EP2977479B1 - Matériau acier présentant une résistance supérieure dans une zone affectée par la chaleur de soudage - Google Patents

Matériau acier présentant une résistance supérieure dans une zone affectée par la chaleur de soudage Download PDF

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EP2977479B1
EP2977479B1 EP14767775.1A EP14767775A EP2977479B1 EP 2977479 B1 EP2977479 B1 EP 2977479B1 EP 14767775 A EP14767775 A EP 14767775A EP 2977479 B1 EP2977479 B1 EP 2977479B1
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rem
steel material
mass
oxides
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EP2977479A4 (fr
EP2977479A1 (fr
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Takashi SUGITANI
Masaki Shimamoto
Hidenori Nako
Sei Kimura
Shinsuke Sato
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Kobe Steel Ltd
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
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    • C—CHEMISTRY; METALLURGY
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
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    • C—CHEMISTRY; METALLURGY
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    • 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
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    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling

Definitions

  • Patent Document 3 is intended to provide a thick steel plate having superior HAZ toughness for super-high heat input welding and a production method thereof. Specifically, in the production method of Patent Document 3, the form of the dendrite formed in a solidification process is further controlled in addition to an adjustment in which the particle compositions of oxides and sulfides, etc., in molten steel are adjusted. Thereby, the production method of Patent Document 3 is said that, austenite particles can be made fine even in a HAZ for super-high heat input welding of no less than 300 kJ/cm by dispersing the dispersed particles in a steel plate more uniformly and finely than related art, thereby allowing HAZ toughness to be remarkably improved.
  • the steel material is characterized as follows: the number of coarse complex oxides having a circular-equivalent diameter of greater than 3 ⁇ m, which adversely affect an improvement in HAZ toughness, is significantly controlled; and complex oxides having a circular-equivalent diameter of 0.1-3 ⁇ m, which is useful for an improvement in HAZ toughness, and having the composition and particle size thereof properly controlled are contained such that the number of the complex oxides is no less than a predetermined value.
  • the steel material according to the embodiment can exert stably superior HAZ toughness even for welding with large heat input.
  • the present steel material containing the aforementioned elements contains complex oxides (oxides and/or oxysulfides) containing REM, Zr, Ti, Al, Ca, and S.
  • the complex oxide included in the present steel material is an Al-Ti-Zr-REM-Ca-S-based complex oxide containing both oxides of Al, Ti, Zr, REM, and Ca and sulfides; however, the complex oxide may contain, other than these, elements such as, for example, Mn and Si, and other component elements.
  • V in an amount of no less than 0.002%, similarly to Nb. However, if the content of V exceeds 0.10%, the precipitating carbonitride is coarsened, which conversely decreases HAZ toughness. Accordingly, the content of V is specified to be no less than 0.002% and no greater than 0.10%.
  • a dissolved oxygen amount and an S concentration in molten steel melted in the vacuum melting furnace were first adjusted.
  • the dissolved oxygen amount (mass% Of) before the addition of complex oxide forming elements was first adjusted to be no greater than 0.005%.
  • the S concentration (mass% S) in the molten steel was adjusted such that the ratio (mass% Of/mass% S) of the dissolved oxygen concentration (mass% Of) to the S concentration (mass% S) was 0.2 ⁇ mass% Of/mass% S ⁇ 9.6.
  • Al which is one of oxysulfide forming elements, was added to the molten steel ahead of Ti.
  • Ca After the addition of REM and Zr, Ca was added and the molten steel was cast. Ca also forms an oxide and a sulfide, but the forms of the oxide and the sulfide are basically dependent on the forms of the inclusions already present in molten steel, and hence the forms of the inclusions, before the addition of Ca, should be particularly noted.
  • a test piece for a welded joint was taken from the thick steel plate and was subjected to V-beveling processing, and electrogas arc welding whose heat input was 60 kJ/mm, equivalent to high heat input welding, was then performed.
  • Three test pieces for Charpy impact test (V-notched test pieces according to JIS Z 2202) were taken, in which a HAZ, located near to a weld line (bond) positioned at a depth of t/4 (t: thickness of the test piece) from the surface of the welded test piece, was processed to have a notch.
  • a Charpy impact test was performed at -40°C on each of the three V-notched test pieces to measure absorbed energy (vE-40), so that the average value and the minimum of the measurement results of the three V-notched test pieces were determined.
  • the test result for HAZ toughness was less than 140 J, namely, in a comparative example in which one or more of the conditions specified in the embodiment were not satisfied, a steel material having superior HAZ toughness was not able to be obtained.
  • 59 and 61-67 of the comparative examples represents an example in which the number of complex oxides having a circular-equivalent diameter of 0.1-3 ⁇ m was less than 100, and the test result for the HAZ toughness of each of them was greatly less than 140 J.
  • Fig. 2 is a graph showing the HAZ toughness of the steel materials according to the present embodiment shown in Table 4 and those of the steel materials Nos. 32-55 of the comparative examples shown in Table 7.
  • the number of complex oxides having a circular-equivalent diameter of greater than 3 ⁇ m is less than 5.0/mm 2 and the number of complex oxides having a circular-equivalent diameter of 0.1-3 ⁇ m is at least 100; however, each of the steel materials Nos. 32-55 of the comparative examples represents an example in which the average composition of a complex oxide does not satisfy the conditions specified in the embodiment, and the test result for HAZ toughness of each of them was greatly less than 140 J.
  • a steel plate according to the present invention achieves superior HAZ toughness even for high heat input welding, and hence is suitable to be used in welded structures, such as ships, constructions, and bridges.

