JPH032322A - Manufacture of steel plate having excellent brittle fracture-propagation stop characteristics - Google Patents
Manufacture of steel plate having excellent brittle fracture-propagation stop characteristicsInfo
- Publication number
- JPH032322A JPH032322A JP2450990A JP2450990A JPH032322A JP H032322 A JPH032322 A JP H032322A JP 2450990 A JP2450990 A JP 2450990A JP 2450990 A JP2450990 A JP 2450990A JP H032322 A JPH032322 A JP H032322A
- Authority
- JP
- Japan
- Prior art keywords
- slab
- point
- thickness
- back surfaces
- 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.)
- Granted
Links
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 39
- 239000010959 steel Substances 0.000 title claims abstract description 39
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 14
- 238000001816 cooling Methods 0.000 claims abstract description 41
- 238000005096 rolling process Methods 0.000 claims abstract description 28
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims abstract description 21
- 239000002344 surface layer Substances 0.000 claims abstract description 16
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 11
- 238000009749 continuous casting Methods 0.000 claims abstract description 10
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 9
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 7
- 229910052802 copper Inorganic materials 0.000 claims abstract description 5
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 5
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 5
- 238000003303 reheating Methods 0.000 claims description 18
- 229910052804 chromium Inorganic materials 0.000 abstract description 2
- 229910052742 iron Inorganic materials 0.000 abstract description 2
- 229910000859 α-Fe Inorganic materials 0.000 description 7
- 238000000034 method Methods 0.000 description 6
- 239000013078 crystal Substances 0.000 description 5
- 230000000694 effects Effects 0.000 description 4
- 230000009466 transformation Effects 0.000 description 4
- 230000006866 deterioration Effects 0.000 description 3
- 238000001953 recrystallisation Methods 0.000 description 3
- 229910000746 Structural steel Inorganic materials 0.000 description 2
- 229910001566 austenite Inorganic materials 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 239000002304 perfume Substances 0.000 description 2
- 238000007670 refining Methods 0.000 description 2
- 229910001208 Crucible steel Inorganic materials 0.000 description 1
- 229910015179 MoB Inorganic materials 0.000 description 1
- 239000010953 base metal Substances 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 230000000644 propagated effect Effects 0.000 description 1
- 238000004080 punching Methods 0.000 description 1
- 230000001105 regulatory effect Effects 0.000 description 1
- 230000003014 reinforcing effect Effects 0.000 description 1
- 230000000630 rising effect Effects 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
Landscapes
- Heat Treatment Of Steel (AREA)
Abstract
Description
【発明の詳細な説明】
〈産業上の利用分野〉
本発明は優れた脆性亀裂伝播停止特性を有する構造用鋼
板の製造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 method for manufacturing a structural steel plate having excellent brittle crack propagation arresting properties.
〈従来の技術〉
鋼板に発生する脆性亀裂は、主亀裂が先行亀裂に連結し
て伝播する。<Prior Art> When a brittle crack occurs in a steel plate, the main crack is connected to a preceding crack and propagates.
この連結は結晶粒界のテアリングと呼ばれる延性破壊で
形成されるが、その時テアリングの延性破壊により亀裂
伝播エネルギーが吸収される。This connection is formed by ductile fracture called grain boundary tearing, and at this time, crack propagation energy is absorbed by the ductile fracture of tearing.
この吸収能は、結晶粒径の微細化により上記延性破壊の
機会が増えて高まり、亀裂の減速効果が向上し、上記脆
性亀裂伝播停止特性を向上する。This absorptive capacity is enhanced by increasing the chance of the ductile fracture due to the refinement of the grain size, improving the crack slowing effect and improving the brittle crack propagation arresting property.
実際に脆性亀裂伝播停止特性の向上に大きく寄与するの
は、脆性亀裂伝播時に鋼板表層部に発生するシアリップ
と榊する塑性変形であり、このシアリップも結晶粒の微
細化で伝播する脆性亀裂が有する伝播エネルギーの吸収
能が増大する。In fact, what greatly contributes to improving the brittle crack propagation arresting properties are the shear lip and plastic deformation that occur in the surface layer of the steel sheet during brittle crack propagation, and this shear lip is also caused by the brittle crack that propagates due to grain refinement. The ability to absorb propagated energy increases.
そこで効果的な結晶粒の微細化の試みが種々行われてい
る。Therefore, various attempts have been made to effectively refine crystal grains.
