EP2060643B1 - Steel excelling in toughness at region affected by welding heat - Google Patents

Steel excelling in toughness at region affected by welding heat Download PDF

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Publication number
EP2060643B1
EP2060643B1 EP06843367A EP06843367A EP2060643B1 EP 2060643 B1 EP2060643 B1 EP 2060643B1 EP 06843367 A EP06843367 A EP 06843367A EP 06843367 A EP06843367 A EP 06843367A EP 2060643 B1 EP2060643 B1 EP 2060643B1
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EP
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Prior art keywords
toughness
steel
less
ceh
acc
Prior art date
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EP06843367A
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German (de)
English (en)
French (fr)
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EP2060643A1 (en
EP2060643A4 (en
Inventor
Ryuji Uemori
Yoshiyuki Watanabe
Kazuhiro Fukunaga
Yoshihide Nagai
Rikio Chijiiwa
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Nippon Steel Corp
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Nippon Steel Corp
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    • 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
    • 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 by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/50—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for welded joints
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese

Definitions

  • the present invention relates to steel excellent in toughness of the weld heat affected zone (HAZ) in small heat input welding to medium heat input welding and a method of production thereof.
  • HZ weld heat affected zone
  • the HAZ toughness of a low alloy steel is governed by various factors such as (1) the size of the crystal grains, (2) the state of dispersion of hard phases such as high-carbon martensite (M*), upper bainite (Bu), and ferrite sideplate (FSP), (3) the state of precipitation hardening, (4) the presence of any intergranular embrittlement, and (5) the microsegregation of the elements. These factors are known to have a large effect on the toughness. Many technologies are being commercialized in order to improve the HAZ toughness.
  • the point of the steel according to the prior invention not substantially including any Al and Nb is made use of in the present invention as well.
  • the C content is high, so the problem of the drop in toughness when increasing the Mn content remains unsolved. Further, there was a concern over the impurities Nb and V having a detrimental effect on the toughness.
  • JP-A-2003-147484 follows the thinking of JP-A-5-247531 and, while making use of Ti oxides, adds Nb and raises the Mn content. This causes the austenite-ferrite transformation start temperature to drop to thereby suppress the formation of the hard phases and simultaneously to obtain a suitable microstructure to thereby satisfy the -10°C CTOD property.
  • the invention of this JP-A-2003-147484 did not sufficiently satisfy the required CTOD property of weld joints at the much tougher level of -40°C or less.
  • JP 2001 355 039 discloses an ultrahigh strength steel tube excellent in the low temperature toughness of the weld metal, but which contains relatively high amounts of niobium and molybdenum.
  • the present invention provides technology which inexpensively produces high strength steel excellent in toughness in multi-layer welding of small to medium heat input.
  • the steel produced by the present invention is extremely good in the CTOD property of multi-layer weld zones of small to medium heat input among the levels of weld heat affected zone toughness.
  • the gist of the present invention is as follows.
  • the CTOD property of the HAZ at the time of small to medium heating input (1.5 to 6.0 kJ/mm with a sheet thickness of 50 mm) welding (CTOD property at temperature of -40°C or less) is governed by the toughness of extremely local regions. Control of the microstructure of this portion and reduction of the embrittlement elements are important. In other words, the CTOD property is not the average property of the material, but is governed by the local embrittlement zones. If there are regions which cause embrittlement, even in just parts of the steel material, the CTOD property of the steel sheet will be remarkably impaired.
  • the local regions which exert the greatest effects on the CTOD property are M*, ferrite sideplate (FSP), and other hard phases.
  • FSP ferrite sideplate
  • the present invention is characterized by the following discoveries and their embodiment in a steel of a high HAZ toughness. Specifically,
  • FIG. 2 shows the results when producing 20 kg of steel of the steel ingredients of 0.05% C-0.15%Si-1.7 to 2.7%Mn by vacuum melting, rolling it to steel sheet, imparting a heat history of an actual welded joint three times by a simulated thermal cycle device, then running a CTOD test.
  • T ⁇ c 0.1 (670.9 CeH-67.6) is the temperature when the lowest value of three CTOD test values at different test temperatures is 0.1 mm. There is a clear trend for the T ⁇ c 0.1 (CTOD property) to excellent substantially linear behavior as the CeH drops. If the CeH drops to around 0.01, it is learned that the T ⁇ c 0.1 reaches -60°C.
  • the intended CTOD property can be obtained.
  • control of the value of CeH according to the required CTOD property is one of the characterizing features of the invention.
  • rectifying the contents of the other alloy elements is required for realizing steel provided with both high strength and a superior CTOD property.
  • C has to be 0.02% or more in order to obtain strength, but if over 0.06%, it degrades the toughness of the welding HAZ and does not allow satisfaction of a good CTOD property, so 0.06% is made the upper limit.
  • Si inhibits the HAZ toughness, so a smaller amount is preferable in order to obtain a good HAZ toughness.
  • no Al is added, so addition of 0.05% or more is necessary for deoxidation.
  • the content is over 0.30%, the HAZ toughness is harmed, so 0.30% is made the upper limit.
