JPH04190902A - Manufacture of extremely thick steel plate - Google Patents
Manufacture of extremely thick steel plateInfo
- Publication number
- JPH04190902A JPH04190902A JP32163090A JP32163090A JPH04190902A JP H04190902 A JPH04190902 A JP H04190902A JP 32163090 A JP32163090 A JP 32163090A JP 32163090 A JP32163090 A JP 32163090A JP H04190902 A JPH04190902 A JP H04190902A
- Authority
- JP
- Japan
- Prior art keywords
- slabs
- rolling
- rolled
- thickness
- steel plate
- 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.)
- Pending
Links
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 32
- 239000010959 steel Substances 0.000 title claims abstract description 32
- 238000004519 manufacturing process Methods 0.000 title claims description 11
- 238000009749 continuous casting Methods 0.000 claims abstract description 10
- 238000005096 rolling process Methods 0.000 abstract description 16
- 238000000034 method Methods 0.000 abstract description 11
- 238000003466 welding Methods 0.000 abstract description 10
- 238000003303 reheating Methods 0.000 abstract description 8
- 230000007547 defect Effects 0.000 abstract description 7
- 239000000853 adhesive Substances 0.000 abstract description 2
- 230000001070 adhesive effect Effects 0.000 abstract description 2
- 238000010438 heat treatment Methods 0.000 abstract description 2
- 239000000203 mixture Substances 0.000 description 3
- 239000000126 substance Substances 0.000 description 3
- CURLTUGMZLYLDI-UHFFFAOYSA-N Carbon dioxide Chemical compound O=C=O CURLTUGMZLYLDI-UHFFFAOYSA-N 0.000 description 2
- 230000006835 compression Effects 0.000 description 2
- 238000007906 compression Methods 0.000 description 2
- 238000007796 conventional method Methods 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- 229910002092 carbon dioxide Inorganic materials 0.000 description 1
- 239000001569 carbon dioxide Substances 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 238000002788 crimping Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000001514 detection method Methods 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 238000005498 polishing Methods 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/38—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling sheets of limited length, e.g. folded sheets, superimposed sheets, pack rolling
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/02—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling heavy work, e.g. ingots, slabs, blooms, or billets, in which the cross-sectional form is unimportant ; Rolling combined with forging or pressing
- B21B2001/028—Slabs
Abstract
Description
【発明の詳細な説明】
（産業上の利用分野）
本発明は比較的薄い連続鋳造で製造したスラブ（通常２
００〜３５０ｍｍ）から内部欠陥のない健全な極厚の鋼
１（１００〜２００ｍｍ）を製造する方法に関するもの
である。DETAILED DESCRIPTION OF THE INVENTION (Industrial Application Field) The present invention relates to a relatively thin continuous casting slab (usually 2
The present invention relates to a method for producing sound, extremely thick steel 1 (100 to 200 mm) free of internal defects from steel 1 (100 to 200 mm) from 100 to 350 mm.
鉄鋼業においては厚板ミルに適用することかもっとも好
ましい。この方法で製造した鋼板は通常の方法で製造し
た鋼板と同様に海洋構造物、圧力容器なとに用いること
かできる。In the steel industry, it is most preferable to apply it to plate mills. Steel plates produced by this method can be used in marine structures, pressure vessels, etc. in the same way as steel plates produced by conventional methods.
（従来の技術）
海洋構造物なと溶接構造物の大型化の進行にともなって
、使用される鋼板の厚みはますます増加する傾向にある
。従来、１００ｍｍ以上の厚みを−Ｈする極厚鋼板は鋼
塊鋳造、分塊圧延によってスラブを製造し、これを厚板
圧延することによって製造されていた（例えば特公昭５
ｇ −２７２］号公報）。(Prior Art) As offshore structures and other welded structures become larger in size, the thickness of the steel plates used tends to increase more and more. Conventionally, extra-thick steel plates with a thickness of 100 mm or more with -H were manufactured by manufacturing slabs by ingot casting and blooming rolling, and then rolling the slabs into thick plates (for example,
g-272] Publication).
