EP4206337A1 - Tôle forte et procédé de traitement thermomécanique d'une matière de départ destinée à la fabrication d'une tôle forte - Google Patents

Tôle forte et procédé de traitement thermomécanique d'une matière de départ destinée à la fabrication d'une tôle forte Download PDF

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Publication number
EP4206337A1
EP4206337A1 EP21218236.4A EP21218236A EP4206337A1 EP 4206337 A1 EP4206337 A1 EP 4206337A1 EP 21218236 A EP21218236 A EP 21218236A EP 4206337 A1 EP4206337 A1 EP 4206337A1
Authority
EP
European Patent Office
Prior art keywords
temperature
cooling rate
thickness
rolling
heavy 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.)
Withdrawn
Application number
EP21218236.4A
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German (de)
English (en)
Inventor
Rupert Egger
Martin Klima
Erik Parteder
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Voestalpine Grobblech GmbH
Original Assignee
Voestalpine Grobblech GmbH
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Voestalpine Grobblech GmbH filed Critical Voestalpine Grobblech GmbH
Priority to EP21218236.4A priority Critical patent/EP4206337A1/fr
Priority to EP22844548.2A priority patent/EP4457370A1/fr
Priority to PCT/EP2022/088050 priority patent/WO2023126506A1/fr
Priority to US18/721,469 priority patent/US20250051890A1/en
Priority to CN202280085265.9A priority patent/CN118475708A/zh
Priority to JP2024539500A priority patent/JP2024546190A/ja
Priority to KR1020247025495A priority patent/KR20240132323A/ko
Publication of EP4206337A1 publication Critical patent/EP4206337A1/fr
Withdrawn legal-status Critical Current

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Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/02—Hardening articles or materials formed by forging or rolling, with no further heating beyond that required for the formation
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0242—Flattening; Dressing; Flexing
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/08—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium

Definitions

  • the invention relates to a heavy plate and a thermomechanical treatment method of a starting material, in particular a slab, for the production of a heavy plate consisting of a steel alloy.
  • thermomechanical treatment process In order to increase the toughness, especially the low-temperature toughness, of a heavy plate made of a steel alloy, WO2011/079341A2 a thermomechanical treatment process is known in which the starting material is hot-rolled in several stages and accelerated between two hot-rolling passes to below the Ar3 temperature and then inductively heated to above the Ac3 temperature. After the last hot rolling pass, a two-stage cooling to room temperature takes place - first with an accelerated cooling rate by water quenching to a cooling stop temperature below Ar3 and finally with cooling at room temperature.
  • these heavy plates have the disadvantage of low uniform elongation Ag, which limits their use in earthquake zones, for example.
  • thermomechanical treatment process for the production of a heavy plate with which an improved uniform elongation Ag can be achieved reproducibly on the heavy plate despite high toughness values.
  • the invention solves the problem set by the features of claim 1.
  • the steel alloy in each case in % by weight) 0.02 to 0.1 carbon (C), 1.0 to 2.0 manganese (Mn), 0.1 to 0.80 silicon (Si), 0.010 to 0.15 aluminum (Al), ⁇ 0.050 Phosphorus (P) and ⁇ 0.010 Sulfur (S) on.
  • the steel alloy can be used individually or in combination from the group (each in % by weight): 0 to 0.75 copper (Cu) 0 to 3.0 Nickel (Ni) 0 to 0.20 vanadium (V) 0 to 0.003 boron (B) exhibit.
  • the desired microstructure consisting of ferrite, bainite and optionally martensite, can be produced more reproducibly in the steel alloy according to the invention in order to achieve high uniform elongation Ag with high toughness.
  • the lower limit for the cooling rate KR2 of the starting material can be 16 °C/s for a heavy plate with a thickness of 25 mm.
  • the lower limit for the cooling rate KR2 of the starting material can be 3.9 °C/s for a heavy plate with a thickness of 80 mm.
  • An exemplary upper limit based on the above formula for cooling rates KR2 for a heavy plate with a thickness of 25 mm is 78.6 °C/s - for a heavy plate with a thickness of 80 mm this is 5.9 °C/s.
  • the range for the second cooling rate KR2 for the thinner heavy plate (starting material after final forming) is in the range from 16 °C/s to 78.6 °C/s and for the thicker heavy plate (starting material after the final forming) can be in the range from 3.9 °C/s to 5.9 °C/s according to the invention.
  • the thicknesses are to be used in mm (millimeters) and the temperatures in °C and the cooling rates in °C/s.
  • the ratio of the second cooling rate KR2 to the first cooling rate KR1 is at least 2:1, this can further increase the uniform elongation Ag if the toughness is sufficiently high.
  • the ratio of the second cooling rate KR2 to the first cooling rate KR1 is at least 3:1, this can lead to an optimum balance between toughness and uniform elongation Ag in the case of stressed steel alloys.
  • the first cooling rate (KR1) is preferably ⁇ 5° C./s, particularly preferably ⁇ 3° C./s, which makes it easier to handle the method and can also further improve the reproducibility for a high uniform elongation Ag with high toughness.
  • the first temperature is T1 in degrees Celsius ⁇ are 1 + 0.1 ⁇ are 3 ⁇ are 1 2 and ⁇ are 1 + 1.9 ⁇ are 3 ⁇ are 1 2
  • a first temperature T1 in this range can, among other things, reproducibly lead to a maximum of uniform elongation Ag in the steel alloy according to the invention.
  • the second temperature T2 is preferably in the range from 450° C. to 100° C., preferably in the range from 400° C. to 150° C., particularly preferably in the range from 400° C. to 250° C., in order to set the structure for high toughness and in this way an optimum combination of high strength, uniform elongation and toughness can be set.
  • Cooling from the second temperature to room temperature in a third stage at a third cooling rate KR3, with the third cooling rate KR3 ⁇ second cooling rate KR2, can further improve the mechanical characteristics of the steel alloy.
  • the third cooling rate KR3 is ⁇ 5° C./s, preferably ⁇ 3° C./s, because—in terms of process technology—the cooling can be carried out unaccelerated in air.
  • the starting material can be inductively heated for this purpose, which can be advantageous for the overall duration of the production route, since this reduces both the cycle time and the heating rate can be set very high.
  • heating can also take place via thermal radiation - this represents a particularly simple and robust method for heating.
  • End forming is preferably carried out to a thickness of the plate in the range from 8 to 150 mm (millimeters), in particular to a thickness of the plate in the range from 25 to 120 mm.
  • the invention solves the problem set by the features of claim 14.
  • the heavy plate produced by the thermomechanical treatment process can have a yield strength ratio (R p0.2 /R m ) of ⁇ 0.7.
  • This heavy plate can preferably have a yield point ratio (R p0.2 /R m ) of ⁇ 0.70.
  • This heavy plate can preferably have a yield point ratio (R p0.2 /R m ) of ⁇ 0.65.
  • the heavy plate has a thickness in the range from 8 to 150 mm.
  • the heavy plate can have a thickness in the range from 25 to 120 mm.
  • the heavy plate preferably has a yield point R p0.2 >550 N/mm 2 (Newton per square millimeter), in particular a yield point R p0.2 (0.2% yield point) >590 N/mm 2 , in order to have a comparatively high to guarantee strength.
  • This heavy plate can therefore be particularly suitable as a longitudinally welded pipe for a natural gas pipeline or as a construction material, especially in a seismically active region.
  • the respective cooling rate (KR1, KR2, KR3) or heating rate from the initial temperature to the final temperature is an average value, namely a cooling rate or heating rate from the initial temperature to the final temperature averaged over the thickness of the starting material.
  • Both heavy plates A, B have the same steel alloy 0.04% by weight (C) carbon, 1.63% by weight (Mn) manganese, 0.34% by weight (Si) silicon, 0.04% by weight (Al) aluminum, 0.012% by weight (P) phosphorus, 0.001% by weight (S) sulphur, 0.17% by weight (Cr) chromium, 0.02% by weight (Mo) molybdenum, 0.035% by weight (Nb) niobium, 0.014% by weight (Ti)titanium, 0.0003% by weight (B) boron, 0.0045% by weight (N) nitrogen and the remainder iron (Fe) and impurities that are unavoidable as a result of production, each with a maximum of 0.05% by weight and a maximum of 0.15% by weight in total.
  • the primary material, namely the slab, of the respective heavy plate A, B is heated 4 to above the Ac3 temperature, namely 1100° C. (degrees Celsius), for example with a slab heating device.
  • the starting material is then partially formed by first rolling W1.
  • accelerated cooling 5 namely quenching, preferably water quenching, with which the starting material is cooled from the first final rolling temperature, which is above Ac3, to below the Ar3 temperature, namely - as in 1 recognizable - the primary material is cooled or quenched to below the Ar1 temperature.
  • quenching preferably water quenching
  • the starting material leaves the second rolling W2 with a second final rolling temperature EW2 ⁇ Ar3, namely 830 °C.
  • EW2 ⁇ Ar3 a second final rolling temperature
  • other heating sources are also conceivable, for example sources with radiant heat. This rapid heating, be it inductive or with radiant heat etc., takes place at a minimum of 12°C/min.
  • This second roll W2 which can also be referred to as end rolls, is followed by two different multi-stage coolings 3 to room temperature (which is usually between 0 and 60 degrees Celsius, for example 20 degrees Celsius in these processes).
  • the starting material of the heavy plate A is accelerated from the second final rolling temperature to a temperature below Ar1 by water quenching at 30° C./s, namely quenched. This is followed by cooling at 0.1° C./s in still air at ambient temperature as the second immediately following second stage 7b of cooling 3 to room temperature RT.
  • the multi-stage cooling 3 according to the invention can be seen from the starting material of the heavy plate B.
  • the starting material is cooled at a first cooling rate KR1, namely 0.6 °C/s, from the second final rolling temperature EW2 to a first temperature T1 between Ar3 and Ar1, namely 720 °C (Centigrade).
  • the starting material is quenched from the first temperature T1 to a second temperature T2 ⁇ Ar1, namely 150° C., at a second cooling rate KR2, namely 30° C./s.
  • a second cooling rate KR2 namely 30° C./s.
  • room temperature RT which has not been detailed.
  • the first cooling rate KR1 ⁇ second cooling rate KR2 specifically by a factor of 3 less than the second cooling rate KR2.
  • a third stage 8c with a third cooling rate KR3 from the second temperature T2 to room temperature RT in still air at ambient temperature can be seen in the multi-stage cooling.
  • the third cooling rate KR3 is preferably 0.1° C./s.
  • accelerated cooling can be understood to mean faster cooling than cooling at room temperature and still air, which is also often referred to as quenching.
  • a block or a billet is also conceivable as the starting material.
  • first and/or second rolling can consist of one or more part-rolls with possibly several part-rolling steps (passes), which is possible, for example, by reversing rolling.
  • the uniform elongation A g of the heavy plate B was increased from 8.9% to 14.7%, ie by 5.8% compared to heavy plate A. Heavy plate B therefore enables a significantly higher energy dissipation capacity, ie energy absorption capacity.
  • heavy plate B undergoes plastic deformation more quickly than heavy plate A (cf. 0.2% yield strength R p0.2 ), but it still occurs with heavy plate B much later to failure (cf. A g ).
  • This property is particularly advantageous when used in earthquake-prone regions or seismically active regions, where the dissipation capacity of the material is crucial.
  • the heavy plate B produced according to the invention can therefore be particularly suitable, for example, as longitudinally welded pipes for natural gas pipelines or in steel construction in seismically active regions. Due to the high uniform elongations, components made from this heavy plate B have a high energy dissipation capacity. It is also conceivable to use it as a building material in steel construction in the production of welded I-beams with advantageous behavior in the event of a hole reveal failure.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
EP21218236.4A 2021-12-29 2021-12-29 Tôle forte et procédé de traitement thermomécanique d'une matière de départ destinée à la fabrication d'une tôle forte Withdrawn EP4206337A1 (fr)