  • Mn is an inexpensive element with a large effect of rectifying the microstructure and lowers the CeH, so addition does not harm the HAZ toughness of small to medium heat input, therefore it is desirable to make the content large and obtain a high strength.
  • the content was made to an upper limit of 2.7%. Further, if less than 1.7%, the effect is small, so the lower limit was made 1.7%. Note that from the viewpoint of toughness, over 2.0% is more preferable.
  • P and S should both be small in amount from the viewpoints of base material toughness and HAZ toughness, but there are limits to their reduction in industrial production. 0.015% and 0.010%, preferably 0.008% and 0.005%, were therefore made the upper limits.
  • Al is not deliberately added in the present invention, but inclusion as an impurity in the steel is unavoidable. This forms Al oxides which inhibit the formation of Ti oxides, so a smaller content is desirable, but there are limits to its reduction in industrial production. 0.004% is therefore the upper limit.
  • Ti forms Ti oxides and makes the microstructure finer, so greatly contributes to improvement of the toughness, but if the content is too great, it forms TiC. This degrades the HAZ toughness, so 0.005 to 0.015% is a suitable range.
  • O is necessary for the formation of a large amount of oxides of Ti. If less than 0.0010%, the effect is small, while if over 0.0045%, it forms coarse Ti oxides and sharply degrades the toughness, so the range of content was made 0.0010 to 0.0045%.
  • N is necessary to form fine Ti nitrides and improve the base material toughness and HAZ toughness, but if less than 0.002%, the effect is small, while if over 0.006%, surface defects are formed at the time of billet production, so the upper limit was made 0.006%.
  • Nb and V are inherently embrittlement elements. As shown by the large coefficient in formula (A), their presence causes the CeH to greatly rise and made the HAZ toughness remarkably fall, so these are not deliberately added in the present invention. Even when included as impurities in the steel, to secure toughness, Nb has to be limited to 0.003% or less. Further, V has to be limited to 0.030% or less, preferably 0.020% or less.
  • Cu and Ni result in little deterioration of the HAZ toughness due to their addition, have the effect of increasing the strength of the base material, and are effective for the further improvement of the properties, but increase the production costs, so the upper limits of the contents when added were made Cu: 0.25% and Ni: 0.50%.
  • the present invention steel is preferably produced industrially by continuous casting.
  • the reasons are that the solidification cooling rate of the molten steel is fast and it is possible to form fine Ti oxides and Ti nitrides in large amounts in the slab.
  • the reheating temperature has to be made 1100°C or less. If the reheating temperature exceeds 1100°C, the Ti nitrides becomes coarser, the toughness of the base material decreases, and the effect of improvement of the HAZ toughness cannot be expected.
  • thermo-mechanical control process the method of production after reheating requires treatment by thermo-mechanical control process.
  • the reason is that even if a superior HAZ toughness is obtained, if the toughness of the base material is inferior, the steel product is insufficient.
  • methods of treatment by thermo-mechanical control process 1) controlled rolling, 2) controlled rolling-accelerated cooling, 3) direct quenching-tempering after rolling, etc. can be mentioned, but the preferred methods are controlled rolling-accelerated cooling and the direct quenching-tempering after rolling.
  • the above method is one example of a method of production of the present invention steel.
  • the method of production of the present invention steel is not limited to the above method.
  • Thick-gauge steel sheets of various steel ingredients were produced by the converter-continuous casting-thick-gauge sheet process.
  • the base material strength was determined and a CTOD test of the weld joints was run.
  • the welding was performed by the submerged arc welding (SAW) method, generally used for test welding, with a welding heat input of 4.5 to 5.0 kJ/mm at the K groove so that the weld fusion line (FL) became perpendicular.
  • SAW submerged arc welding
  • the CTOD test was run by a sheet of a size of t (sheet thickness) x 2t notched by introducing a 50% fatigue crack in the FL location.
  • Table 1 shows examples of the present invention and comparative examples.
  • the steel sheets produced by the present invention had yield strengths (YS) of 430 N/mm 2 or more and exhibited good breaking toughness of CTOD values at -20°C, -40°C, and -60°C all of 0.27 mm or more.
  • Comparative Steels 21 to 26 had strengths and CTOD values inferior to the invention steels and did not possess the properties necessary as steel sheet used under harsh environments. Comparative Steel 21 had Nb added, therefore the Nb content of the steel sheet became too great. The value of CeH also became high, so the CTOD value was a low value. Comparative Steel 22 had too great a C content and also too great a value of CeH, so the CTOD value was a low value. Comparative Steels 23 and 24 had low CeH's, but the Al content was too high, Ti oxides were insufficiently formed, and the microstructure was not sufficiently made finer.
  • Comparative Steel 25 had a CeH of about the same extent as the invention steel, but the C was too low and the O was too great, so the base material strength was low and the CTOD value was a low value. Comparative Steel 26 had an excessively large amount of Nb mixed in as an impurity, so despite CeH being low, the base material strength and CTOD value were low values.
  • the steel produced by the present invention is high in strength, has an extremely good CTOD property of the FL part where the toughness degrades the most at the time of welding, and exhibits superior toughness. Due to this, production of a high strength steel product that can be used in offshore structures, earthquake resistant buildings, and other harsh environments became possible.

