WO2007048497A1 - Procede de fabrication d’une tole chaude presentant une structure multiphase - Google Patents

Procede de fabrication d’une tole chaude presentant une structure multiphase Download PDF

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Publication number
WO2007048497A1
WO2007048497A1 PCT/EP2006/009755 EP2006009755W WO2007048497A1 WO 2007048497 A1 WO2007048497 A1 WO 2007048497A1 EP 2006009755 W EP2006009755 W EP 2006009755W WO 2007048497 A1 WO2007048497 A1 WO 2007048497A1
Authority
WO
WIPO (PCT)
Prior art keywords
cooling
hot strip
austenite
ferrite
strip
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.)
Ceased
Application number
PCT/EP2006/009755
Other languages
German (de)
English (en)
Inventor
Wolfgang Hennig
August Sprock
Joachim Ohlert
Christian Bilgen
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.)
SMS Siemag AG
Original Assignee
SMS Demag AG
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 SMS Demag AG filed Critical SMS Demag AG
Priority to US12/083,822 priority Critical patent/US20090214377A1/en
Priority to CN2006800397062A priority patent/CN101297049B/zh
Priority to JP2008536963A priority patent/JP5130221B2/ja
Priority to EP06806132A priority patent/EP1954842A1/fr
Priority to CA002625564A priority patent/CA2625564A1/fr
Priority to BRPI0617753-0A priority patent/BRPI0617753A2/pt
Priority to AU2006308245A priority patent/AU2006308245B2/en
Publication of WO2007048497A1 publication Critical patent/WO2007048497A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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Classifications

    • 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
    • C21D8/04—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 to produce plates or strips for drawing, e.g. for deep-drawing
    • C21D8/041—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 to produce plates or strips for drawing, e.g. for deep-drawing involving a particular fabrication or treatment of ingot or slab
    • C21D8/0415—Rapid solidification; Thin strip casting
    • 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
    • C21D8/04—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 to produce plates or strips for drawing, e.g. for deep-drawing
    • 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
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
    • C21D1/20—Isothermal quenching, e.g. bainitic hardening
    • 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
    • C21D8/021—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 involving particular fabrication steps or treatments of ingots or slabs
    • C21D8/0215—Rapid solidification; Thin strip casting
    • 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
    • C21D8/0247—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
    • 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
    • C21D8/04—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 to produce plates or strips for drawing, e.g. for deep-drawing
    • C21D8/0421—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 to produce plates or strips for drawing, e.g. for deep-drawing characterised by the working steps
    • C21D8/0426—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
    • C21D8/04—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 to produce plates or strips for drawing, e.g. for deep-drawing
    • C21D8/0447—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 to produce plates or strips for drawing, e.g. for deep-drawing characterised by the heat treatment
    • C21D8/0463—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 to produce plates or strips for drawing, e.g. for deep-drawing 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • 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
    • C21D2211/005—Ferrite