これを実現するため、例えば特開昭61−235534
号公報は、第1図(a)及び(d)に示す如く、温度が
Acx点以上の鋳片鋳片表面から中心部へ板厚の1/8
程度の表層部をAr3点以下に冷却して該鋳片の表層部
と中心部に温度差をつけた侭圧延を開始し、該圧延中又
は圧延後に咳鋳片厚の全域をAc2点以上に復熱し、E
SSO試験による一20’Cにおける脆性亀裂伝播停止
特性にcaが460〜960 kg・14″程度の優れ
た厚w4板を製造する方法を提案している。In order to realize this, for example, Japanese Patent Application Laid-Open No. 61-235534
As shown in Figures 1 (a) and (d), the publication discloses that 1/8 of the thickness of the slab is extended from the surface of the slab whose temperature is above the Acx point to the center.
Start rolling with a temperature difference between the surface layer and the center of the slab by cooling the surface layer of the slab to a point of Ar3 or lower, and bring the entire thickness of the slab to a point of Ac2 or higher during or after rolling. Reheat and E
We are proposing a method for producing a W4 plate with an excellent brittle crack propagation arresting property at -20'C determined by SSO test and having a ca of about 460 to 960 kg/14''.
しかし前記特開昭61−235534号公報の提案は、
鋳片全域をAc3点以上に復熱させるので復熱時間が長
くなって生産性が低下すると共に、Ar3点以下に冷却
される範囲が少なく、従ってオーステナイトからフェラ
イトへの逆変態及び再結晶が利用できる領域が狭く、結
晶粒の微細化、組織の微細化が不十分となり、シアリッ
プ効果が充分発揮されず、これ等が実用上の妨げとなっ
ている。However, the proposal of JP-A No. 61-235534 is
Since the entire area of the slab is reheated to the Ac3 point or higher, the reheating time becomes longer and productivity decreases, and the area that is cooled to the Ar3 point or lower is small, so reverse transformation from austenite to ferrite and recrystallization are utilized. The resulting area is narrow, crystal grain refinement and structure refinement are insufficient, and the shear lip effect is not fully exhibited, which is a hindrance in practical use.
〈発明が解決しようとする課題〉
本発明は上記した従来技術の問題点を解消すると共に、
脆性亀裂伝播停止特性が更に優れ、且つ板厚中心迄優れ
た靭性を有する構造用厚鋼板を生産性良く、経済的に製
造する方法を提供する事を課題とするものである。<Problems to be solved by the invention> The present invention solves the problems of the prior art described above, and
The object of the present invention is to provide a highly productive and economical method for manufacturing thick structural steel plates that have even better brittle crack propagation arresting properties and excellent toughness up to the center of the plate thickness.
く課題を解決するための手段〉
本発明は上記課題を達成するため、
(1)重量%で、
C: o、ot〜0.30 %
SI:≦0.5 %
Mn:≦2.0 %
Al:≦O01%
N : 0.001〜0.01%
その他Fe及び不可避的成分からなる構造用圧延鋼を連
続鋳造して得た鋳片をAc3点以上の温度から冷却速度
2°(/sec以上で水冷を開始し、該鋳片表裏面から
厚みの1/3迄の表層部をAr1点以下に冷却して該水
冷を中止し、該鋳片の復熱が終了する迄の間に仕上圧延
を開始し、該仕上圧延終了後該鋳片の表裏面から厚みの
173迄をAC3点未満に復熱すると共に該鋳片の表裏
面から厚みの173以上をAc2点以上に復熱する事を
特徴とする脆性亀裂伝播停止特性の優れた鋼板の製造方
法を第1の手段とし、
(2)重量%で、
C:0.01〜0.30 %
Si:≦0.5 %
Mn:≦2.0 %
Al:≦0.1 %
N : 0.001−0.01%
更に、
Cr:≦0.5 % Ti:≦0.1 %Ni
:≦1.0 % Nb:≦0.05 %MO:
≦0.5 % B:≦0.0015%V:≦0.
