US20090214377A1 - Method for Producing Hot Rolled Strip with a Multiphase Microstructure - Google Patents

Method for Producing Hot Rolled Strip with a Multiphase Microstructure Download PDF

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Publication number
US20090214377A1
US20090214377A1 US12/083,822 US8382206A US2009214377A1 US 20090214377 A1 US20090214377 A1 US 20090214377A1 US 8382206 A US8382206 A US 8382206A US 2009214377 A1 US2009214377 A1 US 2009214377A1
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Prior art keywords
cooling
hot
rolled strip
austenite
ferrite
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Abandoned
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US12/083,822
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English (en)
Inventor
Wolfgang Hennig
August Sprock
Joachim Ohlert
Christian Bilgen
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SMS Siemag AG
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Assigned to SMS DEMAG AKTIENGESELLSCHAFT reassignment SMS DEMAG AKTIENGESELLSCHAFT ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: OHLERT, JOACHIM, BILGEN, CHRISTIAN, SPROCK, AUGUST, HENNIG, WOLFGANG
Publication of US20090214377A1 publication Critical patent/US20090214377A1/en
Assigned to SMS SIEMAG AKTIENGESELLSCHAFT reassignment SMS SIEMAG AKTIENGESELLSCHAFT CHANGE OF NAME (SEE DOCUMENT FOR DETAILS). Assignors: SMS DEMAG AG
Abandoned legal-status Critical Current

