluminum quilt steel contains 0.02% or more of Al, and because of the presence of A(2N), the austenite during carburization is refined by AlN, and when quenched This means that the hardness is reduced and a sufficient hardened layer depth cannot be obtained.In other words,
As long as conventional heat treatment methods are used, the required surface hardness and wear resistance cannot be obtained.
なお同様な用途に使用される高合金鋼肌焼鋼の場合、Ｃ
ｒ等の合金元素を比較的多量に含むため焼入れ時の臨界
冷却速度はかなり小さく特に問題はない。In the case of high-alloy case-hardened steel used for similar purposes, C
Since it contains a relatively large amount of alloying elements such as r, the critical cooling rate during quenching is quite small and poses no particular problem.
この問題を解決する方法としては、例えば特開昭５７−
１４５９３４号公報に開示されているように、Ａｌ：
０．００１〜０．００５％、Ｎ ： ０．００４０％以
下とし、Ａｌ量とＮ量を低下させてに２Ｎの絶対量を少
なくさせ、かつ仕上温度Ａｒ（〜＾ｒ３点、巻取温度６
５０℃以上とし、α＋γの二相領域での低温仕上圧延後
高温巻取する方法がある。すなわち、ＡｌＮを可及的に
低減化してフェライト粒の微細化を防止する一方、二相
領域圧延を行ってフェライト粒の生成・粗大化を図り、
かつ高温を取りによってフェライト粒の均一成長を促す
というものである。あるいは特開昭５８−２０４１５７
号公報に開示されているようにＡｌ添加による焼入れ性
の低下をＣｒ添加により補う方法も提案されている。As a method to solve this problem, for example,
As disclosed in Publication No. 145934, Al:
0.001 to 0.005%, N: 0.0040% or less, lowering the Al amount and N amount to reduce the absolute amount of 2N, and finishing temperature Ar (~^r 3 points, winding temperature 6
There is a method of finishing rolling at a temperature of 50° C. or higher in a two-phase region of α+γ and then winding at a high temperature. That is, while reducing AlN as much as possible to prevent refinement of ferrite grains, rolling is performed in a two-phase region to generate and coarsen ferrite grains,
The high temperature also promotes uniform growth of ferrite grains. Or JP-A-58-204157
As disclosed in the above publication, a method has also been proposed in which the decrease in hardenability due to the addition of Al is compensated for by the addition of Cr.
しかし現状の製鋼技術のレベルでは、通常の手段で例え
ばＡｌ量を０．００５％以下という極低領域で制御する
ことは困難であり、高価な炉外精錬等の特殊処理を要し
、結局、製造コス１−の上昇を招く、または二相域での
低温仕上圧延は母材の加工性を劣化させやすいことは良
く知られている。一方、Ｃｒの添加は焼入性の点からは
好ましいが、やはり合金コストの上昇を招く。However, with the current level of steelmaking technology, it is difficult to control the Al content to an extremely low level of 0.005% or less using normal means, and special treatments such as expensive out-of-furnace refining are required. It is well known that low-temperature finish rolling in a two-phase region that causes an increase in production cost 1- tends to deteriorate the workability of the base material. On the other hand, although addition of Cr is preferable from the viewpoint of hardenability, it also causes an increase in alloy cost.
すでに述べたように、本発明が対象としている低炭素熱
間圧延鋼板が多量に消費される安価な材料であることを
考えると、これらの手段はいずれも実用的とはいえない
。As already mentioned, considering that the low-carbon hot-rolled steel sheet to which the present invention is directed is an inexpensive material that is consumed in large quantities, none of these measures can be said to be practical.
（発明が解決しようとする問題点）
上述のように、経済性の観点から低炭素熱間圧延鋼板に
おけるＡｌおよびＮの相当量の存在が不可避であるなら
ば、Ａ（２Ｎの析出が焼入れ性態下をもたらす原因およ
び機構を究明することによって、従来のように、例えば
ＡｌＮそれ自体の排除あるいは焼入れ性向上元素の添加
といった高価な手段によらない解決手段が解明されると
の着想にもとずき、鋭意研究をつづけた。(Problems to be Solved by the Invention) As mentioned above, if the presence of a considerable amount of Al and N in a low carbon hot rolled steel sheet is unavoidable from the economic point of view, then the precipitation of A(2N) It is based on the idea that by investigating the causes and mechanisms that cause this condition, we will be able to find solutions that do not rely on conventional expensive methods such as eliminating AlN itself or adding elements that improve hardenability. I continued my research with great enthusiasm.