1 % Cu:≦0.9 %の1種又は2種以
上を含み、その他Fe及び不可避的成分からなる構造用
圧延鋼を連続鋳造して得た鋳片を、Ac2点以上の温度
から冷却速度2℃/sec以上で水冷を開始し、該鋳片
の表裏面から厚みの1/3迄の表層部を冷却してAr+
点以下で該水冷を中止し、該鋳片の復熱が終了する迄の
間に仕上圧延を開始し、該仕上圧延終了後、咳鋳片の表
裏面から厚みの173迄をAc2点未満に復熱すると共
に該鋳片の表裏面から厚みの173以上をAc2点以上
に復熱する事を特徴とする脆性亀裂伝播停止特性の優れ
た鋼板の製造方法を第2の手段とし、(3)重量%で、
C: 0.01〜0.30 %
Si:≦0.5 %
Mn:≦2.0 %
Al=≦0.1 %
N : 0.001〜0.01%
その他Fe及び不可避的成分からなる構造用圧延鋼を連
続鋳造して得た鋳片をAC2点以上の温度から冷却速度
2°(/sec以上で水冷を開始し、該鋳片表裏面から
厚みの1/3迄の表層部をAr3点以下に冷却して該水
冷を中止し、該鋳片の復熱が終了する迄の間に仕上圧延
を開始し、該仕上圧延終了後該鋳片の表裏面から174
迄をAc4点未満に復熱すると共にsti鋳片の表裏面
から1/4以上をAc4点以上に復熱する事を特徴とす
る脆性亀裂伝播停止特性の優れた鋼板の製造方法を第3
の手段とし、(4)重量%で、
C: 0.01〜0.30 %
Si:≦0.5 %
Mn:≦2.0 %
Al:≦0.1 %
N : 0.001〜0.01%
更に、
Cr:≦0.5 % Ti:≦0.1 %Ni:
≦1.0 % Nb:≦0.05 %Mo:≦0
.5 % B=≦0.0015%V:≦0.1
% Cu:≦0.9 %の1種又は2種以上を含み
、その他Fe及び不可避的成分からなる構造用圧延鋼を
連続鋳造して得た鋳片を、Ac1点以上の温度から冷却
速度2℃/sec以上で水冷を開始し、該鋳片の表裏面
から厚みの1/3迄の表層部を冷却してAr3点以下で
該水冷を中止し、2% tfi片の復熱が終了する迄の
間に仕上圧延を開始し、該仕上圧延終了後、該鋳片の表
裏面から1/4迄をAc3点未満に復熱すると共に該鋳
片の表裏面から174以上をAc3点以上に復熱する事
を特徴とする脆性亀裂伝播停止特性の優れた鋼板の製造
方法を第4の手段とし、
(5)上記第1.2.34の手段に記載の復熱終了後の
鋼板を40℃/秒以下の冷却速度で650°C以下迄冷
却する事を第5〜8の手段とするものである。Means for Solving the Problems> The present invention achieves the above problems by: (1) In weight%, C: o,ot~0.30% SI: ≦0.5% Mn: ≦2.0% Al: ≦O01% N: 0.001-0.01% A slab obtained by continuous casting of structural rolled steel consisting of Fe and other unavoidable components was cooled at a cooling rate of 2° (/sec) from a temperature of Ac 3 or higher. With the above, water cooling is started, and the surface layer from the front and back surfaces of the slab to 1/3 of the thickness is cooled to below Ar 1 point, and the water cooling is stopped, and finishing is completed until the reheating of the slab is completed. Start rolling, and after finishing the finish rolling, reheat the slab from the front and back surfaces up to a thickness of 173 to below the AC3 point, and reheat the slab from the front and back surfaces to a thickness of 173 or more to an AC2 point or higher. The first method is to produce a steel plate with excellent brittle crack propagation arresting properties characterized by: (2) In weight%, C: 0.01 to 0.30% Si: ≦0.5% Mn: ≦ 2.0% Al: ≦0.1% N: 0.001-0.01% Furthermore, Cr: ≦0.5% Ti: ≦0.1% Ni
:≦1.0% Nb:≦0.05%MO:
≦0.5% B:≦0.0015%V:≦0.
A slab obtained by continuous casting of a structural rolled steel containing one or more of 1% Cu:≦0.9% and other Fe and other unavoidable components is cooled from a temperature of 2 or more Ac points. Water cooling is started at 2°C/sec or more, and the surface layer from the front and back surfaces of the slab to 1/3 of the thickness is cooled to Ar+.