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    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips 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
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/041—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips 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
    • 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 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
    • 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
    • C21D8/021—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular fabrication or treatment of ingot or slab
    • 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 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
    • 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
    • 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
    • C21D8/0247—Modifying the physical properties 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 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 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips 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 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • C21D8/0463—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips 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 concerns a method for producing hot-rolled strip that consists of TRIP (transformation-induced plasticity) steel with a multiphase microstructure and with both high strength values and outstanding deformation properties, where the TRIP steel strip is produced from the hot-rolled state by controlled cooling after the last rolling stand.
  • TRIP transformation-induced plasticity
  • TRIP steels are now usually produced in a two-stage heat cycle.
  • the starting material is hot-rolled or cold-rolled strip, in which an approximately 50% ⁇ -50% ⁇ initial microstructure is adjusted. Due to the higher solubility of carbon in austenite, austenite has a higher carbon concentration.
  • rapid cooling is carried out past the ferrite and pearlite range into the bainite range, in which isothermal conditions are maintained for some time.
  • the austenite is partially transformed to bainite, and at the same time the remainder of the austenite becomes further enriched with carbon.
  • the martensite start temperature M s is reduced to values below ambient temperature, and consequently the retained austenite also continues to exist at ambient temperature.
  • the final microstructure 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 retained austenite to martensite when external plastic deformation occurs.
  • the transformation of the austenite to martensite is accompanied by an increase in volume, which is supported not just by the austenite alone but rather by the surrounding microstructural components as well.
  • the ferritic matrix is plasticized, which in turn results in greater strain hardening and leads overall to higher plastic elongations.
  • Steels produced in this way have an extraordinary combination of high strength and high ductility, which makes them suitable especially for use in the automobile industry.
  • EP 1 396 549 A1 discloses a method for producing pearlite-free hot-rolled steel strip with TRIP properties in a continuously running operational process, in which a steel melt, which contains, in addition to iron and unavoidable impurities, 0.06-0.3% C; 0.1-3.0% Si; 0.3-1.1% Mn (with the total amount of Si and Mn being 1.5-3.5%); 0.005-0.15% of at least one of the elements Ti or Nb as an essential component; and optionally one or more of the following elements: max. 0.8% Cr; max. 0.8% Cu; and max. 1.0% Ni, is cast into thin slabs, which are annealed at 1,000-1,200° C.
  • the thin slabs are finish hot rolled in the range of 750-1,000° C. and then cooled to a coiling temperature of 300-530° C.
  • the controlled cooling is carried out in two stages at a cooling rate of the first stage of at least 150 K/s with a cooling interruption of 4-8 seconds.
  • the controlled cooling be carried out continuously at a cooling rate of 10-70 K/s without a holding interruption.
  • a third possibility is proposed, in which the cooling is controlled in such a way that the hot rolled strip is cooled in a first phase to a temperature of about 80° C.
  • the objective of the invention is to specify a method which allows simpler and more economical production of TRIP steels in existing plants and in which an annealing treatment and the addition of alloying elements that are otherwise not absolutely necessary can be eliminated.
  • the typical microstructure for a TRIP steel is adjusted immediately after the last rolling stand by a two-stage cooling operation in the cooling line.
  • the adjustment of the appropriate microstructure requires extensive process know-how as well as very exact maintenance of the necessary process parameters. Due to the narrow tolerance range for the production of TRIP steels on hot wide strip mills, since the introduction of thin-slab continuous casting and rolling technology, a plant configuration has been available which provides much better conditions for the direct production of TRIP steels than hot-rolled strip, compared to conventional hot-rolled strip mills.
  • TRIP steels with constant mechanical properties can be reproducibly produced in this way. Due to the short length of the conventional cooling lines used in this process in existing continuous casting and rolling mills, the production of hot-rolled strip with TRIP microstructure is possible only with a special rolling and cooling strategy.
  • the rolling strategy of the invention is used for adjusting a very fine austenite grain (d ⁇ 8 ⁇ m) during the last deformation, which has an accelerating effect on the ferrite transformation in the subsequent cooling line. Therefore, the finish rolling of the strip takes place at temperatures of 770-830° C., just above Ar 3 in the range of metastable austenite.
  • the cooling strategy involves two-stage cooling with the option of using different cooling rates in each stage.
  • the start of the holding time at temperatures of 650-730° C. is determined by the entry of the cooling curve into the ferrite range.
  • the desired transformation of the austenite to at least 40% ferrite then takes place during the following brief cooling interruption.
  • the holding time is then immediately followed by the second cooling stage, in which the hot-rolled strip is cooled to a temperature of 320-480° C.
  • the transformation of austenite to at least 15% bainite takes place at this temperature.
  • the cooling strategy is determined by an exactly defined, predetermined cooling rate for the two cooling stages.
  • a cooling rate less than 30 K/s is not possible due to the small amount of time that is available in the conventional cooling line of a continuous casting and rolling plant, and that cooling rates greater than 150 K/s likewise cannot be realized in cooling lines of this type, which consist of a succession of water cooling zones spaced a certain distance apart.
  • the hot-rolled strip produced with the method of the invention with TRIP steel properties for different strength levels with an elastic limit tensile strength ratio R p0.2 /R m in the range of 0.45-0.75 has the following combinations of tensile strength Rm and percentage elongation after fracture A:
  • FIG. 1 shows a CSP plant.
  • FIG. 2 shows a modified cooling line of the CSP plant.
  • FIG. 3 shows cooling curves for a dual-phase steel and a TRIP steel in a TTT diagram.
  • FIG. 1 shows the layout of a conventional CSP plant 1 schematically.
  • it comprises the following main components in the direction of conveyance (from left to right in the drawing): the casting installation with two strands 2 , the strand guides 3 , the soaking furnaces 4 with a furnace transverse conveyor 5 , a multiple-stand rolling mill 6 , the cooling line 10 , and coilers 8 .
  • FIG. 2 shows a modified cooling line 10 of a CSP plant 1 , which is necessary for carrying out cooling in accordance with the invention and is already known from EP 1 108 072 B1,which describes a method for producing dual-phase steel.
  • This modified cooling line 10 of the CSP plant 1 is installed downstream of the last finish rolling stand 6 ′.
  • the cooling line 10 has several successive water cooling zones 11 1-7 , 12 that are spaced a certain distance apart and can be automatically controlled.
  • the water cooling zones 11 1-7 , 12 are equipped with water spray heads 13 , which evenly spray the upper and lower surfaces of the hot-rolled strip 7 with a specific amount of water.
  • the positioning of the water cooling zones 11 1-7 , 12 within the cooling line 10 , their number, their spacing, and the number of water spray heads 13 per water cooling zone 11 1-7 , 12 are chosen in such a way that the desired cooling rate of the two cooling stages can be variably adjusted in advance in order to achieve optimum adaptation of the water cooling zones 11 1-7 , 12 to the cooling. conditions that are to be adjusted. Automatic control of the amount of water sprayed thus makes it possible, even during the cooling operation, to make any necessary change in the cooling rate.
  • An additional water cooling zone 12 is installed a greater distance from the last water cooling zone 117 of the first cooling stage than the distance between the individual zones of water cooling zones 11 1-7 .
  • the second cooling stage is carried out in this additional water cooling zone 12 .
  • this water cooling zone 12 in contrast to the water cooling zones 11 1-7 of the first cooling stage, there is a significantly larger number of water spray heads 13 in order to carry out forced intensive cooling over a shorter distance.
  • the distance between the last water cooling zone 11 7 of the first cooling stage and the water cooling zone 12 of the second cooling stage is chosen sufficiently large to obtain the holding time necessary to achieve transformation of the austenite to at least 40% ferrite, as prescribed by the invention, at the predetermined strip speed.
  • FIG. 3 shows a TTT diagram with the transformation lines for ferrite, pearlite, and bainite and with the temperature lines ( 20 , 21 , 22 , 24 ) for Ac 3 , Ac 1 , and M S .
  • Horizontal shift arrows 27 for the transformation lines and vertical shift arrows 28 for the temperature lines show the effect of existing or added alloying elements on the position of these transformation and temperature lines in the TTT diagram.
  • the cooling curve 25 for the production of a dual-phase steel and the cooling curve 26 for the production of a TRIP steel in accordance with the invention are plotted in this TTT diagram as examples.
  • the cooling curve 25 passes only into the ferrite range and ends below the martensite start temperature line 22 , which is well above room temperature 23 , so that, as desired, a dual microstructure that consists only of ferrite and martensite is obtained.
  • the cooling curve 26 for the production of a TRIP steel in accordance with the invention passes first through the ferrite range and then through the bainite range and ends above the martensite start temperature line 24 , which is now below room temperature 23 , so that transformation to martensite during cooling does not take place, and, in accordance with the invention, a microstructure is obtained that consists of ferrite, bainite, and some retained austenite.