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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)

Abstract

本発明は、質量％で、Ｃ：０．０２～０．０６％、Ｓｉ：０．０５～０．３０％、Ｍｎ：１．７～２．７％、Ｐ：０．０１５％以下、Ｓ：０．０１０％以下、Ｔｉ：０．００５～０．０１５％、Ｏ：０．００１０～０．００４５、Ｎ：０．００２０～０．００６０％を含有し、残部が鉄および不可避的不純物からなり、不純物としての混入量がＡｌ：０．００４％以下、Ｎｂ：０．００３％以下、Ｖ：０．０３０％以下に制限され、（Ａ）式で表されるＣｅＨが０．０４以下の範囲であることを特徴とする溶接熱影響部の靭性に優れた鋼である。ＣｅＨ＝Ｃ＋１／４Ｓｉ−１／２４Ｍｎ＋１／４８Ｃｕ＋１／３２Ｎｉ＋１／０．４Ｎｂ＋１／２Ｖ　・・・　（Ａ）但し、Ｃ、Ｓｉ，Ｍｎ，Ｃｕ，Ｎｉ，Ｎｂ，Ｖは、それぞれ鋼成分（質量％）を示す。
EP06843367A 2006-12-20 2006-12-20 Steel excelling in toughness at region affected by welding heat Active EP2060643B1 (en)

