EP1778886A1 - Objekt mit einem stahlteil einer metallkonstruktion aus einem mittels hochleistungsdichtestrahl geschweissten bereich und mit hervorragender zähigkeit in einem schmelzbereich sowie verfahren zur herstellung eines derartigen objekts - Google Patents

Objekt mit einem stahlteil einer metallkonstruktion aus einem mittels hochleistungsdichtestrahl geschweissten bereich und mit hervorragender zähigkeit in einem schmelzbereich sowie verfahren zur herstellung eines derartigen objekts

Info

Publication number
EP1778886A1
EP1778886A1 EP05778661A EP05778661A EP1778886A1 EP 1778886 A1 EP1778886 A1 EP 1778886A1 EP 05778661 A EP05778661 A EP 05778661A EP 05778661 A EP05778661 A EP 05778661A EP 1778886 A1 EP1778886 A1 EP 1778886A1
Authority
EP
European Patent Office
Prior art keywords
exp
welding
δtb
steel
welded
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Withdrawn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
EP05778661A
Other languages
English (en)
French (fr)
Inventor
Dominique Kaplan
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.)
ArcelorMittal France SA
Original Assignee
Arcelor France SA
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 Arcelor France SA filed Critical Arcelor France SA
Publication of EP1778886A1 publication Critical patent/EP1778886A1/de
Withdrawn legal-status Critical Current

Links

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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K15/00—Electron-beam welding or cutting
    • B23K15/0046—Welding
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K26/00—Working by laser beam, e.g. welding, cutting or boring
    • B23K26/20—Bonding
    • B23K26/32—Bonding taking account of the properties of the material involved
    • 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
    • C22C38/02—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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K2103/00—Materials to be soldered, welded or cut
    • B23K2103/02—Iron or ferrous alloys
    • B23K2103/04—Steel or steel alloys
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K2103/00—Materials to be soldered, welded or cut
    • B23K2103/50—Inorganic material, e.g. metals, not provided for in B23K2103/02 – B23K2103/26
    • 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
    • C21D2211/002—Bainite
    • 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
    • C21D2211/008—Martensite