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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)
US12/083,822 2005-10-25 2006-10-10 Method for Producing Hot Rolled Strip with a Multiphase Microstructure Abandoned US20090214377A1 (en)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
DE102005051052A DE102005051052A1 (de) 2005-10-25 2005-10-25 Verfahren zur Herstellung von Warmband mit Mehrphasengefüge
DE102005051052.3 2005-10-25
PCT/EP2006/009755 WO2007048497A1 (de) 2005-10-25 2006-10-10 Verfahren zur herstellung von warmband mit mehrphasengefüge

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US20090214377A1 true US20090214377A1 (en) 2009-08-27

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

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US20120006502A1 (en) * 2009-11-21 2012-01-12 Sms Siemag Aktiengesellschaft System and method for casting and rolling metal
US20130081741A1 (en) * 2011-09-30 2013-04-04 Bohuslav Masek Method of achieving trip microstructure in steels by means of deformation heat
CN103898404A (zh) * 2014-04-28 2014-07-02 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
WO2017109540A1 (en) * 2015-12-21 2017-06-29 Arcelormittal Method for producing a high strength steel sheet having improved ductility and formability, and obtained steel sheet
JP2020509192A (ja) * 2016-12-20 2020-03-26 ポスコＰｏｓｃｏ 溶接性及び延性に優れた高強度熱延鋼板及びその製造方法
US11236412B2 (en) 2016-08-05 2022-02-01 Nippon Steel Corporation Steel sheet and plated steel sheet
US11401571B2 (en) * 2015-02-20 2022-08-02 Nippon Steel Corporation Hot-rolled steel sheet
CN115976310A (zh) * 2022-10-31 2023-04-18 昆明理工大学 一种颗粒增强高强贝氏体中温锻造钢及其制备方法
CN115976396A (zh) * 2022-12-30 2023-04-18 包头钢铁（集团）有限责任公司 一种高强度耐腐蚀集装箱用热轧钢带q550nqr1及其生产方法
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CN104169444B (zh) * 2012-03-30 2017-03-29 奥钢联钢铁有限责任公司 高强度冷轧钢板和生产这种钢板的方法
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
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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CN105821190B (zh) * 2016-06-06 2019-01-08 日照宝华新材料有限公司 基于esp薄板坯连铸连轧流程生产中碳热轧trip钢的方法
CN108531811B (zh) * 2018-05-16 2020-05-01 东北大学 一种铸轧trip钢薄带的制备方法
RU2689348C1 (ru) * 2018-06-26 2019-05-27 Публичное акционерное общество "Северсталь" (ПАО "Северсталь") Способ производства горячекатаного проката повышенной прочности
AT525283B1 (de) * 2021-10-29 2023-02-15 Primetals Technologies Austria GmbH Verfahren zur Herstellung eines Dualphasenstahlbands in einer Gieß-Walz-Verbundanlage, ein mit dem Verfahren hergestelltes Dualphasenstahlband und eine Gieß-Walz-Verbundanlage
CN114645187A (zh) * 2022-01-29 2022-06-21 安阳钢铁股份有限公司 一种非调质950MPa级高强捆带钢及其生产方法

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US20130081741A1 (en) * 2011-09-30 2013-04-04 Bohuslav Masek Method of achieving trip microstructure in steels by means of deformation heat
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CN103898404A (zh) * 2014-04-28 2014-07-02 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
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US12054799B2 (en) 2015-12-21 2024-08-06 Arcelormittal Method for producing a high strength steel sheet having improved ductility and formability, and obtained steel sheet
WO2017109540A1 (en) * 2015-12-21 2017-06-29 Arcelormittal Method for producing a high strength steel sheet having improved ductility and formability, and obtained steel sheet
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US12084738B2 (en) 2015-12-21 2024-09-10 Arcelormittal Method for producing a steel sheet having improved strength, ductility and formability
EP3656880A1 (en) * 2015-12-21 2020-05-27 ArcelorMittal Method for producing a high strength steel sheet having improved ductility and formability, and obtained steel sheet
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CN115976396A (zh) * 2022-12-30 2023-04-18 包头钢铁（集团）有限责任公司 一种高强度耐腐蚀集装箱用热轧钢带q550nqr1及其生产方法

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KR20080063307A (ko) 2008-07-03
AU2006308245A2 (en) 2008-06-19
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ZA200802524B (en) 2009-06-24
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RU2008120667A (ru) 2009-12-10
BRPI0617753A2 (pt) 2011-08-02

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