WO2001086013A1 - Tole d'acier epaisse excellente du point de vue de ses caracteristiques ctod dans la zone affectee par la chaleur du soudage et dont la limite conventionnelle d'elasticite est superieure ou egale a 460 mpa - Google Patents

Tole d'acier epaisse excellente du point de vue de ses caracteristiques ctod dans la zone affectee par la chaleur du soudage et dont la limite conventionnelle d'elasticite est superieure ou egale a 460 mpa Download PDF

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Publication number
WO2001086013A1
WO2001086013A1 PCT/JP2001/003876 JP0103876W WO0186013A1 WO 2001086013 A1 WO2001086013 A1 WO 2001086013A1 JP 0103876 W JP0103876 W JP 0103876W WO 0186013 A1 WO0186013 A1 WO 0186013A1
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WO
WIPO (PCT)
Prior art keywords
haz
steel
mass
yield strength
oxide
Prior art date
Application number
PCT/JP2001/003876
Other languages
English (en)
Japanese (ja)
Inventor
Akihiko Kojima
Yoshio Terada
Akihito Kiyose
Yuzuru Yoshida
Toshihiko Adachi
Kazuaki Tanaka
Ryuji Uemori
Shiro Imai
Original Assignee
Nippon Steel Corporation
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 Nippon Steel Corporation filed Critical Nippon Steel Corporation
Priority to DE60108350T priority Critical patent/DE60108350T2/de
Priority to EP01930007A priority patent/EP1221493B1/fr
Publication of WO2001086013A1 publication Critical patent/WO2001086013A1/fr

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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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • 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
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • 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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • 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
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/004—Dispersions; Precipitations

Definitions

  • the present invention relates to a steel plate having a yield strength of 460 MPa or more, preferably 500 to 550 MPa class, which is excellent in CTOD (Crack Tip Opening Displacement) characteristics of a heat affected zone (HAZ). It is mainly used for offshore structures, but can also be applied to other welded structures requiring similar strength and HAZ toughness (CTOD properties).
  • CTOD Cross Tip Opening Displacement
  • this technique reduces the pinning effect of TiN particles and increases the coarseness of ⁇ grains.
  • the microstructure of the HAZ structure can be reduced. It is steel that has been thinned. This acicular ferrite that effectively refines coarse 0 / grain is called intragranular ferrite (IGF).
  • IGF intragranular ferrite
  • An object of the present invention is to provide a steel plate having a yield strength of 460 MPa or more, preferably of a class of 500 to 550 MPa, and a CT0D at 110 ° C. of HAZ of 0.2 mm or more.
  • the present invention relates to
  • FIG. 1 (a) schematically shows the HAZ organization at this time.
  • the primary cause of HAZ embrittlement is that even if the inside of coarse y grains is refined by the formation of intragranular transformation ferrite (IGF), they are formed along the coarse ⁇ grain boundaries. This is because coarse grain boundary ferrite (GBF) ⁇ ferrite side plate (FSP) increases the sensitivity to brittle crushing as HAZ hardens.
  • IGF intragranular transformation ferrite
  • Mg is intentionally added to generate a large number of the above-mentioned ultrafine oxides. Since Mg is also contained in an oxide having a normal size (several ⁇ ), the present invention has sought to generate IGF using such a relatively large Mg-containing oxide. As a result, it was found that the following three conditions were important as IGF metamorphosis nuclei.
  • Mn must be contained in an amount of 0.3% by mass or more in order to function effectively as an IGF transformation nucleus.
  • Mn may be contained in an oxide of 0.5 to 10 ⁇ m.
  • Mg, Al, and Ti which have a higher deoxidizing power than Mn, are essential, so these elements form oxides of 0.5 to 10 ⁇ m.
  • the Mg content in the oxide was important.
  • the oxide contained 10% by mass or more of 3 ⁇ 4.
  • the Mg content in the oxides in which the sulfides did not complex and existed alone were less than 10% by mass.
  • Ca, REM and Zr can be added as deoxidizers and desulfurizers. It contributes to the reduction of O content as a deoxidizer. As a desulfurizing agent, it contributes to the reduction of S content and at the same time controls the form of sulfide. To improve the base metal and HAZ material through these effects, 0.0005% or more is required for each. However, if these elements are too large, they become incorporated into the IGF transformation nucleus, and the Mg and Mn contents in the oxides and sulfides that constitute the IGF transformation nucleus decrease, and the IGF transformation occurs. It loses its core function.
  • V is effective for the strength of base metal and HAZ by precipitation strengthening. For this purpose, 0.005% or more is required. However, if V exceeds 0.05%, weldability and HAZ toughness deteriorate, so this is set as the upper limit.
  • the steel of the present invention is manufactured as a steel plate by adjusting the chemical composition to a predetermined chemical composition in the steelmaking process of the steel industry, reheating a continuously manufactured piece, and controlling various processes of rolling, cooling, and heat treatment in various ways. Is done. In order to obtain a yield strength of 460 MPa or more, preferably 500 to 550 MPa class in a thick material such as a plate thickness of 76.2 mm, direct quenching or It is effective to apply accelerated cooling. Furthermore, tempering can adjust strength and toughness. ⁇ It is also possible to perform hot charge rolling without cooling the piece. HAZ toughness is determined by the dispersion of pinned particles and IGF transformation nuclei in addition to the steel composition. Dispersion of these particles The state does not change significantly during the manufacturing process of the base material. Therefore, the HAZ toughness does not largely depend on the manufacturing process of the base material, and any heating, rolling, or heat treatment process may be applied.
  • Table 1 shows the chemical composition of the continuously formed steel
  • Table 2 shows the thickness of the steel sheet, the manufacturing method, the number of pinning particles and IGF transformation nuclei, the base material, welding conditions, and toughness.
  • J Z' 200 ⁇ 0 ⁇ 0 00 '0 100 ⁇ ⁇ 00 ⁇ 0 800 ⁇ 0 800' 0 0 ⁇ 0, 00 ⁇ 0 S00 ⁇ 0 09 ⁇ 9 ⁇ ⁇ 0 II ⁇ 0 6
  • Z ⁇ zoo ⁇ 0 ZOO ⁇ 3 '9 ⁇ 0: ⁇ 3' 9 ⁇ 0: ⁇ S00 ⁇ 0 ⁇ ' ⁇ 200 ⁇ 600 ⁇ 0 S00 ⁇ 0 20 ⁇ 0 100 ⁇ 0, 00 ⁇ 0 6S ⁇ 02 ⁇ 0 01 0 ⁇
  • the present invention has significantly improved the CTOD characteristics of joints of high-strength and extremely-thick steel plates, and has opened the way to lighter and larger offshore structures. As a result, the cost of building offshore structures can be significantly reduced, and energy development in deeper sea areas becomes possible.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Treatment Of Steel In Its Molten State (AREA)
  • Paper (AREA)