Definitions

  • the invention relates to a method for the production of hot strip with TRIP steel (transform-molded pjasticity) having a multi-phase structure with extremely good deformation properties from the hot-rolled state by controlled cooling after the last rolling stand.
  • the setting of the microstructure is complex with TRIP steels, because in addition to ferrite and bainite a third phase exists as retained austenite or after a subsequent deformation as martensite.
  • Today TRIP steels are usually produced in a two-stage annealing cycle. Starting material is hot or cold strip, in which by an annealing in the intercritical phase space, an approximately 50% ⁇ - 50% y - output structure is set. Due to the higher solubility of the austenite for carbon there is a higher carbon concentration. After the annealing treatment, rapid cooling takes place, past the ferrite and perlite areas into the bainite area, in which it is kept isothermal for some time.
  • the austenite partially converts to bainite and the remaining austenite is simultaneously further enriched in carbon.
  • the martensite start temperature M s is reduced to values below the ambient temperature and the retained austenite consequently also remains at ambient temperature.
  • the final structure consists of 40 - 70% ferrite, 15 - 40% bainite and 5 - 20% retained austenite.
  • TRIP steels The special effect of TRIP steels is the transformation of the metastable austenite to martensite * when an external plastic deformation occurs.
  • the transformation of austenite into martensite causes an increase in volume, which is not carried by austenite alone, but also by the surrounding microstructure constituents.
  • the ferritic matrix is plasticized, which in turn leads to higher solidification and overall leads to higher plastic strains.
  • the result for steels produced in this way is an extraordinary combination of high strength and high ductility, which makes them particularly suitable for use in the automotive industry.
  • EP 1 396 549 describes a process for producing a pearlite-free hot-rolled steel strip with TRIP properties in a continuous working process, in which a molten steel containing, in addition to iron and unavoidable impurities, 0.06-0.3% C ; 0.1-3.0% Si; 0.3-1.1% Mn (the sum of Si and Mn being 1.5- 3.5%) and 0.005-0.15% of at least one of the elements Ti or Nb as an essential component and optionally one or more several of the following elements max. 0.8% Cr; Max. 0.8% Cu; Max. Contains 1.0% Ni, is poured into thin slabs.
  • These thin slabs are annealed with a 850 to 1050 0 C amounting inlet temperature in an annealing furnace for an annealing time of 10 to 60 minutes at 1000 to 1200 0 C. After descaling, the thin slabs are then finish hot rolled in the range of 750 to 1000 0 C and then cooled to a reel temperature of 300 - to 530 0 C.
  • the controlled cooling is carried out in two stages with a cooling rate of the first stage of at least 150 K / s, preferably 300 K / s and a cooling pause of 4 to 8 seconds. Alternatively, it is proposed to carry out the controlled cooling continuously at a cooling rate of 10 to 70 K / s without stopping.
  • the cooling is controlled so that the hot strip in a first stage within 1 to 7 seconds to a temperature of about 80 0 C above and then by air cooling is cooled to reel temperature.
  • the presence of Ti and / or Nb is of importance, since these elements remain in solution until the start of hot rolling and improve their subsequent separation, inter alia, the grain fineness of the hot strip, an increase in retained austenite content and its stability.
  • the rolling strategy according to the invention is used to set a very fine Austenitkorns (d ⁇ 8 microns) in the last transformation, which acts accelerating in the following cooling section on the ferrite conversion.
  • the finish rolling of the strip therefore takes place at temperatures between 770 and 830 ° C. just above Ar 3 in the area of the metastable austenite.
  • the successful implementation of the cooling strategy requires compliance with certain limits of chemical composition in order to achieve the desired degree of conversion within the available short total cooling time.
  • the chemical analysis proposed for the production of TRIP steels therefore moves within the limits: 0.12 - 0.25% C, 0.05 - 1, 8% Si, 1, 0 - 2.0% Mn, balance Fe and usual accompanying elements.
  • the cooling strategy provides for two-stage cooling with either different cooling rates.
  • the start of the hold time at temperatures of 650 - 730 0 C is determined by the entry of the cooling curve in the ferrite region. In the following short cooling break then the desired conversion of austenite is at least 40% ferrite.
  • the second cooling stage is followed immediately by a cooling of the hot strip to a temperature between 320 to this hold time - 480 0 C. At this temperature, the conversion is made from austenite to at least 15% bainite.
  • the cooling strategy is determined by a well-defined predetermined cooling rate for both cooling stages.
  • a cooling rate of less than 30 K / s is not possible in the conventional cooling section of a cast roll mill because cooling time is greater than 150 K / s in such cooling sections of spaced-apart water cooling zones also can not be reached.
  • the hot strips of TRIP steel properties produced by the method of the invention for different strength levels with a yield ratio R p o, 2 / Rm in the range of 0.45 to 0.75 have the following property combinations of tensile strength R m and elongation at break A :
  • FIG. 2 shows a modified cooling section of the CSP system
  • FIG. 3 shows cooling curves for a dual-phase steel and a TRIP steel in a ZTU diagram.
  • the layout of a conventional CSP system 1 is shown schematically. It consists in the example shown in the conveying direction (in the drawing from left to right) from the main components, namely the casting machine with two strands 2, the strand guides 3, the equalizing ovens 4 with. a kiln ferry, a multi-stand rolling mill 6, the cooling section 10 and reels. 8
  • modified cooling section 10 of a CSP system 1 which is required for carrying out the cooling according to the invention and is already known for the production of dual-phase steel from EP 1 108 072 B1.
  • This behind the last finishing stand 6 'arranged modified cooling section 10 of the CSP system 1 has a plurality of spaced successively controllable water cooling zones 11 1 - 7 , 12 with Wassersprühköpfen 13 through which the upper band and the lower side of the strip hot strip 7 evenly with a certain amount of water is sprayed.
  • the positioning of the water cooling stages 11 1 - 7 , 12 within the cooling section 10, their number and their distance from each other and the number of Wassersprühköpfe 13 per water cooling stage 11 1 - 7 , 12 are chosen so that the desired cooling rate of the two cooling stages in advance variable can be adjusted to the water cooling 11 1 . 7 , 12 optimally adapted to the cooling conditions to be set. By controlling the sprayed amount of water can thus also during cooling, a necessary change in the cooling rate be made.
  • a further water cooling stage 12 is arranged, by means of which the second cooling stage is performed.
  • this water cooling stage 12 in contrast to the water cooling zones 111 -7 of the first cooling stage, there are a significantly larger number of water spray heads 13 in order to carry out forced intensive cooling in a shorter way.
  • the spatial distance between the last water cooling stage 11 7 of the first cooling stage and the water cooling stage 12 of the second cooling stage is chosen so large that sets the required hold time for the conversion of austenite according to the invention to at least 40% ferrite at the predetermined belt speed.
  • FIG. 3 is a ZTU diagram with the conversion lines for ferrite, perlite and bainite and with the temperature lines (20, 21, 22, 24) for AC 3 , Aci and M 8 .
  • horizontal displacement arrows 27 for the transformation lines and vertical displacement arrows 28 for the temperature lines it is indicated which influence existing or added alloying elements exert on the position of these transformation or temperature lines in the ZTU diagram.
  • the cooling curve 25 for the production of a dual-phase steel and the cooling curve 26 for the production according to the invention of a TRIP steel are shown by way of example in this ZTU diagram.
  • Cooling curve for a dual-phase steel 26 Cooling curve for a TRIP steel