The water cooling is stopped at a temperature below the Ac point, finish rolling is started until the reheating of the slab is completed, and after finishing the finishing rolling, the thickness of the slab from the front and back to the thickness 173 is reduced to less than the Ac2 point. As a second means, a method for producing a steel plate with excellent brittle crack propagation arresting properties is provided, which is characterized by recuperating heat and reheating a thickness of 173 or more from the front and back surfaces of the slab to an Ac2 point or more, (3) In weight%, C: 0.01-0.30% Si: ≦0.5% Mn: ≦2.0% Al=≦0.1% N: 0.001-0.01% Others Fe and unavoidable A slab obtained by continuous casting of structural rolled steel consisting of the following components is water-cooled from a temperature of AC2 or higher at a cooling rate of 2°/sec or higher, and the slab is cast from the front and back surfaces to 1/3 of the thickness. The surface layer is cooled to an Ar point of 3 or less, the water cooling is stopped, finish rolling is started until the reheating of the slab is completed, and after finishing the finish rolling, 174
A third method for producing a steel plate with excellent brittle crack propagation arresting properties, which is characterized by reheating up to below the Ac4 point and reheating 1/4 or more from the front and back surfaces of the STI slab to an Ac4 point or above.
(4) In weight%, C: 0.01-0.30% Si: ≦0.5% Mn: ≦2.0% Al: ≦0.1% N: 0.001-0. 01% Furthermore, Cr:≦0.5% Ti:≦0.1% Ni:
≦1.0% Nb:≦0.05 %Mo:≦0
.. 5% B=≦0.0015%V:≦0.1
%Cu:≦0.9% A slab obtained by continuous casting of structural rolled steel containing one or more of 0.9% and other Fe and other unavoidable components was cooled at a cooling rate of 2 from a temperature of Ac 1 point or higher. Start water cooling at ℃/sec or more, cool the surface layer from the front and back surfaces of the slab to 1/3 of the thickness, and stop the water cooling when the Ar point is 3 or less, completing the reheating of the 2% TFI piece. In the meantime, finish rolling is started, and after finishing the finish rolling, reheat up to 1/4 of the front and back surfaces of the slab to less than 3 Ac points, and at the same time bring 174 or more from the front and back surfaces of the slab to 3 Ac points or higher. The fourth means is a method for manufacturing a steel plate with excellent brittle crack propagation arresting properties characterized by reheating, and (5) the steel plate after completion of reheating described in the above means 1.2. The fifth to eighth means are to cool down to 650°C or less at a cooling rate of 0°C/sec or less.
以下に上記した成分限定理由を説明する。The reasons for limiting the above-mentioned components will be explained below.
Cは鋼材の強化成分として添加し、溶接部の靭性劣化の
防止から上限を定めている。C is added as a reinforcing component to steel materials, and an upper limit is set to prevent deterioration of the toughness of the welded part.
51は脱酸と強度維持を目的に添加し、溶接性の劣化防
止から上限を定めている。No. 51 is added for the purpose of deoxidizing and maintaining strength, and the upper limit is set to prevent deterioration of weldability.
Mnは低温靭性の向上を目的に添加し、溶接割れの防止
から上限を定めている。Mn is added for the purpose of improving low-temperature toughness, and the upper limit is set to prevent weld cracking.
NはAIと共に窒化物の生成による結晶粒の微細化を目
的として添加し、溶接部の靭性劣化の防止から上限を定
めている。N is added together with AI for the purpose of refining crystal grains by forming nitrides, and the upper limit is set to prevent deterioration of the toughness of the weld zone.
Cr、Ni、MoB 、Cuは何れも焼入れ性を向上し
、効果的な強度上Aを目的として添加し、低温変態生成
物の生成を抑制し、フェライト面積率の減少を防止する
ため上限を定めている。Cr, Ni, MoB, and Cu are all added for the purpose of improving hardenability and effective strength, and upper limits are set to suppress the formation of low-temperature transformation products and prevent a decrease in the ferrite area ratio. ing.
Ti、Nbは結晶粒の微細化を目的として添加し、溶接
部の靭性圧下の防止から上限を定めている。Ti and Nb are added for the purpose of refining crystal grains, and the upper limit is set to prevent reduction in toughness of the weld zone.
■は析出強化を目的に添加し、経済性から上限を定めて
いる。(2) is added for the purpose of precipitation strengthening, and the upper limit is set for economic reasons.