Abstract

L'invention concerne une tôle d'acier épaisse, caractérisée en ce qu'elle possède la composition chimique (pourcentage en masse) suivante : de 0,04 à 0,14 % de C ; moins de 0,4 % de Si ; de 1,0 à 2,0 % de Mn ; moins de 0,02 % de P ; de 0,001 à 0,005 % de S ; de 0,001 à 0,01 % de Al ; de 0,005 à 0,03 % de Ti ; de 0,005 à 0,05 % de Nb ; de 0,0003 à 0,005 % de Mg ; de 0,001 à 0,005 % de O ; de 0,001 à 0,01 % de N, le reste étant du Fe et des impuretés inévitables. Ladite tôle renferme également du TiN, qui comprend un oxyde renfermant Mg et Al, d'une granulométrie comprise entre 0,01 et 0,5 νm, et qui est présent à raison de 10 000 unités/mm2 au moins, et des particules d'un composite constitué d'un oxyde et d'un sulfure contenant au moins 0,3 % en masse de Mn, d'une granulométrie comprise entre 0,5 et 10 νm, et qui sont présentes à raison de 10 unités/mm2 au moins. Ladite tôle d'acier possède une limite conventionnelle d'élasticité supérieure ou égale à 460 Mpa et un CTOD (Crack Tip Opening Displacement) dans la zone affectée par la chaleur à 10 °C de 0,2 mm au moins.
PCT/JP2001/003876 2000-05-09 2001-05-09 Tole d'acier epaisse excellente du point de vue de ses caracteristiques ctod dans la zone affectee par la chaleur du soudage et dont la limite conventionnelle d'elasticite est superieure ou egale a 460 mpa WO2001086013A1 (fr)

Priority Applications (2)

Application Number Priority Date Filing Date Title
DE60108350T DE60108350T2 (de) 2000-05-09 2001-05-09 Dicke stahlplatte mit hervorragenden ctod-eigenschaften der durch schweissen beeinflussten bereiche und mit einer streckgrenze von 460 mpa oder mehr
EP01930007A EP1221493B1 (fr) 2000-05-09 2001-05-09 Tole d'acier epaisse excellente du point de vue de ses caracteristiques ctod dans la zone affectee par la chaleur du soudage et dont la limite conventionnelle d'elasticite est superieure ou egale a 460 mpa