Claims (1)

  1. Matériau acier ayant une résistance supérieure au niveau d'une zone affectée par la chaleur de soudage, le matériau acier étant constitué de, en % massique :
    0,02 à 0,13 % de C,
    0,05 à 0,5 % de Si,
    1,0 à 2,5 % de Mn,
    pas plus de 0,03 % de P, en excluant 0 %,
    pas plus de 0,01 % de S, en excluant 0 %,
    0,002 à 0,040 % d'AI,
    0,005 à 0,040 % de Ti,
    0,0003 à 0,020 % de Zr,
    0,0003 à 0,0020 % de REM,
    0,0003 à 0,0080 % de Ca,
    0,0030 à 0,010 % de N, et
    0,0003 à 0,0050 % de O,
    éventuellement d'au moins l'un parmi :
    0,05 à 1,50 % de Ni,
    0,05 à 1,50 % de Cu,
    0,05 à 1,50 % de Cr,
    0,05 à 1,50 % de Mo,
    0,002 à 0,10 % de Nb,
    0,002 à 0,10 % de V, et
    0,0005 à 0,0050 % de B,
    avec le reste constitué de fer et d'impuretés inévitables, dans lequel le matériau acier contient un oxyde complexe contenant du REM, du Zr, du Ti, de l'Al, du Ca, et du S, et dans lequel par rapport à l'oxyde complexe dans le matériau acier,
    le nombre d'oxydes complexes ayant un diamètre équivalent en cercle supérieur à 3 µm n'est pas supérieur à 5,0/mm2, et
    le nombre d'oxydes complexes ayant un diamètre équivalent en cercle de 0,1 à 3 µm et satisfaisant une formule (1) est d'au moins 100/mm2,
    et de plus, la composition moyenne des oxydes complexes qui sont de 0,1 à 3 µm satisfaisant une formule (1) contient 20 % ou moins d'Al2O3, de 3 à 20 % de TiO2, de 5 à 50 % de ZrO2, de 5 à 50 % d'oxyde REM, de 5 à 50% de CaO, et de 1 à 15% de S, dans lequel la composition de l'oxyde complexe ayant une taille de 0,1 à 3 µm est mesurée à une profondeur de t/4 depuis la surface d'une plaque d'acier épaisse, où t représente l'épaisseur de ladite plaque d'acier épaisse, 0,008 ≤ 1 / d × % massique S/ % massique CaO + % massique REM 2 O 3 ≤ 0,289
    Figure imgb0011
     où d représente le diamètre équivalent en cercle de chaque oxyde complexe, et va de 1 à 3 µm.
EP14767775.1A 2013-03-22 2014-03-17 Matériau acier présentant une résistance supérieure dans une zone affectée par la chaleur de soudage Not-in-force EP2977479B1 (fr)