又木′発明が対象とする構造用圧延112I鋳片は、連
続鋳造の侭の高温の鋼片、及び−旦冷却後再加熱した鋼
片、更には連続鋳造の侭の形状の鋼片、及び連続鋳造抜
形状調整圧延等の圧延を行った鋼片等を指す。Structural rolled 112I slabs to which the present invention is directed include continuously cast high-temperature steel slabs, steel slabs that have been cooled and then reheated, furthermore continuous cast steel slabs that have the same shape as before, and Refers to steel billets, etc. that have been subjected to rolling such as continuous casting, punching, shape adjustment rolling, etc.
又本発明における水冷は、連続鋳造で通常使用されてい
る冷却速度2゛C/秒以上の水冷手段を使用して充分に
行える。Further, the water cooling in the present invention can be sufficiently carried out using a water cooling means which has a cooling rate of 2° C/sec or more and is normally used in continuous casting.
〈作用〉
本発明者等は上記課題を達成するため、重量%で、
C:0゜01〜0.30 %
Si:≦0.5 %
Mn:≦2.0 %
Al;≦0.1 %
N : 0.001 〜0.01%
更に、
Cr:≦0.5 % Ti:≦0.1 %Ni:
≦1.0 % Nb:≦0.05 %Mo:≦0
.5 % B:≦0.0015%■二≦0.1%C
u:50.9%
の1種又は2種以上を含み、その他Fe及び不可避的成
分からなる構造用圧延鋼を連続鋳造して得た鋳片を用い
て種々の実験検討を繰り返した。<Function> In order to achieve the above-mentioned object, the present inventors prepared the following in weight%: C: 0°01 to 0.30% Si: ≦0.5% Mn: ≦2.0% Al; ≦0.1% N: 0.001 to 0.01% Furthermore, Cr: ≦0.5% Ti: ≦0.1% Ni:
≦1.0% Nb:≦0.05 %Mo:≦0
.. 5% B:≦0.0015%■2≦0.1%C
Various experimental studies were repeated using slabs obtained by continuous casting of structural rolled steel containing one or more of u: 50.9% and other Fe and other unavoidable components.
その結果厚み50m+n以下の鋼板は、第1回(a)(
b)に示す如く、該鋳片の厚み方向に該鋳片の表裏面か
ら厚みの173(以下1/3Lと記す)程度迄を冷却速
度2℃/秒以上でAr3点以下迄冷却し、該鋳片の表層
部と中心部に温度差をつけた信任上圧延を開始し、該仕
上圧延終了後、該鋳片の表裏面から1/3L程度の表層
部をAc2点未満に、該鋳片の表裏面から1/3を以上
をAc3点以上に復熱すると該圧延が昇温過程内の圧延
のため、未再結晶域でありながらフェライトが充分に再
結晶して結晶粒が微細化する事を知得し、厚み50mm
超の鋼板は、第1図(a)(c)に示す如く、該鋳片の
表裏面から厚みのl/4(以下1/4tと記す)程度以
上をAc3点以上に復熱すると、174E未満の部分は
上記と同様の再結晶により微細化し、1/4L程度以上
の部分はフェライトからオーステナイトへの逆変態で結
晶粒が微細化する事を知得した。As a result, steel plates with a thickness of 50m+n or less were tested in the first (a) (
As shown in b), the slab is cooled from the front and back surfaces of the slab in the thickness direction to about 173 (hereinafter referred to as 1/3 L) of the thickness at a cooling rate of 2°C/sec or more to an Ar point of 3 or less. Confidence rolling is started with a temperature difference between the surface layer and the center of the slab, and after finishing the finish rolling, the surface layer of about 1/3L from the front and back surfaces of the slab is reduced to less than the Ac2 point. When more than 1/3 of the front and back surfaces of the ferrite are reheated to Ac3 point or higher, the ferrite is sufficiently recrystallized and the crystal grains become fine even though it is in the non-recrystallized area because the rolling is performed during the temperature rising process. Thickness: 50mm
As shown in Figures 1(a) and (c), super steel plates can be heated to 174E or higher by reheating approximately 1/4 (hereinafter referred to as 1/4t) of the thickness from the front and back surfaces of the slab to a point of Ac3 or higher. It has been learned that the portion smaller than 1/4 L is refined by recrystallization as described above, and the portion larger than about 1/4 L is refined by reverse transformation from ferrite to austenite.
