EP1099769B1 - Verfahren zur Herstellung von warmgewalztem, hochfestem Stahlblech zur Umformung und insbesondere zum Tiefziehen - Google Patents

Verfahren zur Herstellung von warmgewalztem, hochfestem Stahlblech zur Umformung und insbesondere zum Tiefziehen Download PDF

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Publication number
EP1099769B1
EP1099769B1 EP00402987A EP00402987A EP1099769B1 EP 1099769 B1 EP1099769 B1 EP 1099769B1 EP 00402987 A EP00402987 A EP 00402987A EP 00402987 A EP00402987 A EP 00402987A EP 1099769 B1 EP1099769 B1 EP 1099769B1
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EP
European Patent Office
Prior art keywords
temperature
cooling
steel sheet
per
cooling step
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Revoked
Application number
EP00402987A
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English (en)
French (fr)
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EP1099769A1 (de
Inventor
Christophe Issartel
Christian Marteau
Christian Giraud
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ArcelorMittal France SA
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USINOR SA
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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
    • 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
    • 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
    • C22C38/02—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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese

Definitions

  • the invention relates to a method for producing a strip of sheet metal laminated to hot with very high resistance, usable for shaping and in particular for stamping.
  • a metallurgical solution to improve the strength compromise mechanical and elongation consists of the use of TRIP steels of ferrite-bainite structure- residual austenite.
  • the resistance compromise mechanical and elongation is clearly improved by the presence, in the microstructure, residual austenite.
  • the amount of austenite must be residual is greater than 5%.
  • a first possibility of obtaining TRIP steels is the use of steels C-Mn-Si type composition> 1%. These compositions have the disadvantage generate the formation of fayalite due to the presence of silicon.
  • compositional steels of the C-Mn-Al type Another possibility is the use of compositional steels of the C-Mn-Al type. This composition has an insufficient residual austenite.
  • a winding temperature below 350 ° C causes the appearance of martensite, which degrades in particular the formability of steels.
  • a temperature of too high winding leads to a purely ferito-bainitic structure without residual austenite therefore without improvement in formability. Indeed, the presence residual austenite must be greater than 5% to obtain an effect on the formability of the steels produced. Below this value, its influence is practically zero.
  • the winding temperatures in the area specified above are particularly difficult to obtain. Indeed, the temperature range winding between 350 ° C and 400 ° C corresponds to a zone of exchange instability between the steel strip and the cooling water, due to the rupture of the film of water vapor forming a screen between the hot metal and the cooling water. This phenomenon leads to a sudden increase in the exchange coefficient thermal in the area concerned which results, on the rolled steel strip, a heterogeneity of microstructure detrimental to the regularity of the properties mechanics of the finished product.
  • the obligation to use winding temperatures bass associated with the allied character of TRIP compositions causes difficulties of achievement. It is therefore sought to increase the temperature of winding to take advantage of higher ductility at high temperature.
  • the object of the invention is to develop a method for producing a very high strength TRIP type steel strip with good properties formatting.
  • Figure 1 shows a diagram of the cooling of the sheet metal strip hot rolled according to the invention.
  • Figure 2 shows the variation of the austenite content depending on the winding temperature for examples of steels according to the invention in comparison with reference steels TRIP C-Mn-Si and TRIP 0% Cr.
  • a first short cooling for example with air, is carried out in a time less than 10 seconds to obtain fine grains and to avoid the appearance of the perlite phase during cooling.
  • the steel is then subjected to a second controlled cooling whose speed is between 20 ° C / second and 150 ° C / second, depending on the thickness of the steel strip laminated treated.
  • the cooling rate controlled according to the invention, ensures significant germination of the ferritic phase.
  • the temperature at the end of second cooling is within a temperature range varying from 700 ° C and 750 ° C, that is to say below the point Ar3 of the formation of austenite in ferrite.
  • the sheet is then maintained on a temperature level where it undergoes a slow cooling, for example in air, with a cooling rate between 3 ° C / second and 20 ° C / second to reach an end temperature between 700 ° C and 640 ° C. Maintaining the steel strip on this bearing ensures the formation of a ferrite rate between 40% and 70%. It allows enrich the residual austenite with carbon, not transformed into ferrite, delaying its formation during cooling.
  • Hot rolled steel sheet, after temperature maintenance on the bearing is subjected to a third also controlled cooling, the speed of which is between 20 ° C / second and 150 ° C / second, related to the thickness of the strip treated sheet metal and this up to a temperature between 350 ° C and 525 ° C so to complete the enrichment of the residual austenite during the transformation which starts at a temperature of around 640 ° C.