Applications Claiming Priority (6)

Application Number Priority Date Filing Date Title
JP2000136105 2000-05-09
JP2000-348257 2000-11-15
JP2000-136105 2000-11-15
JP2000348257 2000-11-15
JP2001-049838 2001-02-26
JP2001049838A JP3699657B2 (ja) 2000-05-09 2001-02-26 溶接熱影響部のＣＴＯＤ特性に優れた４６０ＭＰａ以上の降伏強度を有する厚鋼板

Publications (1)

Publication Number Publication Date
WO2001086013A1 true WO2001086013A1 (fr) 2001-11-15

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PCT/JP2001/003876 WO2001086013A1 (fr) 2000-05-09 2001-05-09 Tole d'acier epaisse excellente du point de vue de ses caracteristiques ctod dans la zone affectee par la chaleur du soudage et dont la limite conventionnelle d'elasticite est superieure ou egale a 460 mpa

Country Status (6)

Country Link
JP (1) JP3699657B2 (fr)
KR (1) KR100469378B1 (fr)
CN (1) CN1188535C (fr)
DE (1) DE60108350T2 (fr)
TW (1) TW541343B (fr)
WO (1) WO2001086013A1 (fr)

Cited By (4)

* Cited by examiner, † Cited by third party
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CN102400053A (zh) * 2010-09-07 2012-04-04 鞍钢股份有限公司 屈服强度460MPa级建筑结构用钢板及其制造方法
CN102459656A (zh) * 2009-06-11 2012-05-16 新日本制铁株式会社 大线能量焊接热影响区韧性优异的厚壁高强度钢板的制造方法、以及大线能量焊接热影响区韧性优异的厚壁高强度钢板
US8361248B2 (en) 2007-12-07 2013-01-29 Nippon Steel Corporation Steel superior in CTOD properties of weld heat-affected zone and method of production of same
US8668784B2 (en) 2009-05-19 2014-03-11 Nippon Steel & Sumitomo Metal Corporation Steel for welded structure and producing method thereof

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JP4528089B2 (ja) * 2003-10-22 2010-08-18 新日本製鐵株式会社 耐脆性破壊発生特性を有する船体用大入熱突合せ溶接継手
JP4891836B2 (ja) * 2007-05-09 2012-03-07 株式会社神戸製鋼所 大入熱溶接における溶接熱影響部の靭性に優れた鋼板
CN101578380B (zh) * 2007-12-06 2011-01-12 新日本制铁株式会社 脆性破坏传播停止特性与大线能量焊接热影响部韧性优异的厚壁高强度钢板及其制造方法
JP5439887B2 (ja) * 2008-03-31 2014-03-12 Ｊｆｅスチール株式会社 高張力鋼およびその製造方法
JP4399018B1 (ja) * 2008-07-15 2010-01-13 新日本製鐵株式会社 溶接熱影響部の靭性に優れた鋼板
CN101845590A (zh) * 2009-03-25 2010-09-29 株式会社神户制钢所 焊接热影响部的韧性优良的钢材
TWI365915B (en) * 2009-05-21 2012-06-11 Nippon Steel Corp Steel for welded structure and producing method thereof
US9403242B2 (en) 2011-03-24 2016-08-02 Nippon Steel & Sumitomo Metal Corporation Steel for welding
JP5201301B1 (ja) * 2011-11-25 2013-06-05 新日鐵住金株式会社 溶接用鋼材
KR101719943B1 (ko) 2013-03-12 2017-03-24 제이에프이 스틸 가부시키가이샤 다층 용접 조인트 ctod 특성이 우수한 후강판 및 그 제조 방법
US10855194B2 (en) 2015-12-22 2020-12-01 Thermatool Corp. High frequency power supply system with closely regulated output for heating a workpiece
CN106011361B (zh) * 2016-07-08 2018-07-31 华北理工大学 提高焊接性能的Mo-Nb-Ti-Mg钢冶炼方法
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KR102027871B1 (ko) 2017-10-03 2019-10-04 닛폰세이테츠 가부시키가이샤 강판 및 강판의 제조 방법
KR102045641B1 (ko) 2017-12-22 2019-11-15 주식회사 포스코 저온에서의 내파괴 특성이 우수한 극지 환경용 고강도 강재 및 그 제조방법
CN109930056B (zh) * 2019-04-09 2020-01-07 东北大学 一种400MPa级细晶粒螺纹钢筋及其制造方法