Priority Applications (7)

Application Number Priority Date Filing Date Title
EP21218236.4A EP4206337A1 (fr) 2021-12-29 2021-12-29 Tôle forte et procédé de traitement thermomécanique d'une matière de départ destinée à la fabrication d'une tôle forte
EP22844548.2A EP4457370A1 (fr) 2021-12-29 2022-12-29 Plaque lourde et procédé de manipulation thermomécanique de matériau de départ de production de plaque lourde
PCT/EP2022/088050 WO2023126506A1 (fr) 2021-12-29 2022-12-29 Plaque lourde et procédé de manipulation thermomécanique de matériau de départ de production de plaque lourde
US18/721,469 US20250051890A1 (en) 2021-12-29 2022-12-29 Heavy plate and thermomechanical treatment method for a starting material for the production of the heavy plate
CN202280085265.9A CN118475708A (zh) 2021-12-29 2022-12-29 厚板及用于制造厚板的针对初加工材料的热机械处理方法
JP2024539500A JP2024546190A (ja) 2021-12-29 2022-12-29 厚鋼板及び厚鋼板の製造のための出発原料に対する加工熱処理方法
KR1020247025495A KR20240132323A (ko) 2021-12-29 2022-12-29 중판 및 중판의 제조를 위한 출발 물질에 대한 열기계적 처리 방법

