JPS5959827A - Manufacture of hot-rolled steel plate with superior processability - Google Patents
Manufacture of hot-rolled steel plate with superior processabilityInfo
- Publication number
- JPS5959827A JPS5959827A JP16764582A JP16764582A JPS5959827A JP S5959827 A JPS5959827 A JP S5959827A JP 16764582 A JP16764582 A JP 16764582A JP 16764582 A JP16764582 A JP 16764582A JP S5959827 A JPS5959827 A JP S5959827A
- Authority
- JP
- Japan
- Prior art keywords
- hot
- rolling
- rolled steel
- rolled
- less
- 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
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
Description
【発明の詳細な説明】
本発明は成形性の優れた加工用熱延鋼板の製造方法に関
するものである。DETAILED DESCRIPTION OF THE INVENTION The present invention relates to a method for producing a hot-rolled steel sheet for processing with excellent formability.
従来、加工用鋼板としては成形性のすぐれた冷延鋼板が
一般に使用されているが、最近コスト低減などの理由に
よシ、成形性のすぐれた加工用熱延鋼板が要望されるよ
うになった。Traditionally, cold-rolled steel sheets with excellent formability have been generally used as processing steel sheets, but recently there has been a demand for hot-rolled steel sheets with excellent formability for reasons such as cost reduction. Ta.
現在使用されている加工用熱延鋼板は伸びの点でけ冷延
鋼板と比較しても劣らぬ特性を示すが、従来の熱延条件
ではｒ値が０６８前後が一般で、深絞シ性においては冷
延鋼板よシかなシ劣っている。The hot-rolled steel sheets currently used for processing exhibit properties that are comparable to cold-rolled steel sheets in terms of elongation, but under conventional hot-rolling conditions, the r value is generally around 068, making it difficult to deep draw. It is inferior to cold-rolled steel sheets.
一方、すぐれた加工性を有する熱延鋼板の製造法は従来
Ａｒ３変態点以上で加工されることが前提になっている
。その理由は通常の圧下条件ではＡｒ３変態点以下で圧
延すると表面が粗粒組織となシ、機械的性質の劣化が起
るためである。この問題は特に薄手熱延鋼板の製造にお
ける板温管理条件を厳しいものにし、エネルギ経済的に
不利であるスラブの高温加熱を強いる結果になっている
。On the other hand, conventional methods for producing hot-rolled steel sheets with excellent workability have been based on the premise that the steel sheets are processed at an Ar3 transformation point or higher. The reason for this is that under normal rolling conditions, rolling below the Ar3 transformation point results in a coarse grain structure on the surface and deterioration of mechanical properties. This problem has made the plate temperature control conditions particularly severe in the production of thin hot rolled steel sheets, forcing the slab to be heated to high temperatures, which is disadvantageous in terms of energy economy.
一方、プレス加工性の優れた熱延鋼板を得るには普通粒
度番号８程度の粒度がよいとされている晶粒度を粒度番
号８前後にすることは難しい。しかしこれ以上の高温で
捲取るとスケール及び表面欠陥の問題が急増する。On the other hand, in order to obtain a hot-rolled steel sheet with excellent press workability, it is difficult to set the grain size to around 8, although it is generally said that a grain size of around 8 is good. However, when rolled at higher temperatures, problems of scale and surface defects rapidly increase.
本発明はこれらの問題点を有利に解決したものであり、
その要旨はＣＤ、 １ ％以下、Ｃ以外の合金含有量６
％以下である鋼を熱間圧延するに際Ｉ７、核熱間圧延の
終段において、６００℃〜（Ａｒ３−）１００℃）の温
度域で２秒以内に１回または２回以上の合計圧下率が６
０％以上の圧延を行い、核熱間圧延終了後、２０℃／Ｓ
以下の速度で冷却し２．７００〜５００℃の温度域で捲
取ることを特徴とする加工性の優れた熱延鋼板の製造方
法である。The present invention advantageously solves these problems,
The gist is CD, 1% or less, alloy content other than C6
% or less, I7, in the final stage of nuclear hot rolling, one or more total rolling reductions within 2 seconds in a temperature range of 600 ° C to (Ar3-) 100 ° C) rate is 6
0% or more rolling and after completion of core hot rolling, 20℃/S
This is a method for producing a hot-rolled steel sheet with excellent workability, which is characterized by cooling at the following rate and rolling in a temperature range of 2.700 to 500°C.