  • the cooling rates Vref1 and Vref2 are included between 20 ° C / s and 50 ° C / S for sheet thicknesses between 4.5 mm and 6 mm and between 50 ° C / S and 150 ° C / s for thicknesses between 1.4 mm and 4.5 mm.
  • the final structure of hot rolled steel is composed of ferrite, bainite and residual austenite at a content higher than 5%, which allows to reach a mechanical resistance greater than 700 MPa, with elongation values distributed greater than 10% and an elongation at break greater than 25%.
  • the carbon stabilizes the austenite.
  • Manganese lowers the points of transformation Ar3, Bs and Ms respectively corresponding to the temperature of start of ferritic transformation, at the start of transformation temperature bainitic and the temperature at the start of the martensitic transformation.
  • Aluminum and silicon prevents the diffusion of carbon and ensures the stabilization of austenite by their effect on carbon. Silicon and aluminum have the same effect complementing each other. However, it is preferable to keep the silicon at low contents to avoid the formation of fayalite generating surface defects that appear after pickling.
  • the presence of phosphorus and chromium, alphagenic elements promotes the formation of the ferritic phase at during the hold on the temperature level. The proportion of ferrite formed is important and the carbon enrichment of the residual austenite allows the stabilization of this phase in a large winding temperature range.
  • Titanium, niobium and vanadium elements introduced into the composition so optional are micro alloy elements which can be added in the composition of the steel to obtain precipitation hardening and to refine the grain size of the ferrite. This provides more mechanical strength high by slightly reducing the distributed elongation.
  • composition of the steel according to the invention makes it possible to obtain a microstructure residual austenite bainite ferrite type, hot rolling ensuring on the one hand, good recrystallization of the austenite grains at the outlet of the rolling mill stands and on the other hand, an equiaxed texture.
  • the average residual austenite is 7%. Winding at 500 ° C. Rp02 MPa rm MPa Ag (%) Re / Rm not (4-8%) 458 779 14.4 0.59 0.21 Note: The microstructure is of the bainite ferrite type where the bainite is predominant in the form of large areas. Austenite is mainly in the form of blocks between the ferrite grains. The average residual austenite is 9.4%. Winding at 550 ° C. Rp02 MPa rm MPa Ag (%) Re / Rm not (4-8%) 569 758 9.5 0.75 0.15 Note: The microstructure has very little residual austenite, the average residual austenite is 0.2%. Winding at 600 ° C. Rp02 MPa rm MPa Ag (%) Re / Rm not (4-8%) 487 655 12.8 0.74 0.22 Note: the microstructure is of the ferrite bainite type and does not have any residual austenite.
  • steel with a ferrite-bainite-austenite microstructure residual with the following mechanical characteristics: Rm> 700 MPa, Re / Rm ratio ⁇ 0.7, Ag> 10% and A%> 25% can only be achieved for winding temperatures between 400 ° C and 500 ° C thanks to a quantity residual austenite greater than 5%.
  • the quantity of residual austenite is zero or almost zero and the mechanical properties are not conform with an elongation Ag% or with a limit at rupture Rm acceptable, the Re / Rm ratio being moreover too high.
  • Figure 2 shows the residual austenite rate as a function of the winding temperature for different reference TRIP steel compositions and according to the invention. It makes it possible to show that the method according to the invention has compared, for example, to steel A taken as a reference, TRIP C-Mn-Si a quantity higher austenite for a wider winding temperature range and higher in temperature.
  • Figure 2 shows, for comparison with steel A on steel 1 of the example, and two steels 2 and 3 according to the invention and comprising 0% Cr and 2% Cr respectively.
  • we can obtain the rate of austenite desired in a wide range of winding temperature, which ensures regularity of the mechanical characteristics of the sheet produced, regularity without which the use of sheet metal for a stamped part would be impossible.
  • the possibility according to the process of winding at higher temperature allows an industrial realization of the sheet without strengthening the capacities of industrial tool.
  • the proposed invention allows the production of a rolled steel strip thickness between 1.4 mm and 6 mm which has both a high mechanical resistance greater than 700 MPa and setting properties important shape thanks to a Re / Rm ratio of less than 0.7, to an elongation distributed greater than 10% and an elongation at break greater than 25%.
  • the method makes it possible to obtain a strip of sheet steel hot rolled with a residual austenite bainite austenite structure at more 5% by performing in the process an extended winding in an interval of temperature between 350 ° C and 525 ° C. It is thus possible to leave the domain instability of the winding temperature below 400 ° C. This is possible in particular by the use in the composition of the base steel of a content determined in chromium and phosphorus.
  • the sheet metal strip according to the invention can be introduced in use for stamped, bent or profiled parts in the construction sector mechanical and automotive. Its use gives the possibility of reducing thicknesses parts ensuring their lightening and or an improvement in their performance tired.
  • the parts that can be produced include absorbers, reinforcement, structural parts, wheels requiring good resistance to fatigue and also good stampability.