これ等の知見により、上記方法によると鋼板厚みに影響
される事なく鋼板全体に及ぶ広範囲な領域で微細な組織
を短時間の中に的確に生成出来る事を見出した。Based on these findings, it has been found that the above method can accurately generate a fine structure in a wide range of areas throughout the steel plate in a short period of time without being affected by the thickness of the steel plate.
又、この時、TiとNbを含まない鋼板は、5μl以下
の結晶粒径のフェライトが表層部の50%以上の面積率
に達し、TiとNbを含む鋼板は3μm以下の結晶粒径
のフェライトが表層部の面積率50%以上に達し、共に
kca (−70)≧600が極めて安定した脆性亀裂
伝播停止特性を発揮する事を見出した。In addition, at this time, the steel sheet that does not contain Ti and Nb has ferrite with a grain size of 5 μl or less reaching an area ratio of 50% or more of the surface layer, and the steel sheet that contains Ti and Nb has ferrite with a grain size of 3 μm or less. It has been found that when the area ratio of the surface layer reaches 50% or more, and both kca (-70)≧600, extremely stable brittle crack propagation arresting properties are exhibited.
又これ等の鋼板は、40℃/秒以下の冷却速度で650
°C以下迄強制冷却すると、母材強度と靭性が向上する
事を見出した。Also, these steel plates can be heated to 650℃ at a cooling rate of 40℃/second or less.
It has been found that forced cooling to below °C improves the strength and toughness of the base metal.
本発明は上記知見を基になされたものである。The present invention is based on the above findings.
〈実施例〉 1、供試w4:表1に示す。<Example> 1. Test w4: Shown in Table 1.
2、圧延条件 :表2に示す。2. Rolling conditions: Shown in Table 2.
3、冷却条件 二表2に示す。3. Cooling conditions are shown in Table 2.
4、冷却停止条件二表2に示す。4. Cooling stop conditions 2 are shown in Table 2.
S、ul熱条件 8表2に示す。S, ul heat conditions 8 are shown in Table 2.
6、熱燗後の制御冷却条件:表2に示す。6. Controlled cooling conditions after hot sake: Shown in Table 2.
7、粒度別面積率とKca r表3に示す。7. Area ratio and Kca by particle size are shown in Table 3.
本発明例の調香1,3〜7,9〜11.13〜17.1
9〜21.24,25.27〜29は、にca (−7
0″C)≧600を示した。これに対し比較例の調香2
,8.12.18.22,23.26は、Kca(−7
0℃)≦300シか得られなかった。Perfumes of the invention examples 1, 3 to 7, 9 to 11.13 to 17.1
9-21.24, 25.27-29 are ca (-7
0″C)≧600. In contrast, Comparative Example Perfume 2
, 8.12.18.22, 23.26 is Kca (-7
0°C)≦300°C was not obtained.
〈発明の効果〉
本発明は、未再結晶域での昇温下圧延による再結晶と逆
変態の組み合わせにより、鋼板の厚み方向全域に及んで
微細な組織を形成し、シアリップを効果的に作用させる
ので、優れた脆性亀裂伝播停止特性Kca (−70)
≧600を発揮する鋼板の製造の経済性、生産性を格段
に向上したもので、この種分野にもたらす効果は極めて
大きい。<Effects of the Invention> The present invention forms a fine structure throughout the thickness of the steel sheet by combining recrystallization and reverse transformation by rolling at elevated temperature in the non-recrystallized region, and effectively acts on the shear lip. Excellent brittle crack propagation arresting property Kca (-70)
≧600, the economic efficiency and productivity of manufacturing steel plates have been significantly improved, and the effect it brings to this type of field is extremely large.
第1図(a)は、本発明が規制する鋳片及び鋼板の厚み
方向の位置を示す。
伽)は、請求項1,2.5の本発明例における上記位置
と水冷・復熱温度の関係を示し、(C)は、請求項3,
4.5の本発明例における上記位置と水冷・復熱温度の
関係を示す。
(d)は、従来例(特開昭61−235534号公報例
)における上記位置と水冷・復熱温度の関係を示す。
特許出願人 新日本製鐵株式会社FIG. 1(a) shows the positions in the thickness direction of slabs and steel plates regulated by the present invention. (C) indicates the relationship between the position and the water cooling/recuperation temperature in the example of the present invention of claims 1 and 2.5, and (C) indicates the relationship between the above position and the water cooling/recuperation temperature in the example of the present invention of claims 1 and 2.5.