ここに、本発明の目的は、上記の従来技術の各
。Here, an object of the present invention is to solve each of the above-mentioned conventional techniques.
.
問題点を解決するとともに、連続鋳造の作業性を阻害せ
ずに良好な加工性と浸炭焼入性をもつ低炭素アルミキル
ド鋼を経済的に製造する方法を提供することである。The object of the present invention is to solve the problems and provide a method for economically producing low carbon aluminum killed steel having good workability and carburizing hardenability without impairing the workability of continuous casting.
（問題点を解決す名ための手段）
本発明者らは、Ａ１２． Ｎの多量は通常レベルとしつ
つも、従来問題となったＡｌＮの析出の害は、析出する
ＡｌＮを粗大化することによって解消することを知った
。(Means for solving the problem) The present inventors have discovered A12. It has been found that while keeping the amount of N at a normal level, the harm caused by the precipitation of AlN, which has been a problem in the past, can be resolved by making the precipitated AlN coarser.
すなわち、本発明者らの知見によれば、Ａｌ、Ｎの多量
は通常レベルとしつつも、析出するＡｌＮの形態を制御
することによって焼入れ性の低下を防止できることを知
り、さらに検針を続けたところ、熱間圧延段階で析出Ａ
ｌＮの凝集化を図ることが有効であることを知見し、本
発明を完成した。That is, according to the findings of the present inventors, it was found that deterioration in hardenability could be prevented by controlling the form of precipitated AlN while keeping the large amounts of Al and N at normal levels. , precipitation A during the hot rolling stage
The present invention was completed based on the finding that it is effective to aggregate IN.
よって、本発明の要旨とするところは、重量％で、
Ｃ：０．１０％以下、 Ｓｉ ： ０．０６％以下、
Ｍｎ ： Ｑ、１ 〜０．５ ％、 Ａｌ
： ０．０１〜０．０４ ％、Ｎ ： ０．００６
０％以下、
残部Ｆｅおよび不可避的不純物元素
からなる組成を有するＡｌキルド鋼を連続鋳造し、得ら
れた熱鋳片を７５０℃以上、Ａｒ３点以下に降温し、次
いで１０００〜１１５０℃に加熱した後、仕上温度Ａｒ
３点以上および巻取温度２５０〜５００℃の条件下で圧
延することを特徴とする、浸炭焼入れ性のすぐれた鋼板
の製造方法である。Therefore, the gist of the present invention is, in weight percent, C: 0.10% or less, Si: 0.06% or less,
Mn: Q, 1-0.5%, Al
: 0.01-0.04%, N: 0.006
Al-killed steel having a composition of 0% or less, the balance consisting of Fe and unavoidable impurity elements was continuously cast, and the temperature of the obtained hot slab was lowered to 750°C or higher and Ar3 point or lower, and then heated to 1000 to 1150°C. After that, finish temperature Ar
This is a method for manufacturing a steel plate with excellent carburizing and hardenability, which is characterized by rolling at three or more points and at a coiling temperature of 250 to 500°C.
このように、本発明によれば、むしろＡｌＮを積極的に
析出させ、粗大化させてその無害化を図っているのであ
り、しかも予想外にも加工性が併せて大巾に改善される
のである。In this way, according to the present invention, AlN is actively precipitated and coarsened to make it harmless, and unexpectedly, workability is also greatly improved. be.
したがって、本発明により実用上初めて連続鋳造低炭素
Ａｌキルド鋼の肌焼鋼が製造され得るのである。Therefore, according to the present invention, for the first time in practical use, a continuously cast low carbon Al-killed case hardened steel can be manufactured.
（作用）
次に、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を詳述する。なお、特にことわりが
ない限り、本明細書において「％」は「重量％」である
。(Function) Next, the reason why the steel composition and hot rolling conditions are limited as described above in the present invention will be explained in detail. In this specification, "%" means "% by weight" unless otherwise specified.
Ｃ：本発明にあってＣ量の下限の制限はとくにないが０
．０１％より少ない極低Ｃ量を得るには特殊な精錬を要
するため０．０１％以上であることが好ましい。一方、
ｃｌが０．１θ％超では加工性が劣化し、かつ硬質とな
るため、上限は０．１０％とする。好ましくは０．０４
〜０．０８％である。C: In the present invention, there is no particular restriction on the lower limit of the amount of C, but 0
．． Since special refining is required to obtain an extremely low C content of less than 0.01%, the content is preferably 0.01% or more. on the other hand,
If Cl exceeds 0.1θ%, workability deteriorates and the steel becomes hard, so the upper limit is set to 0.10%. Preferably 0.04
~0.08%.