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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 Sheet Steel (AREA)
  • Laminated Bodies (AREA)
  • Coating With Molten Metal (AREA)

Claims (7)

  1. Verfahren zur Herstellung eines warmgewalzten Stahlbandes mit sehr hoher Festigkeit und einer Ferrit-Bainit-Restaustenitstruktur, das für die Umformung und insbesondere zum Tiefziehen verwendbar ist, dadurch gekennzeichnet, dass der Stahl mit folgender massebezogener Zusammensetzung:
    0,12% ≤ Kohlenstoff ≤ 0,25%,
    1% ≤ Mangan ≤ 2%,
    0,03% ≤ Aluminium ≤ 2,5%,
    0,03% ≤ Silicium ≤ 2%,
    0,04% ≤ Chrom ≤ 2%,
    0,02% ≤ Phosphor ≤ 0,09%,
    Schwefel ≤ 0,01%, und fakultativ
    Titan ≤ 0,15%,
    Niob ≤ 0,15%,
    Vanadium ≤ 0,15%, wobei der Rest aus Eisen und
    Restverunreinigungen besteht,
    folgendermaßen behandelt wird:
    Walzen bei einer Temperatur unter 880°C,
    erstes, kurzes Abkühlen, das in einem Zeitraum unter 10 Sekunden erfolgt,
    zweites Abkühlen mit einer Abkühlgeschwindigkeit V ref1, die in Abhängigkeit von der Dicke des gewalzten Stahlbandes im Bereich von 20 bis 150°C/Sekunde liegt, wobei die Endtemperatur der zweiten Abkühlung unter dem Punkt Ar3 der Umwandlung von Austenit in Ferrit liegt und wobei die Endtemperatur der zweiten Abkühlung im Bereich von 700 bis 750°C liegt,
    Halten auf einer Temperaturstufe, das mit einem langsamen Abkühlen verbunden ist, wobei die Abkühlgeschwindigkeit im Bereich von 3 bis 20°C/Sekunde liegt, bis zu einer Endtemperatur der Stufe, die im Bereich von 700 bis 640°C liegt,
    drittes, ebenfalls geregeltes Abkühlen, dessen Geschwindigkeit in Abhängigkeit von der Dicke des gewalzten Stahlbandes im Bereich von 20 bis 150°C/Sekunde liegt, wobei die Endtemperatur der dritten Abkühlung im Bereich von 350 bis 550°C liegt.
  2. Verfahren nach Anspruch 1, dadurch gekennzeichnet, dass die massebezogene Zusammensetzung weniger als 0,5% Silicium enthält.
  3. Verfahren nach Anspruch 1, dadurch gekennzeichnet, dass die Abkühlvorgänge unter Luft erfolgen.
  4. Verfahren nach Anspruch 1, dadurch gekennzeichnet, dass der Stahl warmgewalzt wird, um ein warmgewalztes Stahlband zu erhalten, dessen Dicke im Bereich von 1,4 bis 6 mm liegt.
  5. Warmgewalztes Stahlblech, das mit einer Ferrit-Bainit-Restaustenitstruktur gemäß dem Verfahren nach einem der Ansprüche 1 bis 4 hergestellt wird, dadurch gekennzeichnet, dass es in seiner massebezogenen Zusammensetzung enthält:
    0,12% ≤ Kohlenstoff ≤ 0,25%,
    1% ≤ Mangan ≤ 2%,
    0,03% ≤ Aluminium ≤ 2,5%,
    0,03% ≤ Silicium ≤ 2%,
    0,04% ≤ Chrom ≤ 2%,
    0,02% ≤ Phosphor ≤ 0,09%,
    Schwefel ≤ 0,01%, und fakultativ
    Titan ≤ 0,15%,
    Niob ≤ 0,15%,
    Vanadium ≤ 0,15%, wobei der Rest aus Eisen und
    Restverunreinigungen besteht.
  6. Blech nach Anspruch 5, dadurch gekennzeichnet, dass es in seiner massebezogenen Zusammensetzung weniger als 0,5% Silicium enthält.
  7. Blech nach Anspruch 5, dadurch gekennzeichnet, dass es eine Dicke im Bereich von 1,4 bis 6 mm aufweist.
EP00402987A 1999-11-12 2000-10-27 Verfahren zur Herstellung von warmgewalztem, hochfestem Stahlblech zur Umformung und insbesondere zum Tiefziehen Revoked EP1099769B1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
FR9914187A FR2801061B1 (fr) 1999-11-12 1999-11-12 Procede de realisation d'une bande de tole laminere a chaud a tres haute resistance, utilisable pour la mise en forme et notamment pour l'emboutissage
FR9914187 1999-11-12