Definitions

  • the present invention relates to steel metallic constructions concerned by a high energy density beam, and more particularly
  • the assembly by high energy density beam, such as LASER or the electron beam, of hot-rolled steel sheets and plates has particularly developed in the last twenty years due
  • the present invention aims to provide such welded assemblies and a method for obtaining such assemblies from structural steel.
  • a first object of the invention consists of an object comprising at least one steel part, the composition of which comprises, the contents being expressed by weight, carbon with a content of between 0.005 and 0.27%, manganese. between 0.5 and 1.6%, silicon between 0.1 and 0.4%, chromium in content less than 2.5%, Mo in content less than 1%, possibly one or more elements chosen from nickel, copper, aluminum, niobium, vanadium, titanium, boron, zirconium, nitrogen, the rest being iron and impurities resulting from the production.
  • the steel part comprises at least one zone melted by high energy density beam with a microstructure consisting of 60 to 75% of self-returning martensite and, in addition, 40 to 25% of lower bainite, and preferably 60 to 70 % of self-returning martensite and, in addition, 40 to 30% of lower bainite.
  • the object is a steel tube comprising at least one section having a zone welded in the longitudinal or transverse direction.
  • the object consists of at least two hot-rolled or forged sheets of steel of identical or different composition, of identical or different thickness, welded together.
  • the high energy density beam is a beam
  • the high energy density beam is an electron beam.
  • the subject of the invention is also a method of manufacturing one of the preceding objects, comprising the steps consisting in:
  • an object comprising at least one steel part, the composition of which comprises the contents being expressed by weight, carbon in content of between 0.005 and 0.27%, manganese between 0.5 and 1.6%, silicon between 0.1 and 0.4%, chromium in content less than 2.5%, Mo in content less than 1%, optionally one or more elements chosen from nickel, copper, aluminum, niobium, vanadium, titanium, boron, zirconium, nitrogen, the rest being iron and impurities resulting from the production,
  • the welding power, the welding speed, the means of a possible pre or post-heating or cooling being chosen so that a molten zone is obtained with a microstructure consisting of 60 to 75% of martensite self-returned and, in addition, 40 to 25% of lower bainite, preferably 60 to 70% of self-returned martensite and, in addition, 40 to 30% of lower bainite.
  • the nitrogen content of the molten zone is less than or equal to 0.020%
  • the welding power, the welding speed, the means of a possible pre or post-heating or cooling are chosen so that the molten zone cools according to a parameter ⁇ / 5 8 0 ° 0 ° such that:
  • CE C + Mn / 6 + Si / 24 + Mo / 4 + Ni / 12 + Cu / 15 + (Cr (1-0,16-v / Cr) / 8) + f (B)
  • CE , C + Mn / 3,6 + Cu / 20 + Ni / 9 + Cr / 5 + Mo / 4,
  • C, Mn, Si, Mo, Ni, Cu, Cr, B and N respectively designating the carbon, manganese, silicon, molybdenum, nickel, copper, chromium, boron and nitrogen contents, expressed as a percentage by weight, of said molten zone.
  • the welding is carried out by a LASER beam in a homogeneous and autogenous manner, the nitrogen content of the steel is less than or equal to 0.020%, and the welding power, the welding speed, the means of a possible pre or post-heating or cooling, are chosen so that the molten zone cools according to a parameter At ⁇ such that:
  • CE C + Mn / 6 + Si / 24 + Mo / 4 + Ni / 12 + Cu / 15 + (Cr (1-0,16VCr) / 8) + f (B)
  • CE 1 C + Mn / 3.6 + Cu / 20 + Ni / 9 + Cr / 5 + Mo / 4,
  • f (B) (0.09-4.5N) if B> 0.0004%, C, Mn, Si, Mo, Ni, Cu, Cr, B, N respectively denoting the contents of carbon, manganese, silicon, molybdenum, nickel, copper, chromium, boron and nitrogen, expressed as a percentage by weight, of the welded steel .
  • the welding is carried out by electron beam in an autogenous and homogeneous manner, the nitrogen content of the steel is less than or equal to 0.022%, the welding power, the welding speed, the means of a possible pre or post-heating or cooling, are chosen so that the zone melted by the electron beam cools according to a parameter At ⁇ such that:
  • CE C + Mn / 6.67 + Si / 24 + Mo / 4 + Ni / 12 + Cu / 15 + (Cr (I-0, 16-VCr) / 8) + f (B)
  • CE ,, C + Mn / 4 + Cu / 20 + Ni / 9 + Cr / 5 + Mo / 4,
  • C, Mn, Si, Mo, Ni, Cu, Cr, B, N respectively designating the contents of carbon, manganese, silicon, molybdenum, nickel, copper, chromium, boron, and nitrogen, expressed as a percentage by weight, of the welded steel .
  • the steel part is welded with a steel part of identical or different composition, of identical or different thickness, whether or not part of said object, using a filler product metallic
  • FIG. 1 illustrates the comparison of the hardness of the Heat Affected Zone with that of the molten zone in LASER welding and in electron beam welding of steel structural steel.
  • - Figure 2 presents the comparison of the Charpy V transition temperature at the 28 Joule level (TK 2 Sj) of the Heat Affected Zone with that of the molten zone in LASER and electron beam welding of structural steels metallic.
  • - Figure 3 illustrates a typical change in the ductile-brittle transition temperature and the hardness in the Heat Affected Zone of a metallic structural steel, as a function of the cooling rate.
  • FIG. 6 shows the modification of the nitrogen content in the molten zone compared to that of the base metal during electron beam welding.
  • the welded part consists of two distinct zones:
  • the molten zone which corresponds to a zone which has passed through the liquid state during welding, ie that where the temperature has been higher than that of the liquidus of the welded material.
  • Zone Affected by Heat (or “ZAC”), which can include in the broad sense all the zones having undergone an allotropic transformation during welding. Subsequently, this term ZAC will be reserved here for the parts of the assembly remaining in the solid state brought to the highest temperatures during welding which are the seat of a greater magnification of the austenitic grain. These zones, very often the most critical from the point of view of toughness, correspond to maximum temperatures greater than 1200-1300 ° C.
  • Figure 3 presents a typical example of the evolution of the hardness and the ductile-brittle transition temperature of the ZAC of a metallic structural steel at 0.04% C, 1, 3% Mn in function of the cooling rate after welding.
  • This speed is here characterized by A / °° o , parameter which designates the time which elapses between the passage at the temperature of 800 0 C and the temperature of 500 0 C during cooling in welding.
  • There is a cooling speed range (located for this steel composition around ⁇ 500 ”1-2s), for which the toughness is optimal.
  • fresh martensite non-returned martensite
  • the microstructures corresponding to the optimum toughness consist partly of self-tempered martensite, the tempering being due to the welding cycle itself, and partly of lower bainite.
  • the self-returning structure is characterized by the presence of fine carbides precipitated in the martensite slats.
  • f500 Time elapsing between 800 and 500 0 C during the cooling of the welded area after welding
  • ⁇ t M Critical cooling time leading to 100% martensite
  • ⁇ t B Critical cooling time leading to 100% bainite
  • the critical cooling times are related to the chemical composition by the following expressions:
  • ⁇ t M exp (10 - 6 CE l - 4 - 8) .
  • CE C + Mn / 6 + Si / 24 + Mo / 4 + Ni / 12 + Cu / 15 + (Cr (1-0,16VCr) / 8) + f (B)
  • CE ,, C + Mn / 3,6 + Cu / 20 + NÎ / 9 + Cr / 5 + Mo / 4,
  • C, Mn, Si, Mo, Ni, Cu, Cr, B and N respectively denote the carbon, manganese, silicon, molybdenum, nickel, copper, chromium, boron and nitrogen contents, expressed in weight percent, of the steel.
  • the similarity of the ZAC and the molten zone in homogeneous and autogenous welding at high energy density indicates that the previous formulations valid for the ZAC are also applicable to the molten zone.
  • a martensite content of between 60 and 75%, preferably between 60 and 70%, combined with a supplement in lower bainite results in excellent toughness. This is obtained if the cooling parameter obeys the following expression:
  • the composition of the molten zone is practically identical to that of the base metal.
  • N and Mn in the molten zone are respectively equal to 0.9C and 0.9Mn.
  • CEi C + Mn / 6.67 + Si / 24 + Mo / 4 + N ⁇ / 12 + Cu / 15 + (Cr (IO 1 IeVO 7 ) / 8) + f (B)
  • CEn C + Mn / 4 + Cu / 20 + Ni / 9 + Cr / 5 + Mo / 4,
  • C, Mn, Si, Mo, Ni, Cu, Cr, B and N respectively denote the contents of carbon, manganese, silicon, molybdenum, nickel, copper, chromium, boron and nitrogen, expressed as a percentage by weight, of the welded steel .
  • the invention can also be transposed in the case where a steel part is welded with another steel part of different composition, and this taking into account the relative participation of each element to form the molten zone, c 'ie the coefficient of dilution.
  • c 'ie the coefficient of dilution the coefficient of dilution.
  • the same remark also applies in the case of welding with metallic filler, the composition and dilution coefficient of which must be taken into account, in order to assess the composition of the molten area.
  • the transition temperature determined from impact tensile tests on notched cylindrical specimens of 4mm in diameter, is of -120 ° C., which translates an excellent toughness and a high resistance to brittle fracture of the tubes manufactured under these conditions by LASER welding. Thanks to the invention, the production of welded structures with high energy density is therefore carried out economically, without the need for expensive addition elements.
  • the invention makes it possible to choose the assembly conditions so as to meet the security requirements with respect to the risk of sudden rupture.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Organic Chemistry (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Physics & Mathematics (AREA)
  • Optics & Photonics (AREA)
  • Plasma & Fusion (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Laser Beam Processing (AREA)
  • Heat Treatment Of Articles (AREA)
  • Joining Of Building Structures In Genera (AREA)
EP05778661A 2004-07-05 2005-06-21 Objekt mit einem stahlteil einer metallkonstruktion aus einem mittels hochleistungsdichtestrahl geschweissten bereich und mit hervorragender zähigkeit in einem schmelzbereich sowie verfahren zur herstellung eines derartigen objekts Withdrawn EP1778886A1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
FR0407512A FR2872442B1 (fr) 2004-07-05 2004-07-05 Assemblages soudes a haute densite d'energie d'aciers de construction metallique presentant une excellente tenacite dans la zone fondue, et methode de fabrication de ces assemblages soudes
PCT/FR2005/001543 WO2006013242A1 (fr) 2004-07-05 2005-06-21 Objet comprenant une partie en acier de construction metallique, cette partie comportant une zone soudee a l’aide d’un faisceau a haute densite d’energie et presentant une excellente tenacite dans la zone fondue ; metode de fabrication de cet objet