以下、本発明の詳細な説明する。The present invention will be explained in detail below.
本発明者達は本発明で規定した成分範囲の材料□に、所
定の温度域で大圧下を加えると、該材料に加Ｉ時の変態
が生ずるばかりでなく、一部重復してフェライトが再結
晶するという新しい知見を得たのである。そして、この
再結晶したフェライトは従来の圧延条件下で本発明成分
材料では到底得られなかった極細粒組織を示すことを発
見した。The inventors of the present invention have discovered that when a large pressure is applied in a predetermined temperature range to a material □ having the composition range specified in the present invention, not only does the material undergo transformation at the time of I application, but also a portion of the material overlaps and the ferrite regenerates. They obtained new knowledge that crystallization occurs. It was also discovered that this recrystallized ferrite exhibits an extremely fine grain structure that could not be obtained with the component materials of the present invention under conventional rolling conditions.
即ち、適切な温度域において、圧下率が６０チを越える
と動的変態が生じ、６〜４μｍ以下の平均フェライト粒
径が得られるようになり、更に圧下率が増すと、細粒化
は一層著るしくなり、６５％以上ではフェライトの動的
再結晶も加わる司能性があシ、２〃ｍまたはそれ以下の
超微細粒組織が得られるのである。このようにして得ら
れたフェライト組織は粒の形が著るしい伸長を示さず、
殆んど等方の極細粒である。That is, in an appropriate temperature range, when the rolling reduction rate exceeds 60 mm, dynamic transformation occurs and an average ferrite grain size of 6 to 4 μm or less can be obtained, and as the rolling reduction rate increases further, the grain size becomes even finer. At 65% or more, dynamic recrystallization of ferrite is also added, and an ultrafine grain structure of 2 m or less is obtained. The ferrite structure obtained in this way does not show significant elongation in grain shape,
Almost isotropic ultrafine grains.
また、粒界近傍の優先結晶方位が（１１１）であると言
う実験結果が示唆したように、かかる極細粒フェライト
組織は（１１１）方位が多く、それが粒成長した組織も
この結晶方位成分が従来の熱延鋼板より多く存在し、〒
値が１に近いかそれ以上の値を示す使れた深絞り性を示
す。そして強度−延性バランスも従来の熱延鋼板と比較
して同レベルかイれ以上を表すことが分かつた。Furthermore, as suggested by the experimental results that the preferred crystal orientation near grain boundaries is (111), the ultrafine grain ferrite structure has many (111) orientations, and the structures in which these grains have grown also have this crystal orientation component. There are more of them than conventional hot rolled steel sheets,
Indicates good deep drawability with a value close to 1 or greater. It was also found that the strength-ductility balance was at the same level or better than that of conventional hot-rolled steel sheets.
まだ、極細粒組織は一度粒成長が始まると粗粒のものよ
シ粒成長速度が速く、さらに、結晶方位が上述したよう
に（１１１）の方位が多くなっているので、捲取温度を
高くしなくても、良加工性を表わす所望の粒度及び方位
を得ることができる。このように、本発明は超微細粒鋼
の圧延直後の冷却速度及び捲取温度を規制して、粒成長
させ、加工性の優れた熱延鋼板を提供するものである。However, once grain growth begins in the ultra-fine grain structure, the grain growth rate is faster than that in the coarse-grain structure, and as mentioned above, the crystal orientation is more likely to be (111), so it is necessary to raise the winding temperature. A desired grain size and orientation indicating good processability can be obtained even without this. In this way, the present invention regulates the cooling rate and winding temperature of ultrafine grained steel immediately after rolling to allow grain growth and provide a hot rolled steel sheet with excellent workability.