4.5 shows the relationship between the above position and water cooling/recuperation temperature in the present invention example. (d) shows the relationship between the above-mentioned position and water cooling/recuperation temperature in a conventional example (Japanese Patent Laid-Open No. 61-235534). Patent applicant Nippon Steel Corporation
Claims (4)
続鋳造して得た鋳片をAc_3点以上の温度から冷却速
度2℃/sec以上で水冷を開始し、該鋳片表裏面から
厚みの1/3迄の表層部をAr_3点以下に冷却して該
水冷を中止し、該鋳片の復熱が終了する迄の間に仕上圧
延を開始し、該仕上圧延終了後該鋳片の表裏面から厚み
の1/3迄をAc_3点未満に復熱すると共に該鋳片の
表裏面から厚みの1/3以上をAc_3点以上に復熱す
る事を特徴とする脆性亀裂伝播停止特性の優れた鋼板の
製造方法。(1) In weight%, C: 0.01-0.30% Si: ≦0.5% Mn: ≦2.0% Al: ≦0.1% N: 0.001-0.01% Other Fe A slab obtained by continuous casting of structural rolled steel consisting of unavoidable components is started to be water-cooled from a temperature of Ac_3 or higher at a cooling rate of 2°C/sec or higher, and 1/3 of the thickness is removed from the front and back surfaces of the slab. Cool the surface layer to below Ar_3 point, stop the water cooling, start finish rolling until the reheating of the slab is completed, and after finishing the finish rolling, reduce the thickness from the front and back sides of the slab. A steel plate with excellent brittle crack propagation arresting properties, characterized in that up to 1/3 of the slab is reheated to below the Ac_3 point, and at least 1/3 of the thickness from the front and back surfaces of the slab is reheated to the Ac_3 point or more. Production method.
分からなる構造用圧延鋼を連続鋳造して得た鋳片を、A
c_3点以上の温度から冷却速度2℃/sec以上で水
冷を開始し、該鋳片の表裏面から厚みの1/3迄の表層
部を冷却してAr_3点以下で該水冷を中止し、該鋳片
の復熱が終了する迄の間に仕上圧延を開始し、該仕上圧
延終了後、該鋳片の表裏面から厚みの1/3迄をAc_
3点未満に復熱すると共に該鋳片の表裏面から厚みの1
/3以上をAc_3点以上に復熱する事を特徴とする脆
性亀裂伝播停止特性の優れた鋼板の製造方法。(2) In weight%, C: 0.01-0.30% Si: ≦0.5% Mn: ≦2.0% Al: ≦0.1% N: 0.001-0.01% Furthermore, Cr:≦0.5% Ti:≦0.1% Ni:≦1.0% Nb:≦0.05% Mo:≦0.5% B:≦0.0015% V:≦0.1% Cu :≦0.9% of one or more of the above, and other Fe and other unavoidable components.
Start water cooling at a cooling rate of 2°C/sec or higher from a temperature of C_3 or higher, cool the surface layer from the front and back surfaces of the slab to 1/3 of the thickness, stop the water cooling at a temperature of Ar_3 or lower, and Finish rolling is started before the reheating of the slab is completed, and after finishing the finishing rolling, the slab is Ac_
1 of the thickness from the front and back surfaces of the slab.
A method for producing a steel plate having excellent brittle crack propagation arresting properties, characterized by recuperating heat from /3 or more to Ac_3 point or more.
続鋳造して得た鋳片をAc_3点以上の温度から冷却速
度2℃/sec以上で水冷を開始し、該鋳片表裏面から
厚みの1/3迄の表層部をAr_3点以下に冷却して該
水冷を中止し、該鋳片の復熱が終了する迄の間に仕上圧
延を開始し、該仕上圧延終了後該鋳片の表裏面から1/
4迄をAc_3点未満に復熱すると共に該鋳片の表裏面
から1/4以上をAc_3点以上に復熱する事を特徴と
する脆性亀裂伝播停止特性の優れた鋼板の製造方法。(3) In weight%, C: 0.01-0.30% Si: ≦0.5% Mn: ≦2.0% Al: ≦0.1% N: 0.001-0.01% Other Fe A slab obtained by continuous casting of structural rolled steel consisting of unavoidable components is started to be water-cooled from a temperature of Ac_3 or higher at a cooling rate of 2°C/sec or higher, and 1/3 of the thickness is removed from the front and back surfaces of the slab. The surface layer is cooled to below Ar_3 point, the water cooling is stopped, finish rolling is started until the reheating of the slab is completed, and after finishing the finishing rolling, 1 /
A method for producing a steel sheet with excellent brittle crack propagation arresting properties, characterized by reheating up to Ac_3 point up to Ac_3 point and reheating 1/4 or more from the front and back surfaces of the slab to Ac_3 point or more.