しかし、二のような極厚鋼板を連続鋳造スラブから、製
造することは容易ではなく、高度の技術を必要とする。However, it is not easy to manufacture extremely thick steel plates such as the one shown in Figure 2 from continuously cast slabs, and requires advanced technology.
これは連続鋳造法で製造できるスラフ厚みか最大で３５
０ ｍｍ程度であり、極厚鋼板を製造する際に、６熱間
圧延時の圧−ド比か十分に出れないためである。圧下比
か不足すると、■スラブの中心部に存在するセンターポ
ロンティの未圧着による内部欠陥（超音波探傷による欠
陥）の発生、■鋼板厚み方向の強度・延性不足、■圧延
鋼板の結晶粒の微細化不足による延靭性の劣化、なとか
生じる。このため、連続鋳造法では極厚鋼板の製造か不
可能とされていた。This is the maximum slough thickness that can be manufactured using the continuous casting method.
This is because when manufacturing extra-thick steel plates, the rolling stock ratio during hot rolling cannot be sufficiently achieved. If the reduction ratio is insufficient, ■ Internal defects (defects detected by ultrasonic testing) may occur due to unbonded center holes in the center of the slab, ■ Insufficient strength and ductility in the thickness direction of the steel plate, ■ Crystal grains in the rolled steel plate may Deterioration of ductility and toughness may occur due to insufficient refinement. For this reason, it was considered impossible to manufacture extremely thick steel plates using the continuous casting method.
（発明が解決しようとする課題う
本発明は連続鋳造法で製造したスラブから極厚鋼板を製
造する方法を提供するものであり、この方法で製造した
スラブは従来法で製造した鋼板と同様に優れた諸特性を
有する。(Problems to be Solved by the Invention) The present invention provides a method for manufacturing extra-thick steel plates from slabs manufactured by continuous casting, and slabs manufactured by this method have the same properties as steel plates manufactured by conventional methods. Has excellent properties.
（課題を解決するための手段）
本発明の要旨は、厚み１５０〜３００ ｍｍに圧延した
連続鋳造法で製造したスラブを２枚重ね合わせ、四周を
溶接してスラブを組立てた後、１０００〜１３００℃の
温度範囲に加熱、圧下比２５以上で圧延することである
。(Means for Solving the Problems) The gist of the present invention is to assemble two slabs manufactured by continuous casting method that have been rolled to a thickness of 150 to 300 mm, and then weld the four circumferences to assemble the slab. C. and rolling at a reduction ratio of 25 or more.
本発明では、とくに鋼の化学成分を限定しないが、極厚
鋼板の強度レベルは４０〜８〇九、厚みは１００〜２０
０ ｍｍを対象とする。In the present invention, the chemical composition of the steel is not particularly limited, but the strength level of the extra-thick steel plate is 40 to 809, and the thickness is 100 to 20.
Target is 0 mm.
以下、本発明について詳細に説明する。The present invention will be explained in detail below.
本発明では、まず、連続鋳造法で製造したスラブ（ＣＣ
スラブ）を厚み１５０〜３００ｍｍに再加熱・圧延しな
ければならない。この理由は、■スラブ中心部に存在す
るセンターポロシティ−の圧着を促進させる、■適切な
スラブ厚みを１１）るためである。このときの圧下比（
＝元のスラブ厚／′圧延スラブ厚）については、とくに
制限はしないか、圧下比≧１．１５とすることかセンタ
ーポロシティーの圧着上好ましい。In the present invention, first, a slab manufactured by a continuous casting method (CC
The slab must be reheated and rolled to a thickness of 150 to 300 mm. The reasons for this are: (1) promoting the compression of the center porosity existing at the center of the slab; and (2) creating an appropriate slab thickness11). The rolling reduction ratio at this time (
=Original slab thickness/'Rolled slab thickness) It is preferable that there is no particular restriction, or that the rolling ratio is 1.15 or more, from the viewpoint of crimping the center porosity.