以下本発明の構成要件の限定理由を述べる。本発明鋼の
化学成分を規定した理由は次の通りである。炭素量を０
１％以下にした理由は、これ以上炭素が入ると炭化物が
増加して加工性を劣化させるためである。一方炭素以外
の合金元素の金側を５％以下に規定した理由は、合金元
素を添加すると一般に再結晶温度が高くなり、一部の元
素を除きＡｒ３変態点を下げるため本発明鋼の製造温度
範囲が挟まり、製造条件が厳しくなるばかりでなく、細
粒化そのものを抑制する。又圧延後の粒成長も抑制する
ので捲取温度を高めなければならなくなる。その上一般
に合金元素が添加されると加工性を劣化するので合計で
′５％以上の合金元素を添加するのは本発明の主旨に反
する。以」二の現象は特にＰ、Ｓ、Ｎ等が顕著に影響を
与えるので、これらの元素は本発明鋼では特に少い方が
有利である。The reasons for limiting the constituent elements of the present invention will be described below. The reason for specifying the chemical composition of the steel of the present invention is as follows. Carbon content 0
The reason why it is set to 1% or less is that if more carbon is added, carbides will increase and workability will deteriorate. On the other hand, the reason why the gold side of alloying elements other than carbon is specified to be 5% or less is that adding alloying elements generally increases the recrystallization temperature, and with the exception of some elements, the Ar3 transformation point is lowered, so the manufacturing temperature of the steel of the present invention is Not only does this narrow the range and make manufacturing conditions stricter, but it also suppresses grain refinement itself. In addition, since grain growth after rolling is also suppressed, the winding temperature must be increased. Furthermore, since the addition of alloying elements generally deteriorates workability, it is contrary to the spirit of the present invention to add more than 5% of alloying elements in total. Since P, S, N, etc. have a significant influence on the above two phenomena, it is particularly advantageous to have a small amount of these elements in the steel of the present invention.
水元明妊おいて規定した圧延終段において、６００℃〜
（Ａｔ３＋１００℃）の温度域で２秒以内に１回または
２回以上の合計圧下率が６０％以上と言う条件は、フェ
ライトの極細粒組織を造シ出す必要条件である０その生
成機構としては加工誘起変態及びフェライトの動的及び
凝動的再結晶などの現象に関連するものである。上記条
件の圧下率が６０％以下であるとフェライトが熱延工程
で十分再結晶せず加工フェライト組織が生成し、加工性
の著しい劣化が起る。又加工温度が６００℃以下に下が
るとやはり同様のことが起る。一方加工温度が（Ａｒａ
＋ １００℃）以上ではフェライト粒の細粒化はオー
ステナイト粒の細粒化によシフエライトの生成サイトを
増加させることに基〈もので本発明の意図とは異る。At the final stage of rolling specified by Akira Mizumoto, 600℃~
The condition that the total rolling reduction rate of 60% or more once or twice within 2 seconds in the temperature range of (At3 + 100℃) is a necessary condition for producing the ultrafine grain structure of ferrite. It is related to phenomena such as deformation-induced transformation and dynamic and condensation recrystallization of ferrite. If the rolling reduction under the above conditions is 60% or less, ferrite will not be sufficiently recrystallized in the hot rolling process, resulting in formation of a processed ferrite structure, resulting in significant deterioration of workability. The same thing happens when the processing temperature drops below 600°C. On the other hand, the processing temperature (Ara
+100° C.) or higher, the refinement of ferrite grains is based on increasing the number of sipherite formation sites by refining austenite grains, which is different from the intention of the present invention.
ここでＡｒ３点は次式によって表わされる。Here, the Ar3 points are expressed by the following equation.