分からなる構造用圧延鋼を連続鋳造して得た鋳片を、A
c_3点以上の温度から冷却速度2℃/sec以上で水
冷を開始し、該鋳片の表裏面から厚みの1/3迄の表層
部を冷却してAr_3点以下で該水冷を中止し、該鋳片
の復熱が終了する迄の間に仕上圧延を開始し、該仕上圧
延終了後、該鋳片の表裏面から1/4迄をAc_3点未
満に復熱すると共に該鋳片の表裏面から1/4以上をA
c_3点以上に復熱する事を特徴とする脆性亀裂伝播停
止特性の優れた鋼板の製造方法。(5)上記請求項1〜
4に記載の復熱終了後の鋼板を40℃/秒以下の冷却速
度で650℃以下迄冷却をする事を特徴とする脆性亀裂
伝播停止特性の優れた鋼板の製造方法。(4) In weight%, C: 0.01-0.30% Si: ≦0.5% Mn: ≦2.0% Al: ≦0.1% N: 0.001-0.01% Furthermore, Cr:≦0.5% Ti:≦0.1% Ni:≦1.0% Nb:≦0.05% Mo:≦0.5% B:≦0.0015% V:≦0.1% Cu :≦0.9% of one or more of the above, and other Fe and other unavoidable components.
Start water cooling at a cooling rate of 2°C/sec or higher from a temperature of C_3 or higher, cool the surface layer from the front and back surfaces of the slab to 1/3 of the thickness, stop the water cooling at a temperature of Ar_3 or lower, and Finish rolling is started before the reheating of the slab is completed, and after finishing the finish rolling, the front and back surfaces of the slab are reheated to less than 1/4 of the Ac_3 point, and the front and back surfaces of the slab are reheated to less than Ac_3 point. 1/4 or more from A
c_A method for producing a steel plate with excellent brittle crack propagation arresting properties characterized by recuperation to a point of 3 or higher. (5) Claims 1-
4. A method for producing a steel plate having excellent brittle crack propagation arresting properties, which comprises cooling the steel plate after completion of reheating according to item 4 to 650°C or less at a cooling rate of 40°C/sec or less.
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2706089 | 1989-02-06 | ||
JP1-27060 | 1989-02-06 |
Publications (2)
Publication Number | Publication Date |
---|---|
JPH032322A true JPH032322A (en) | 1991-01-08 |
JPH075967B2 JPH075967B2 (en) | 1995-01-25 |
Family
ID=12210525
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP2024509A Expired - Fee Related JPH075967B2 (en) | 1989-02-06 | 1990-02-05 | Method for producing steel sheet with excellent brittle crack propagation stopping properties |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPH075967B2 (en) |
Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH04141517A (en) * | 1990-09-28 | 1992-05-15 | Nippon Steel Corp | Production of steel plate excellent in brittle crack propagation arresting property and toughness at low temperature |
JPH05271860A (en) * | 1992-03-25 | 1993-10-19 | Nippon Steel Corp | Structural steel excellent in brittle fracture resistance and its production |
JPH0688161A (en) * | 1992-07-29 | 1994-03-29 | Nippon Steel Corp | Steel sheet excellent in brittle fracture property and fatigue property and its production |
-
1990
- 1990-02-05 JP JP2024509A patent/JPH075967B2/en not_active Expired - Fee Related
Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH04141517A (en) * | 1990-09-28 | 1992-05-15 | Nippon Steel Corp | Production of steel plate excellent in brittle crack propagation arresting property and toughness at low temperature |
JPH05271860A (en) * | 1992-03-25 | 1993-10-19 | Nippon Steel Corp | Structural steel excellent in brittle fracture resistance and its production |
JPH0688161A (en) * | 1992-07-29 | 1994-03-29 | Nippon Steel Corp | Steel sheet excellent in brittle fracture property and fatigue property and its production |
Also Published As
Publication number | Publication date |
---|---|
JPH075967B2 (en) | 1995-01-25 |
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