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JP2013060452A JP6226542B2 (ja) 2013-03-22 2013-03-22 溶接熱影響部の靭性に優れた鋼材
PCT/JP2014/057205 WO2014148447A1 (fr) 2013-03-22 2014-03-17 Matériau acier présentant une résistance supérieure dans une zone affectée par la chaleur de soudage

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EP2977479A1 EP2977479A1 (fr) 2016-01-27
EP2977479A4 EP2977479A4 (fr) 2016-11-30
EP2977479B1 true EP2977479B1 (fr) 2018-04-25

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JP6301805B2 (ja) * 2014-10-17 2018-03-28 株式会社神戸製鋼所 溶接熱影響部の靭性に優れたタンク用厚鋼板
JP2016216819A (ja) * 2015-05-22 2016-12-22 株式会社神戸製鋼所 厚鋼板及び溶接継手
WO2017094593A1 (fr) * 2015-12-04 2017-06-08 株式会社神戸製鋼所 Tôle d'acier non traitée thermiquement ayant une limite élastique élevée dans laquelle la dureté d'une zone affectée par la chaleur de soudage et la dégradation de la ténacité à basse température de la zone affectée par la chaleur de soudage sont supprimées
WO2017141425A1 (fr) * 2016-02-19 2017-08-24 新日鐵住金株式会社 Acier
US20190032178A1 (en) * 2016-02-19 2019-01-31 Nippon Steel & Sumitomo Metal Corporation Steel
CN107709599B (zh) * 2016-04-19 2018-10-02 新日铁住金株式会社 钢材
JP6828638B2 (ja) * 2017-08-14 2021-02-10 日本製鉄株式会社 鋼板および鋼板の製造方法
JP2018016890A (ja) * 2017-09-26 2018-02-01 株式会社神戸製鋼所 溶接熱影響部の靱性に優れたタンク用厚鋼板
JP7172100B2 (ja) * 2018-04-02 2022-11-16 日本製鉄株式会社 無方向性電磁鋼板
JP7328491B2 (ja) * 2018-11-09 2023-08-17 日本製鉄株式会社 無方向性電磁鋼板
CN116752044A (zh) 2019-06-27 2023-09-15 日本制铁株式会社 钢材及其制造方法
CN114032469B (zh) * 2021-03-04 2022-05-20 东北大学 一种含锆细晶粒热轧板带钢及其制备方法
CN114075617B (zh) * 2021-09-30 2023-05-16 山东钢铁股份有限公司 一种降低钢材中TiN夹杂危害性的方法

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JP4261968B2 (ja) 2003-04-24 2009-05-13 新日本製鐵株式会社 溶接熱影響部靭性の優れた鋼材およびその製造方法
JP4515428B2 (ja) * 2006-09-29 2010-07-28 株式会社神戸製鋼所 溶接熱影響部の靭性および脆性破壊発生特性に優れた鋼材およびその製法
JP5201665B2 (ja) * 2007-11-13 2013-06-05 株式会社神戸製鋼所 大入熱溶接時の熱影響部の靭性に優れた溶接用高張力厚鋼板
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WO2014148447A1 (fr) 2014-09-25
JP6226542B2 (ja) 2017-11-08
KR20150119391A (ko) 2015-10-23
JP2014185364A (ja) 2014-10-02
CN105051229B (zh) 2017-03-15
CN105051229A (zh) 2015-11-11
EP2977479A4 (fr) 2016-11-30
EP2977479A1 (fr) 2016-01-27
KR101718275B1 (ko) 2017-03-20

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