Publications (1)

Publication Number Publication Date
EP1778886A1 true EP1778886A1 (de) 2007-05-02

Family

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Family Applications (1)

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EP05778661A Withdrawn EP1778886A1 (de) 2004-07-05 2005-06-21 Objekt mit einem stahlteil einer metallkonstruktion aus einem mittels hochleistungsdichtestrahl geschweissten bereich und mit hervorragender zähigkeit in einem schmelzbereich sowie verfahren zur herstellung eines derartigen objekts

Country Status (7)

Country Link
US (1) US20080302450A1 (de)
EP (1) EP1778886A1 (de)
CN (1) CN1989268A (de)
BR (1) BRPI0512996A (de)
CA (1) CA2572869A1 (de)
FR (1) FR2872442B1 (de)
WO (1) WO2006013242A1 (de)

Families Citing this family (9)

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Publication number Priority date Publication date Assignee Title
JP5365216B2 (ja) * 2008-01-31 2013-12-11 Ｊｆｅスチール株式会社 高強度鋼板とその製造方法
JP5906147B2 (ja) * 2012-06-29 2016-04-20 株式会社神戸製鋼所 母材靭性およびｈａｚ靱性に優れた高張力鋼板
MX2016006485A (es) 2013-11-25 2016-08-05 Magna Int Inc Componente estructural que incluye zona de transicion templada.
ES2627220T3 (es) 2014-05-09 2017-07-27 Gestamp Hardtech Ab Métodos para la unión de dos formatos y los formatos y los productos obtenidos
CN104759625B (zh) * 2015-03-27 2017-01-04 桂林电子科技大学 一种使用激光3d打印技术制备铝合金结构件的材料及方法
CN105296852B (zh) * 2015-11-24 2017-03-29 西安三维应力工程技术有限公司 汽车传动轴用焊接钢管及其制造方法
US10252378B2 (en) * 2015-12-10 2019-04-09 Caterpillar Inc. Hybrid laser cladding composition and component therefrom
CN106319385A (zh) * 2016-09-30 2017-01-11 无锡市明盛强力风机有限公司 一种金属材料及其制备方法
WO2019171624A1 (ja) * 2018-03-09 2019-09-12 日新製鋼株式会社 鋼管および鋼管の製造方法

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AU4111193A (en) * 1992-05-27 1993-12-30 Alloy Rods Global, Inc. Welding electrodes for producing low carbon bainitic ferrite weld deposits
JPH1094890A (ja) * 1996-09-24 1998-04-14 Nippon Steel Corp 溶接部継手靭性に優れた鋼板のレーザー溶接方法
DZ2528A1 (fr) * 1997-06-20 2003-02-01 Exxon Production Research Co Conteneur pour le stockage de gaz natural liquéfiesous pression navire et procédé pour le transport de gaz natural liquéfié sous pression et système de traitement de gaz natural pour produire du gaz naturel liquéfié sous pression.
JP3519966B2 (ja) * 1999-01-07 2004-04-19 新日本製鐵株式会社 低温靱性に優れた超高強度ラインパイプおよびその製造法
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Also Published As

Publication number Publication date
US20080302450A1 (en) 2008-12-11
WO2006013242A1 (fr) 2006-02-09
FR2872442A1 (fr) 2006-01-06
CA2572869A1 (fr) 2006-02-09
BRPI0512996A (pt) 2008-04-22
FR2872442B1 (fr) 2006-09-15
WO2006013242A9 (fr) 2007-06-14
CN1989268A (zh) 2007-06-27

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