Ａ、ｒ３＝ ９１６−５０９Ｃ＋２７ Ｓｉ −６４Ｍ
ｎなお、６０％以上の圧下は１・ξスで加えるのが最も
望ましいが短時間であれば多・ξスで加えた累積歪でも
ほぼこれに近い効果があることが確認された。このパス
間時゛間は２秒以内でおればよいことも確認された。ま
た、か＼る圧延は圧延による粗粒化を防止する意味で熱
延最終段階で６０％以−トの圧延を行わなければならな
い。A, r3=916-509C+27Si-64M
Although it is most desirable to apply a reduction of 60% or more in 1·ξ steps, it has been confirmed that for a short period of time, cumulative strain applied in many·ξ steps can have almost the same effect. It was also confirmed that the time between passes should be within 2 seconds. In addition, such rolling must be carried out at a rolling rate of 60% or more in the final stage of hot rolling in order to prevent grain coarsening due to rolling.
次に、圧延後、捲取１での間の冷却速度を２０℃／ ｓ
ｅｃ以下とした理由はこれ以上の冷速では焼入組織の発
生によって加工性が劣化するためである。Next, after rolling, the cooling rate during winding 1 was set to 20°C/s.
The reason for setting it below ec is that if the cooling rate is higher than this, the workability will deteriorate due to the generation of quenched structure.
冷却後の捲取温度を７００℃以下に限定した理由は高温
捲取による諸問題、たとえばスケール、こし折れ、表面
欠陥など、を防ぐためであり、本発明鋼の特徴である極
細粒組織は７００℃以下の捲取でも十分粒成長を起し、
加工用鋼板として適当とされる粒度番号８番が容易に得
られる。The reason why the winding temperature after cooling is limited to 700°C or less is to prevent various problems caused by high-temperature winding, such as scale, cracking, and surface defects. Grain growth occurs even when rolled at temperatures below ℃,
Grain size No. 8, which is suitable for processing steel plates, can be easily obtained.
址だ、捲取温度の下限を５００℃にしたのは、。That's why we set the lower limit of the winding temperature to 500℃.
これ以下では炭化物が十分析出せず粒内に炭素が固溶さ
れ加工性を劣化させるためである。This is because if it is less than this, not enough carbides can be extracted, and carbon is solidly dissolved in the grains, deteriorating workability.
次に本発明を実施例に基き詳細に説明する。第１表に示
す化学成分の鋼に種々の圧延・冷却を与えた結果を第３
表に示す。Next, the present invention will be explained in detail based on examples. The results of various rolling and cooling treatments of steel with the chemical composition shown in Table 1 are shown in Table 3.
Shown in the table.
圧延は第２表の・モススケジュールに従って連続圧延し
た。The rolling was carried out continuously according to the Moss schedule shown in Table 2.
第２表 ノξススケジュ′−ル
Ｆ６の回転数は表６のｄの場合のみ７５０ ｍｐｍ、そ
の他は１２００ ｒｎｐｍである。Table 2 No. ξ Schedule The rotation speed of F6 is 750 mpm only in case d of Table 6, and 1200 rnpm in other cases.
本発明範囲内のａ、ｂ、ｅの鋼はいずれも極細粒組織形
成後、粒度番号８前後に粒成長し、３４に２／−以下の
強度を示す。一方これらの鋼は強度−延性バランスが良
いばかシでなくｒ値も１に近く良加工性を示す。一方、
本発明範囲外で圧延・冷却を行った試料は粒成長が著し
く肌荒れを起した！ｌ） （Ｃ）、加工組織を示したＤ
（ｄ）、粒成長が抑制され過ぎたシして（ｆＸｇ）、本
発明鋼の意図する特性が得られない。Steels a, b, and e within the scope of the present invention all grow grains to a grain size number of about 8 after forming an ultrafine grain structure, and exhibit a strength of 34 and 2/- or less. On the other hand, these steels do not have a good balance of strength and ductility, have an r value close to 1, and exhibit good workability. on the other hand,
Samples rolled and cooled outside the scope of the present invention had significant grain growth and rough skin! l) (C), D showing processed structure
(d) Grain growth is too suppressed (fXg), making it impossible to obtain the intended properties of the steel of the present invention.