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JPH09157787A (ja) * 1995-12-06 1997-06-17 Nippon Steel Corp 超大入熱溶接熱影響部の靱性に優れた溶接用高張力鋼
JPH09176730A (ja) * 1995-12-27 1997-07-08 Sumitomo Metal Ind Ltd 靱性に優れた厚鋼板の製造法
JPH09310147A (ja) * 1996-05-21 1997-12-02 Nippon Steel Corp 溶接熱影響部靭性の優れた鋼板
JPH101744A (ja) * 1996-04-17 1998-01-06 Nippon Steel Corp 溶接熱影響部靭性の優れた鋼
JPH108132A (ja) * 1996-06-14 1998-01-13 Sumitomo Metal Ind Ltd 靭性に優れた厚鋼板の製造方法
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JPH10298708A (ja) * 1997-02-28 1998-11-10 Nippon Steel Corp 超大入熱溶接熱影響部の靱性に優れた溶接用高張力鋼
JPH11236645A (ja) * 1998-02-24 1999-08-31 Nippon Steel Corp 超大入熱溶接熱影響部の靱性に優れた溶接用高張力鋼
JPH11264048A (ja) * 1998-03-16 1999-09-28 Nippon Steel Corp 溶接部靱性の優れた高強度鋼板
JPH11279684A (ja) * 1998-03-26 1999-10-12 Nippon Steel Corp 超大入熱溶接熱影響部の靱性に優れた溶接用高張力鋼
JPH11286743A (ja) * 1998-04-01 1999-10-19 Nippon Steel Corp 超大入熱溶接用高張力鋼
JPH11293382A (ja) * 1998-04-15 1999-10-26 Nippon Steel Corp Ｍｇを含有する超大入熱溶接用鋼
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JPH09157787A (ja) * 1995-12-06 1997-06-17 Nippon Steel Corp 超大入熱溶接熱影響部の靱性に優れた溶接用高張力鋼
JPH09176730A (ja) * 1995-12-27 1997-07-08 Sumitomo Metal Ind Ltd 靱性に優れた厚鋼板の製造法
JPH101744A (ja) * 1996-04-17 1998-01-06 Nippon Steel Corp 溶接熱影響部靭性の優れた鋼
JPH09310147A (ja) * 1996-05-21 1997-12-02 Nippon Steel Corp 溶接熱影響部靭性の優れた鋼板
JPH108132A (ja) * 1996-06-14 1998-01-13 Sumitomo Metal Ind Ltd 靭性に優れた厚鋼板の製造方法
JPH1053838A (ja) * 1996-08-12 1998-02-24 Nippon Steel Corp 溶接熱影響部靭性の優れた鋼板
JPH10298708A (ja) * 1997-02-28 1998-11-10 Nippon Steel Corp 超大入熱溶接熱影響部の靱性に優れた溶接用高張力鋼
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JPH11236645A (ja) * 1998-02-24 1999-08-31 Nippon Steel Corp 超大入熱溶接熱影響部の靱性に優れた溶接用高張力鋼
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JPH11279684A (ja) * 1998-03-26 1999-10-12 Nippon Steel Corp 超大入熱溶接熱影響部の靱性に優れた溶接用高張力鋼
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JPH11293382A (ja) * 1998-04-15 1999-10-26 Nippon Steel Corp Ｍｇを含有する超大入熱溶接用鋼

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Cited By (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US8361248B2 (en) 2007-12-07 2013-01-29 Nippon Steel Corporation Steel superior in CTOD properties of weld heat-affected zone and method of production of same
US8668784B2 (en) 2009-05-19 2014-03-11 Nippon Steel & Sumitomo Metal Corporation Steel for welded structure and producing method thereof
CN102459656A (zh) * 2009-06-11 2012-05-16 新日本制铁株式会社 大线能量焊接热影响区韧性优异的厚壁高强度钢板的制造方法、以及大线能量焊接热影响区韧性优异的厚壁高强度钢板
CN102459656B (zh) * 2009-06-11 2013-08-14 新日本制铁株式会社 大线能量焊接热影响区韧性优异的厚壁高强度钢板的制造方法
CN102400053A (zh) * 2010-09-07 2012-04-04 鞍钢股份有限公司 屈服强度460MPa级建筑结构用钢板及其制造方法
CN102400053B (zh) * 2010-09-07 2014-03-12 鞍钢股份有限公司 屈服强度460MPa级建筑结构用钢板及其制造方法

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DE60108350D1 (de) 2005-02-17
KR100469378B1 (ko) 2005-02-02
JP3699657B2 (ja) 2005-09-28
CN1188535C (zh) 2005-02-09
KR20020028203A (ko) 2002-04-16
CN1380910A (zh) 2002-11-20
DE60108350T2 (de) 2005-12-22
JP2002212670A (ja) 2002-07-31
TW541343B (en) 2003-07-11

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