Ｓｉ ： Ｓｉは浸炭−焼入れ性には影響のない元素で
あるが、その含有量が０．０６％超では加工性が劣化す
るため、上限を０．０６％とする。好ましくは０゜０１
〜０．０５％である。Si: Si is an element that has no effect on carburizing and hardenability, but if its content exceeds 0.06%, workability deteriorates, so the upper limit is set to 0.06%. Preferably 0°01
~0.05%.
Ｍｎ：焼入れ性を確保するために０．１％以上を必要と
するが、０．５％超では加工性が劣化し、かつ得られる
組織が硬質となる。よって、本発明ではＭｎ量は０．１
〜０．５％とする。好ましくは０．１２〜０．４０％で
ある。Mn: 0.1% or more is required to ensure hardenability, but if it exceeds 0.5%, workability deteriorates and the resulting structure becomes hard. Therefore, in the present invention, the Mn amount is 0.1
~0.5%. Preferably it is 0.12 to 0.40%.
Ａｌ、Ｎ：ＡｌおよびＮはいずれも通常量の存在で浸炭
時のオーステナイト粒を微細化し、焼入れ性を低下させ
る元素であるが、本発明では後述するように、Ａｌおよ
びＮをＡｌＮとして析出させ、この析出するＡｌＮを粗
大化させることによりその影響を無害化しているのでＡ
ｌおよびＮの容量は通常のレベルでよい。すなわち、鮫
は脱酸に必要なレベル０．０１％を下限として、上限は
脱酸効果が飽和する０、０４％とする。またＮの上限は
０．００６０％以下とする。これらは上述の範囲内にお
いて低い方が好ましい。好ましくはＡｌ ： ０．０１
５〜０．０３０％、Ｎ ： ０．００４０％以下である
。Al, N: Both Al and N are elements that refine austenite grains during carburization and reduce hardenability when present in normal amounts, but in the present invention, as described later, Al and N are precipitated as AlN. , by coarsening the precipitated AlN, the effect is rendered harmless, so
The capacitances of l and N may be at conventional levels. That is, for sharks, the lower limit is 0.01%, which is the level required for deoxidation, and the upper limit is 0.04%, at which the deoxidizing effect is saturated. Further, the upper limit of N is 0.0060% or less. It is preferable that these values are lower within the above-mentioned ranges. Preferably Al: 0.01
5 to 0.030%, N: 0.0040% or less.
なお、本発明においてその他通常の付随不純物が含有さ
れるが、例えばＳおよびＰについてはそれぞれ０．０２
０％以下および０．１０％以下に制限すれば十分である
。In addition, other usual incidental impurities are contained in the present invention, but for example, S and P each contain 0.02
It is sufficient to limit it to 0% or less and 0.10% or less.
加熱条件二本発明によれば、連続鋳造により得られた熱
鋳片は７５０℃以上、Ａｒ３点以下に降温するが、熱鋳
片をＡ’ｒ ３点より高い温度で加熱炉に装入すると添
加したＡｌ、Ｎは固溶したままで存在し、圧延後に微細
析出し、前述したように浸炭時のオーステナイトを微細
化するため焼入れ性が低下する。したがって連続鋳造に
よる熱鋳片を一旦Ａｒ３点以下に降温し積極的にＡｌＮ
を析 出させる必要がある。また７５０℃より
低温に降温させてもＡｌＮの析出は飽和し、その効果が
飽和するばかりでなく、後続工程で行う再加熱に必要な
エネルギーが増加するため下限を７５０℃、好ましくは
８００℃とする。Heating condition 2 According to the present invention, the temperature of the hot slab obtained by continuous casting is lowered to 750°C or higher and below the Ar3 point, but if the hot slab is charged into the heating furnace at a temperature higher than the A'r3 point, The added Al and N exist as a solid solution, and finely precipitate after rolling, and as described above, they refine the austenite during carburization, resulting in a decrease in hardenability. Therefore, the temperature of hot slabs produced by continuous casting is lowered to below the Ar3 point, and then AlN is actively applied.
It is necessary to precipitate the Furthermore, even if the temperature is lowered to lower than 750°C, the precipitation of AlN will not only be saturated, but also the energy required for reheating in the subsequent process will increase, so the lower limit should be set at 750°C, preferably 800°C. do.