以上述べた本発明の製造法に従えばホットコイル全域に
おいてほぼ均一な材質が得られ、ｒ値も１に近いか、そ
れ以上の値を示す加工性の良い熱延鋼板を得ることがで
きる。そして、圧延後の冷却条件を変えることによって
フェライト粒径を広範囲に変えられるので比較的簡単に
用途に合った加工用熱延鋼板を任意に造り込むことが可
能である。その上、本発明鋼は粒成長が比較的低い温度
でも顕著に進行するので、捲取温度を高くする必要がな
く、スケール及び表面欠陥の少ない鋼が得られる。又本
発明鋼の粒径は広範囲な温度域で相大粒がないので、従
来の加工用熱延鋼板の製造において問題とされている全
板厚・板幅に対してＡｒ３変態点以上の温度に保持しな
ければならないと貫う厳しい板温管理の必要がなく、従
って、１２咽程度の加工用薄手熱延鋼板の製造が著しく
容易になるばかりでなく、スラブの低温加熱化にも寄力
しうるなど本発明は工業的効果が極めて大きいものであ
る。According to the manufacturing method of the present invention described above, a substantially uniform material can be obtained over the entire hot coil area, and a hot rolled steel sheet with good workability and an r value close to 1 or higher can be obtained. Since the ferrite grain size can be varied over a wide range by changing the cooling conditions after rolling, it is relatively easy to create a hot-rolled steel sheet suitable for the intended use. Furthermore, in the steel of the present invention, grain growth progresses significantly even at relatively low temperatures, so there is no need to increase the winding temperature, and steel with fewer scales and surface defects can be obtained. In addition, the grain size of the steel of the present invention has no large grains in a wide temperature range, so it can be used at temperatures above the Ar3 transformation point for the total thickness and width, which are problems in the production of conventional hot-rolled steel sheets for processing. There is no need to maintain strict plate temperature control, which not only makes it significantly easier to manufacture thin hot-rolled steel sheets with a thickness of about 12 mm, but also contributes to lower temperature heating of slabs. The present invention has extremely large industrial effects.
Claims (1)
を熱間圧延するに際し、該熱間圧延の終段において、６
０［３℃〜（Ａｒ３ ＋ １０．０℃）の温度域で２秒
以内に１回まだは２回以上の合計圧下率が６０％以上の
圧延を行い、該熱間圧延終了後、２０℃／Ｓ 以下の速
度で冷却し、７００〜５００℃の温度域で捲取ることを
特徴とする加工性の優れた熱延鋼板の製造方法。When hot rolling steel having a CD of 1% or less and a content of alloys other than C of 6 or less, in the final stage of the hot rolling, 6.
Rolling is performed once or twice or more at a total reduction rate of 60% or more within 2 seconds in a temperature range of 0[3°C to (Ar3 + 10.0°C), and after the hot rolling is completed, the rolling process is carried out at 20°C. A method for producing a hot-rolled steel sheet with excellent workability, characterized by cooling at a rate of less than /S and rolling at a temperature range of 700 to 500°C.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP16764582A JPS5959827A (en) | 1982-09-28 | 1982-09-28 | Manufacture of hot-rolled steel plate with superior processability |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP16764582A JPS5959827A (en) | 1982-09-28 | 1982-09-28 | Manufacture of hot-rolled steel plate with superior processability |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS5959827A true JPS5959827A (en) | 1984-04-05 |
| JPS6141970B2 JPS6141970B2 (en) | 1986-09-18 |
Family
ID=15853602
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP16764582A Granted JPS5959827A (en) | 1982-09-28 | 1982-09-28 | Manufacture of hot-rolled steel plate with superior processability |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS5959827A (en) |
Cited By (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS59107023A (en) * | 1982-12-09 | 1984-06-21 | Nippon Steel Corp | Manufacture of hyperfine-grained hot-rolled steel plate |
| JPS613845A (en) * | 1984-06-18 | 1986-01-09 | Nippon Steel Corp | Manufacture of steel sheet superior in deep drawability |