つきに、二のようにして製造したスラブを２枚重ね合わ
せて四周を溶接し、圧延で分離しないようにする。この
際、接着面はあらかじめ平削、研磨などて平滑にし、か
つ汚れを除去、脱脂することか重要である。また溶接後
、真空ポンプなとて接着面に存在する空気を除去するこ
とか好ましい。At the same time, two slabs manufactured as described in step 2 are stacked together and welded around the four circumferences so that they do not separate during rolling. At this time, it is important to make the adhesive surface smooth by planing or polishing, and to remove dirt and degrease in advance. After welding, it is preferable to use a vacuum pump to remove air present on the bonding surface.
四周溶接法はとくに指定しないか、潜弧溶接、自動・半
自動炭酸カス溶接、手溶接などが考えられる。The four-circle welding method may not be specified, or it may include submerged arc welding, automatic/semi-automatic carbon dioxide scum welding, manual welding, etc.
溶接によって組立てたスラブは、１０００〜１３００℃
に再加熱後、圧下比２．５以上で圧延しなければならな
い。再加熱温度と圧延温度を同時に限定することによっ
て、■センターポロシティーの完全な圧着、■上下スラ
ブの完全な冶金学的結合が可能となり、鋼板の内部欠陥
をなくすことができる。Slabs assembled by welding are heated to 1000-1300℃.
After reheating, it must be rolled at a reduction ratio of 2.5 or more. By limiting the reheating temperature and the rolling temperature at the same time, it is possible to achieve (1) complete compression of the center porosity, (2) complete metallurgical bonding of the upper and lower slabs, and eliminate internal defects in the steel plate.
二のとき再加熱温度か１０００℃以下であったり、また
は圧下比か２．５以下であるとセンターポロシティ−の
圧着や上下スラブの完全な冶金学的結合は不可能となる
。なお圧下比は大きいはと好ましいか、実用上６．０以
下か好ましい。一方、再加熱７８度か１３００’Ｃを超
えるとバーニング現象か起こり、表面性状の良好な鋼板
の製造が困難になる。If the reheating temperature is below 1000°C or the rolling reduction ratio is below 2.5, it will be impossible to press the center porosity or completely metallurgically bond the upper and lower slabs. It is preferable that the rolling reduction ratio is large, and in practical terms, it is preferably 6.0 or less. On the other hand, when reheating exceeds 78 degrees or 1300'C, a burning phenomenon occurs, making it difficult to produce a steel plate with good surface properties.
なお、本発明では、鋼の化学成分や上記以外の鋼板製造
条件（圧延温度、冷却条件、熱処理の有無など）につい
ては、本発明の必須条件でないため、とくに限定しない
。例えば制御圧延や加速冷却の適用は、鋼の強靭化に有
効であることは周知の通りである。Note that, in the present invention, the chemical composition of the steel and the steel plate manufacturing conditions other than those described above (rolling temperature, cooling conditions, presence or absence of heat treatment, etc.) are not particularly limited, since they are not essential conditions of the present invention. For example, it is well known that controlled rolling and accelerated cooling are effective for toughening steel.
（実 施 例）
転炉一連続鋳造で表１に示す化学成分のスラブ（厚さ２
５０．３００ｍｍ）を製造し、これを１２００℃に再加
熱・圧延し、その片面を機械的に平削、脱脂処理した。(Example) A slab with the chemical composition shown in Table 1 (thickness 2
50.300 mm), which was reheated and rolled at 1200°C, and one side of which was mechanically planed and degreased.
このようにして製造したスラブを２枚重ね合わせ、四周
を潜弧溶接後、接着面の空気を除去した。Two slabs thus produced were stacked together, and after submerged arc welding on all four sides, the air on the bonded surfaces was removed.
組立てたスラブ（厚み２２０〜５００ｍｎ＋）は種々の
再加熱温度、圧下比で圧延後、機械的性質を調査した。The assembled slabs (thickness 220-500 mm+) were rolled at various reheating temperatures and rolling reduction ratios, and then their mechanical properties were investigated.
結果を表２に示す。The results are shown in Table 2.