次いで、上述のようにして一旦＋＋ｉ温させた熱鋳片は
再び１０００〜１１５０℃に加熱してから熱間圧延を行
うが、その場合、加熱温度が１１５０℃を超えると、先
に析出したＡｌＮが完全再固溶し、やはり前述と同じ理
由で焼入性が低下するためこ ７のときの
加熱温度の上限は１１５０℃とする。一方、１０００℃
未満では熱間圧延時にＡｒ３点以上の仕上温度が確保で
きないと共に析出したＡｌＮの粗大凝集化が不十分であ
る。したがって、本発明では加熱温度は１０００〜１１
５０℃とする。Next, the hot slab that has been once heated to ++i temperature as described above is heated again to 1000 to 1150°C and then hot rolled. In this case, if the heating temperature exceeds 1150°C, the AlN precipitated earlier The upper limit of the heating temperature in step 7 is set at 1150°C because the hardenability is also reduced due to the same reason as mentioned above. On the other hand, 1000℃
If it is less than that, it will not be possible to secure a finishing temperature of Ar3 or higher during hot rolling, and coarse agglomeration of precipitated AlN will be insufficient. Therefore, in the present invention, the heating temperature is 1000 to 11
The temperature shall be 50°C.
仕上温度：Ａｒ３点未満の温度で圧延するとフェライト
粒が析出することになり、このフェライト粒が加工され
ると、加工性が劣化する。Finishing temperature: If rolling is performed at a temperature below Ar3, ferrite grains will precipitate, and if these ferrite grains are worked, workability will deteriorate.
巻取温度：すでに述べたように、本発明にあっては、熱
間圧延に先立って加熱時にＡｌＮを析出させる必要はな
い。加工性の点から巻取温度が制約されるだけである。Coiling temperature: As already mentioned, in the present invention, it is not necessary to precipitate AlN during heating prior to hot rolling. The winding temperature is only restricted from the viewpoint of processability.
すなわち、５００℃を超えた巻取温度では、フェライト
粒界に粗大な炭化物が生成し、加工性、特に絞り性を劣
化させる。That is, at a winding temperature exceeding 500° C., coarse carbides are generated at ferrite grain boundaries, deteriorating workability, particularly drawability.
一方、２５０℃未満の温度での巻取では、熱間圧延板中
に固溶Ｃが存在し、ひずみ時効による加工性の劣化が生
じるため、本発明における巻取温度は２５０〜５００℃
とする。On the other hand, when coiling at a temperature of less than 250°C, solid solution C exists in the hot rolled plate and deterioration of workability occurs due to strain aging. Therefore, the coiling temperature in the present invention is 250 to 500°C.
shall be.
次に、実施例によって本発明をさらに説明する。Next, the present invention will be further explained by examples.
１施皿上
第１表に示す組成を有するアルミキルド鋼を連続鋳造し
て２１０ ｍ厚のスラブとし、次いで第２表に示す条件
で熱間圧延し、２．６Ｎ厚の熱間圧延板とした。1. On a plate, aluminum killed steel having the composition shown in Table 1 was continuously cast into a 210 m thick slab, and then hot rolled under the conditions shown in Table 2 to form a 2.6N thick hot rolled plate. .
このようにして得た熱間圧延鋼板について浸炭焼入試験
を行った。浸炭焼入性試験方法は、カーボンポテンシャ
ル０．９０％のガス浸炭を８６０℃×９０分行い、次い
で１６０℃の油浴に焼入れして、′表面硬さＨｖ （５
ｋｇＦ＞および有効硬化層深さくＨｖ ５００の位置）
を調査することにより行った。A carburizing and quenching test was conducted on the hot rolled steel sheet thus obtained. The carburizing and hardenability test method was to perform gas carburizing at 860°C for 90 minutes with a carbon potential of 0.90%, and then quench in an oil bath at 160°C to obtain a surface hardness of Hv (5
kgF> and position of effective hardening layer depth Hv 500)
This was done by investigating.
この熱間圧延板の機械的特性および焼入性についての試
験結果を同表にまとめて示す。The test results regarding the mechanical properties and hardenability of this hot rolled plate are summarized in the same table.