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Metal Rolling (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

L'invention concerne un procédé de fabrication, dans des conditions de lamination à chaud, d'une tôle chaude en acier TRIP (transformation induced plasticity) présentant une structure multiphase ayant à la fois une grande résistance et des propriétés de mise en forme particulièrement bonnes, ledit procédé étant réalisé à partir d'une composition chimique prédéterminée du type d'acier utilisé comprenant de 0,12 à 0,25 % de C ; de 0,05 à 1,8 % de Si ; de 1,0 à 2,0 % de Mn ; le reste étant du Fe ainsi que les éléments d'accompagnement usuels, par une combinaison de laminages et de refroidissements, afin d'obtenir une structure contenant de 40 à 70 % de ferrite, de 15 à 45 % de bainite et de 5 à 20 % de résidu d'austénite, le laminage de finition de la tôle chaude (7) permettant d'obtenir un grain d'austénite très fin (d < 8 µm) lors de la dernière transformation (6') à une température comprise entre 770 et 830 °C légèrement supérieure à Ar3 dans le domaine de l'austénite métastable, et un refroidissement contrôlé en deux étapes (10, 11, 12) étant effectué après le dernier laminage (6') de la tôle chaude (7) à une température de tôle dans le domaine de formation de bainite entre 320 et 480 °C, avec un temps de maintien aux environ de 650 à 730 °C, le début dudit temps de maintien étant déterminé par l'entrée de la courbe de refroidissement dans le domaine de la ferrite et sa durée étant déterminée par un taux d'austénite d'au moins 40 % de la ferrite.
PCT/EP2006/009755 2005-10-25 2006-10-10 Procede de fabrication d’une tole chaude presentant une structure multiphase Ceased WO2007048497A1 (fr)

Priority Applications (7)

Application Number Priority Date Filing Date Title
US12/083,822 US20090214377A1 (en) 2005-10-25 2006-10-10 Method for Producing Hot Rolled Strip with a Multiphase Microstructure
CN2006800397062A CN101297049B (zh) 2005-10-25 2006-10-10 用于制造具有多相组织的热轧带材的方法
JP2008536963A JP5130221B2 (ja) 2005-10-25 2006-10-10 マルチフェイズ構造の熱間ストリップの製造方法
EP06806132A EP1954842A1 (fr) 2005-10-25 2006-10-10 Procede de fabrication d'une tole chaude presentant une structure multiphase
CA002625564A CA2625564A1 (fr) 2005-10-25 2006-10-10 Procede de fabrication d'une tole chaude presentant une structure multiphase
BRPI0617753-0A BRPI0617753A2 (pt) 2005-10-25 2006-10-10 processo para produção de tira de laminação a quente com estrutura multifásica
AU2006308245A AU2006308245B2 (en) 2005-10-25 2006-10-10 Method for producing hot strip with a multiphase structure

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE102005051052.3 2005-10-25
DE102005051052A DE102005051052A1 (de) 2005-10-25 2005-10-25 Verfahren zur Herstellung von Warmband mit Mehrphasengefüge

Publications (1)

Publication Number Publication Date
WO2007048497A1 true WO2007048497A1 (fr) 2007-05-03