| JPS613844A (en) * | 1984-06-18 | 1986-01-09 | Nippon Steel Corp | Manufacture of hot rolled steel sheet superior in formability |
| JPS6148531A (en) * | 1984-08-13 | 1986-03-10 | Nippon Steel Corp | Manufacture of hot-rolled low-carbon steel sheet having superior deep drawability |
| JPS61119621A (en) * | 1984-11-16 | 1986-06-06 | Nippon Steel Corp | Manufacture of cold rolled steel sheet for deep drawing |
| JPS61204320A (en) * | 1985-03-06 | 1986-09-10 | Kawasaki Steel Corp | Production of as-rolled thin steel sheet for working having excellent ridging resistnace |
| JPS61204328A (en) * | 1985-03-06 | 1986-09-10 | Kawasaki Steel Corp | Production of as-rolled thin steel sheet for working having excellent ridging resistance and corrosion resistance |
| JPS61204322A (en) * | 1985-03-06 | 1986-09-10 | Kawasaki Steel Corp | Production of as-rolled thin steel sheet for working having small plane anisotropy and excellent ridging resistance |
| JPS61204323A (en) * | 1985-03-06 | 1986-09-10 | Kawasaki Steel Corp | Production of as-rolled thin steel sheet for working having small plane anisotropy and excellent ridging resistance |
| JPS6213534A (en) * | 1985-03-06 | 1987-01-22 | Kawasaki Steel Corp | Manufacture of as-rolled steel sheet for working having superior ridging resistance and bulgeability |
-
1982
- 1982-09-28 JP JP16764582A patent/JPS5959827A/en active Granted
Cited By (16)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS59107023A (en) * | 1982-12-09 | 1984-06-21 | Nippon Steel Corp | Manufacture of hyperfine-grained hot-rolled steel plate |
| JPS625212B2 (en) * | 1982-12-09 | 1987-02-03 | Nippon Steel Corp | |
| JPS613845A (en) * | 1984-06-18 | 1986-01-09 | Nippon Steel Corp | Manufacture of steel sheet superior in deep drawability |
| JPS613844A (en) * | 1984-06-18 | 1986-01-09 | Nippon Steel Corp | Manufacture of hot rolled steel sheet superior in formability |
| JPH0138855B2 (en) * | 1984-06-18 | 1989-08-16 | Nippon Steel Corp | |
| JPS6148531A (en) * | 1984-08-13 | 1986-03-10 | Nippon Steel Corp | Manufacture of hot-rolled low-carbon steel sheet having superior deep drawability |
| JPS61119621A (en) * | 1984-11-16 | 1986-06-06 | Nippon Steel Corp | Manufacture of cold rolled steel sheet for deep drawing |
| JPS61204323A (en) * | 1985-03-06 | 1986-09-10 | Kawasaki Steel Corp | Production of as-rolled thin steel sheet for working having small plane anisotropy and excellent ridging resistance |
| JPS61204322A (en) * | 1985-03-06 | 1986-09-10 | Kawasaki Steel Corp | Production of as-rolled thin steel sheet for working having small plane anisotropy and excellent ridging resistance |
| JPS6213534A (en) * | 1985-03-06 | 1987-01-22 | Kawasaki Steel Corp | Manufacture of as-rolled steel sheet for working having superior ridging resistance and bulgeability |
| JPS61204328A (en) * | 1985-03-06 | 1986-09-10 | Kawasaki Steel Corp | Production of as-rolled thin steel sheet for working having excellent ridging resistance and corrosion resistance |
| JPS61204320A (en) * | 1985-03-06 | 1986-09-10 | Kawasaki Steel Corp | Production of as-rolled thin steel sheet for working having excellent ridging resistnace |
| JPH0257128B2 (en) * | 1985-03-06 | 1990-12-04 | Kawasaki Steel Co | |
| JPH0257129B2 (en) * | 1985-03-06 | 1990-12-04 | Kawasaki Steel Co | |
| JPH0257132B2 (en) * | 1985-03-06 | 1990-12-04 | Kawasaki Steel Co | |
| JPH0257130B2 (en) * | 1985-03-06 | 1990-12-04 | Kawasaki Steel Co |
Also Published As
| Publication number | Publication date |
|---|---|
| JPS6141970B2 (en) | 1986-09-18 |
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