同表に示す結果より明らかなように、本発明に係る製造
方法による場合、良好な加工性と焼入性が併せて得られ
るのが分かる。一方、本発明における製造条件を外れた
試験陽２〜６に示すものはいずれも、例えば伸び値で示
される加工性が低下しているか、あるいは有効硬化層深
さで示される焼入れ性が低下している。特に、試験隘２
に示すように、降温温度が９５０℃と高くなると、Ａｌ
Ｎの析出が十分でなく、焼入れ性の低下は免れない。As is clear from the results shown in the table, it can be seen that the manufacturing method according to the present invention provides both good workability and hardenability. On the other hand, all of the test positives 2 to 6, which deviate from the manufacturing conditions of the present invention, have a decrease in workability, as indicated by the elongation value, or a decrease in hardenability, as indicated by the effective hardened layer depth. ing. In particular, exam room 2
As shown in , when the cooling temperature is as high as 950°C, Al
N is not sufficiently precipitated, and hardenability inevitably deteriorates.
また試験患４に示すものは加熱温度が十分でないばかり
か仕上げ温度もＡｒ３点未満であるため、ＡｌＮの粗大
凝集が十分でなくまたフェライト粒が加工されるため加
工性の低下は免れない。In addition, in the case of Test Case 4, not only was the heating temperature insufficient, but also the finishing temperature was below the Ar3 point, so coarse aggregation of AlN was insufficient and ferrite grains were processed, resulting in a decrease in workability.
実庭拠１
鋼成分の加工性および焼入れ性への影響を調査するため
第３表に示す成分の鋼を連続鋳造し厚さ２３０鶴のスラ
ブとし、同表に示す条件で圧延した。Practical basis 1 In order to investigate the influence of steel components on workability and hardenability, steels with the components shown in Table 3 were continuously cast into slabs with a thickness of 230 mm, and rolled under the conditions shown in the table.
焼入性は実施例１と同じ方法で測定した。Hardenability was measured using the same method as in Example 1.
同表に示す結果より明らかなように、Ｃ，ＳｉおよびＭ
ｎが本発明の規定する上限より外れた場合（試験陽４．
６．７）は加工性の劣化が、同じ＜Ｍｎが下限より外れ
た場合はく試験階５）焼入れ性の低下がそれぞれ観察さ
れる。As is clear from the results shown in the same table, C, Si and M
If n is outside the upper limit specified by the present invention (test positive 4.
In case 6.7), deterioration in workability is observed, and in cases where <Mn falls below the lower limit, a decrease in hardenability is observed in case 5).
呈上表 （重量％）presentation table (weight%)
Claims (1)
．１〜０．５％、Ａｌ：０．０１〜０．０４％、Ｎ：０
．００６０％以下、 残部Ｆｅおよび不可避的不純物元素 からなる組成を有するＡｌキルド鋼を連続鋳造し、得ら
れた熱鋳片を７５０℃以上、Ａｒ＿３点以下に降温し、
次いで１０００〜１１５０℃に加熱した後、仕上温度Ａ
ｒ＿３点以上および巻取温度２５０〜５００℃の条件下
で圧延することを特徴とする、浸炭焼入れ性のすぐれた
鋼板の製造方法。[Claims] In weight %, C: 0.10% or less, Si: 0.06% or less, Mn: 0
．． 1-0.5%, Al: 0.01-0.04%, N: 0
．． 0060% or less, the balance consisting of Fe and unavoidable impurity elements is continuously cast, and the temperature of the obtained hot slab is lowered to 750°C or higher and Ar_3 point or lower,
Then, after heating to 1000 to 1150°C, finish temperature A
A method for producing a steel plate with excellent carburizing and hardenability, characterized by rolling under conditions of r_3 points or more and a coiling temperature of 250 to 500°C.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP22384584A JPS61104030A (en) | 1984-10-26 | 1984-10-26 | Manufacture of steel sheet having superior carburization hardenability |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP22384584A JPS61104030A (en) | 1984-10-26 | 1984-10-26 | Manufacture of steel sheet having superior carburization hardenability |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS61104030A true JPS61104030A (en) | 1986-05-22 |
| JPH0553845B2 JPH0553845B2 (en) | 1993-08-11 |
Family
ID=16804621
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP22384584A Granted JPS61104030A (en) | 1984-10-26 | 1984-10-26 | Manufacture of steel sheet having superior carburization hardenability |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS61104030A (en) |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5650785A (en) * | 1979-09-14 | 1981-05-08 | Trw Inc | Method and device for welding stud |
-
1984
- 1984-10-26 JP JP22384584A patent/JPS61104030A/en active Granted
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5650785A (en) * | 1979-09-14 | 1981-05-08 | Trw Inc | Method and device for welding stud |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0553845B2 (en) | 1993-08-11 |
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