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Application Number Title Priority Date Filing Date
PCT/EP2006/009755 Ceased WO2007048497A1 (fr) 2005-10-25 2006-10-10 Procede de fabrication d’une tole chaude presentant une structure multiphase

Country Status (14)

Country Link
US (1) US20090214377A1 (fr)
EP (1) EP1954842A1 (fr)
JP (1) JP5130221B2 (fr)
KR (1) KR20080063307A (fr)
CN (1) CN101297049B (fr)
AU (1) AU2006308245B2 (fr)
BR (1) BRPI0617753A2 (fr)
CA (1) CA2625564A1 (fr)
DE (1) DE102005051052A1 (fr)
RU (1) RU2398028C2 (fr)
TW (1) TW200724690A (fr)
UA (1) UA90436C2 (fr)
WO (1) WO2007048497A1 (fr)
ZA (1) ZA200802524B (fr)

Cited By (2)

* Cited by examiner, † Cited by third party
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WO2012064129A3 (fr) * 2010-11-10 2012-07-12 (주)포스코 Procédé pour fabriquer un acier à plasticité induite par transformation laminé à froid/laminé à chaud de haute résistance ayant une résistance à la traction d'une valeur de 590 mpa, une excellente usinabilité, et un faible écart de propriété mécanique
CN105063309A (zh) * 2015-07-31 2015-11-18 首钢总公司 一种提高低碳微合金钢强度的方法

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EP2180075B1 (fr) * 2007-08-01 2017-05-03 Kabushiki Kaisha Kobe Seiko Sho Tôle d'acier de résistance élevée présentant une excellente aptitude à la flexion et une excellente résistance à la fatigue
DE102010050647A1 (de) * 2009-11-21 2011-05-26 Sms Siemag Aktiengesellschaft Anlage und Verfahren zum Gießen und Walzen von Metall
CN102133579B (zh) * 2010-01-27 2013-05-01 中国钢铁股份有限公司 减少蚀坑产生的钢胚热轧制程
JP5547287B2 (ja) 2010-10-22 2014-07-09 新日鐵住金株式会社 ホットスタンプ成形体の製造方法及びホットスタンプ成形体
JP5224010B2 (ja) 2010-10-22 2013-07-03 新日鐵住金株式会社 縦壁部を有するホットスタンプ成形体の製造方法及び縦壁部を有するホットスタンプ成形体
US9896736B2 (en) 2010-10-22 2018-02-20 Nippon Steel & Sumitomo Metal Corporation Method for manufacturing hot stamped body having vertical wall and hot stamped body having vertical wall
BR112014000086A2 (pt) * 2011-07-06 2017-02-14 Nippon Steel & Sumitomo Metal Corp método para produção de folha de aço laminada a frio
CN103857808B (zh) * 2011-09-13 2016-11-23 塔塔钢铁艾默伊登有限责任公司 高强度热浸镀锌钢带材
CZ303949B6 (cs) * 2011-09-30 2013-07-10 Západoceská Univerzita V Plzni Zpusob dosazení TRIP struktury ocelí s vyuzitím deformacního tepla
JP6232045B2 (ja) * 2012-03-30 2017-11-15 フォエスタルピネ スタール ゲゼルシャフト ミット ベシュレンクテル ハフツングＶｏｅｓｔａｌｐｉｎｅ Ｓｔａｈｌ Ｇｍｂｈ 高強度冷間圧延鋼板およびそのような鋼板を作製する方法
CN102586562B (zh) * 2012-03-30 2013-08-21 河北钢铁集团有限公司 一种防震抗灾用热轧trip钢板的生产工艺
CZ304832B6 (cs) * 2013-04-13 2014-11-26 Západočeská Univerzita V Plzni Způsob tepelného zpracování polotovarů z TRIP oceli
CN103898404B (zh) * 2014-04-28 2015-12-09 莱芜钢铁集团有限公司 一种钒微合金化热轧相变诱导塑性钢及制备方法
CN104233092B (zh) * 2014-09-15 2016-12-07 首钢总公司 一种热轧trip钢及其制备方法
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RU2008120667A (ru) 2009-12-10
CA2625564A1 (fr) 2007-05-03
EP1954842A1 (fr) 2008-08-13
AU2006308245A2 (en) 2008-06-19
UA90436C2 (ru) 2010-04-26
CN101297049A (zh) 2008-10-29
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AU2006308245A1 (en) 2007-05-03
JP5130221B2 (ja) 2013-01-30
AU2006308245B2 (en) 2010-09-30
US20090214377A1 (en) 2009-08-27
DE102005051052A1 (de) 2007-04-26
CN101297049B (zh) 2012-01-11

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