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
EP21218236.4A EP4206337A1 (fr) 2021-12-29 2021-12-29 Tôle forte et procédé de traitement thermomécanique d'une matière de départ destinée à la fabrication d'une tôle forte

Publications (1)

Publication Number Publication Date
EP4206337A1 true EP4206337A1 (fr) 2023-07-05

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Application Number Title Priority Date Filing Date
EP21218236.4A Withdrawn EP4206337A1 (fr) 2021-12-29 2021-12-29 Tôle forte et procédé de traitement thermomécanique d'une matière de départ destinée à la fabrication d'une tôle forte
EP22844548.2A Pending EP4457370A1 (fr) 2021-12-29 2022-12-29 Plaque lourde et procédé de manipulation thermomécanique de matériau de départ de production de plaque lourde

Family Applications After (1)

Application Number Title Priority Date Filing Date
EP22844548.2A Pending EP4457370A1 (fr) 2021-12-29 2022-12-29 Plaque lourde et procédé de manipulation thermomécanique de matériau de départ de production de plaque lourde

Country Status (6)

Country Link
US (1) US20250051890A1 (fr)
EP (2) EP4206337A1 (fr)
JP (1) JP2024546190A (fr)
KR (1) KR20240132323A (fr)
CN (1) CN118475708A (fr)
WO (1) WO2023126506A1 (fr)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN119617906A (zh) * 2024-11-11 2025-03-14 宝钢湛江钢铁有限公司 一种宽厚板加热炉智能烧钢的方法

Families Citing this family (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN117286420B (zh) * 2023-08-18 2025-09-09 山东钢铁集团日照有限公司 一种高强度轴管用钢的生产方法

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH07278656A (ja) * 1994-04-04 1995-10-24 Nippon Steel Corp 低降伏比高張力鋼の製造方法
JPH07286232A (ja) * 1994-04-18 1995-10-31 Nippon Steel Corp 繰り返し曲げ変形性能の優れた曲げ加工用鋼板とその製造方法
EP2340897A1 (fr) * 2009-12-23 2011-07-06 Voestalpine Grobblech GmbH Procédé de traitement thermomécanique pour tôles épaisses
JP2015127447A (ja) * 2013-12-27 2015-07-09 Ｊｆｅスチール株式会社 耐疲労き裂伝ぱ特性に優れた高強度鋼材およびその判定方法
EP3272899A1 (fr) * 2015-03-20 2018-01-24 Baoshan Iron & Steel Co., Ltd. Tôle d'acier épaisse à haute résistance-ténacité et faible limite conventionnelle d'élasticité présentant une excellente ténacité au choc à basse température et procédé de fabrication s'y rapportant

Family Cites Families (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2001288512A (ja) * 2000-04-05 2001-10-19 Nippon Steel Corp 靱性と延性に優れた高張力鋼の製造方法
ES2614465T3 (es) * 2012-07-10 2017-05-31 Thyssenkrupp Steel Europe Ag Producto plano de acero laminado en frío y procedimiento para su fabricación

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH07278656A (ja) * 1994-04-04 1995-10-24 Nippon Steel Corp 低降伏比高張力鋼の製造方法
JPH07286232A (ja) * 1994-04-18 1995-10-31 Nippon Steel Corp 繰り返し曲げ変形性能の優れた曲げ加工用鋼板とその製造方法
EP2340897A1 (fr) * 2009-12-23 2011-07-06 Voestalpine Grobblech GmbH Procédé de traitement thermomécanique pour tôles épaisses
WO2011079341A2 (fr) 2009-12-23 2011-07-07 Voestalpine Grobblech Gmbh Procédé de traitement thermomécanique
JP2015127447A (ja) * 2013-12-27 2015-07-09 Ｊｆｅスチール株式会社 耐疲労き裂伝ぱ特性に優れた高強度鋼材およびその判定方法
EP3272899A1 (fr) * 2015-03-20 2018-01-24 Baoshan Iron & Steel Co., Ltd. Tôle d'acier épaisse à haute résistance-ténacité et faible limite conventionnelle d'élasticité présentant une excellente ténacité au choc à basse température et procédé de fabrication s'y rapportant

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN119617906A (zh) * 2024-11-11 2025-03-14 宝钢湛江钢铁有限公司 一种宽厚板加热炉智能烧钢的方法

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US20250051890A1 (en) 2025-02-13
CN118475708A (zh) 2024-08-09
JP2024546190A (ja) 2024-12-17
WO2023126506A1 (fr) 2023-07-06
EP4457370A1 (fr) 2024-11-06
KR20240132323A (ko) 2024-09-03

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