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
PCT/JP2006/325984 WO2008075443A1 (ja) 2006-12-20 2006-12-20 溶接熱影響部の靭性に優れた鋼

Publications (3)

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EP2060643A1 EP2060643A1 (en) 2009-05-20
EP2060643A4 EP2060643A4 (en) 2010-12-01
EP2060643B1 true EP2060643B1 (en) 2012-04-18

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EP06843367A Active EP2060643B1 (en) 2006-12-20 2006-12-20 Steel excelling in toughness at region affected by welding heat

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EP (1) EP2060643B1 (ja)
KR (1) KR100940617B1 (ja)
CN (1) CN100594250C (ja)
BR (1) BRPI0607524B1 (ja)
CA (1) CA2602076C (ja)
WO (1) WO2008075443A1 (ja)

Families Citing this family (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP4751341B2 (ja) * 2007-01-11 2011-08-17 新日本製鐵株式会社 溶接熱影響部のｃｔｏｄが優れた鋼およびその製造方法
KR20110125277A (ko) 2007-12-07 2011-11-18 신닛뽄세이테쯔 카부시키카이샤 용접열 영향부의 ｃｔｏｄ 특성이 우수한 강 및 그 제조 방법
RU2458174C1 (ru) 2009-05-19 2012-08-10 Ниппон Стил Корпорейшн Сталь для сварных конструкций и способ ее получения
TWI365915B (en) * 2009-05-21 2012-06-11 Nippon Steel Corp Steel for welded structure and producing method thereof
KR101360737B1 (ko) 2009-12-28 2014-02-07 주식회사 포스코 취성 균열 발생 저항성이 우수한 고강도 강판 및 그 제조방법
JP2011246804A (ja) * 2010-04-30 2011-12-08 Nippon Steel Corp 電子ビーム溶接継手及び電子ビーム溶接用鋼材とその製造方法
US9403242B2 (en) 2011-03-24 2016-08-02 Nippon Steel & Sumitomo Metal Corporation Steel for welding

Family Cites Families (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS624826A (ja) * 1985-07-01 1987-01-10 Kobe Steel Ltd 不安定延性破壊伝播停止特性にすぐれた高強度高靭性ラインパイプ用鋼板の製造方法
JPH093597A (ja) * 1995-06-21 1997-01-07 Nippon Steel Corp 溶接熱影響部靱性の優れた低温用鋼材およびその製造方法
CA2231985C (en) * 1997-03-26 2004-05-25 Sumitomo Metal Industries, Ltd. Welded high-strength steel structures and methods of manufacturing the same
JP3522564B2 (ja) * 1998-04-17 2004-04-26 新日本製鐵株式会社 溶接熱影響部の靱性に優れた鋼板
JP4268317B2 (ja) * 2000-06-09 2009-05-27 新日本製鐵株式会社 溶接部の低温靱性に優れた超高強度鋼管及びその製造方法
JP4311740B2 (ja) * 2004-10-27 2009-08-12 株式会社神戸製鋼所 大入熱溶接継手靭性に優れた厚鋼板
JP4303703B2 (ja) * 2005-06-21 2009-07-29 新日本製鐵株式会社 溶接熱影響部の破壊靭性に優れた鋼及びその製造方法

Also Published As

Publication number Publication date
BRPI0607524B1 (pt) 2016-01-19
EP2060643A1 (en) 2009-05-20
CN101292055A (zh) 2008-10-22
CA2602076C (en) 2012-07-10
BRPI0607524A2 (pt) 2010-03-23
WO2008075443A1 (ja) 2008-06-26
KR100940617B1 (ko) 2010-02-05
KR20080067957A (ko) 2008-07-22
CA2602076A1 (en) 2008-06-20
CN100594250C (zh) 2010-03-17
EP2060643A4 (en) 2010-12-01

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