表 １
０．１２０．２８１，５００．０＋００．００１０５０
０．５００，０３０．０１１０．００５０本発明鋼は、
鋼板厚み方向（板厚方向）の強度、絞り値（延性）に優
れ、ＵＳＴ （超音波探１易）による欠陥も皆無である
。これに対して比較鋼では、再加熱温度か低く過きたり
（鋼５）、圧下比か小さ過ぎるために（ｐＡ６． ７）
、板厚方向の強度、延性か劣り、ＵＳＴによる内部欠
陥も多く発生している。Table 1 0.120.281,500.0+00.001050
0.500,030.0110.0050 The steel of the present invention is
It has excellent strength and reduction of area (ductility) in the steel sheet thickness direction, and has no defects caused by UST (ultrasonic detection). On the other hand, in the comparison steel, the reheating temperature was too low (Steel 5) and the reduction ratio was too low (pA 6.7).
, strength and ductility in the thickness direction are poor, and many internal defects due to UST occur.
（発明の効果）
本発明により、連続鋳造法では製造不可能であった種々
の強度・靭性レヘルの極厚鋼板の製造が可能となった。(Effects of the Invention) According to the present invention, it has become possible to manufacture extremely thick steel plates with various levels of strength and toughness, which were impossible to manufacture by continuous casting.
その結果、省エネルギー・省工程で品質の良い極厚鋼板
が大量に提供できるようになった。As a result, we are now able to provide large quantities of high-quality, extra-thick steel plates that save energy and process.
Claims (1)
たスラブを２枚重ね合わせ、四周を溶接してスラブを組
立てた後、１０００〜１３００℃の温度範囲に加熱、圧
下比２．５以上で圧延することを特徴とする極厚鋼板の
製造方法。Two slabs rolled to a thickness of 150 to 300 mm manufactured by continuous casting are stacked together and the four circumferences are welded to assemble the slab, then heated to a temperature range of 1000 to 1300°C and rolled at a reduction ratio of 2.5 or more. A method for producing extra-thick steel plate characterized by the following.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP32163090A JPH04190902A (en) | 1990-11-26 | 1990-11-26 | Manufacture of extremely thick steel plate |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP32163090A JPH04190902A (en) | 1990-11-26 | 1990-11-26 | Manufacture of extremely thick steel plate |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH04190902A true JPH04190902A (en) | 1992-07-09 |
Family
ID=18134652
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP32163090A Pending JPH04190902A (en) | 1990-11-26 | 1990-11-26 | Manufacture of extremely thick steel plate |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH04190902A (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2006320923A (en) * | 2005-05-18 | 2006-11-30 | Jfe Steel Kk | Method for manufacturing thick steel plate having excellent low-temperature toughness |
| WO2015140846A1 (en) * | 2014-03-20 | 2015-09-24 | Ｊｆｅスチール株式会社 | High toughness and high tensile strength thick steel plate and production method therefor |
| US10358688B2 (en) | 2014-04-24 | 2019-07-23 | Jfe Steel Corporation | Steel plate and method of producing same |
-
1990
- 1990-11-26 JP JP32163090A patent/JPH04190902A/en active Pending
Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2006320923A (en) * | 2005-05-18 | 2006-11-30 | Jfe Steel Kk | Method for manufacturing thick steel plate having excellent low-temperature toughness |
| JP4626394B2 (en) * | 2005-05-18 | 2011-02-09 | Ｊｆｅスチール株式会社 | Manufacturing method of thick steel plate with excellent low temperature toughness |
| WO2015140846A1 (en) * | 2014-03-20 | 2015-09-24 | Ｊｆｅスチール株式会社 | High toughness and high tensile strength thick steel plate and production method therefor |
| CN106102940A (en) * | 2014-03-20 | 2016-11-09 | 杰富意钢铁株式会社 | Heavy wall high tenacity high-tensile steel and manufacture method thereof |
| EP3120941A4 (en) * | 2014-03-20 | 2017-03-15 | JFE Steel Corporation | High toughness and high tensile strength thick steel plate and production method therefor |
| JPWO2015140846A1 (en) * | 2014-03-20 | 2017-04-06 | Ｊｆｅスチール株式会社 | Thick and high toughness high strength steel sheet and method for producing the same |
| US10443110B2 (en) | 2014-03-20 | 2019-10-15 | Jfe Steel Corporation | High toughness and high tensile strength thick steel plate and production method therefor |
| US10358688B2 (en) | 2014-04-24 | 2019-07-23 | Jfe Steel Corporation | Steel plate and method of producing same |
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