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EP1099769A1 EP1099769A1 (de) 2001-05-16
EP1099769B1 true EP1099769B1 (de) 2004-03-17

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US (2) US6475308B1 (de)
EP (1) EP1099769B1 (de)
AT (1) ATE262046T1 (de)
BR (1) BR0005331A (de)
CA (1) CA2325892C (de)
DE (1) DE60009002T2 (de)
ES (1) ES2216840T3 (de)
FR (1) FR2801061B1 (de)
PT (1) PT1099769E (de)

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CN101263239B (zh) * 2005-08-04 2012-06-27 安赛乐米塔尔法国公司 生产具有优异延展性的高强度钢板的方法和由此生产的板材

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CA2387322C (en) * 2001-06-06 2008-09-30 Kawasaki Steel Corporation High-ductility steel sheet excellent in press formability and strain age hardenability, and method for manufacturing the same
JP3828466B2 (ja) * 2002-07-29 2006-10-04 株式会社神戸製鋼所 曲げ特性に優れた鋼板
DE102005051052A1 (de) * 2005-10-25 2007-04-26 Sms Demag Ag Verfahren zur Herstellung von Warmband mit Mehrphasengefüge
CN101191174B (zh) * 2006-11-20 2010-05-12 宝山钢铁股份有限公司 抗拉强度750MPa级热轧相变诱发塑性钢及制造方法
KR101957078B1 (ko) * 2015-02-20 2019-03-11 신닛테츠스미킨 카부시키카이샤 열연 강판
CN105925887B (zh) * 2016-06-21 2018-01-30 宝山钢铁股份有限公司 一种980MPa级热轧铁素体贝氏体双相钢及其制造方法
WO2018026014A1 (ja) 2016-08-05 2018-02-08 新日鐵住金株式会社 鋼板及びめっき鋼板
CN112760554A (zh) * 2019-10-21 2021-05-07 宝山钢铁股份有限公司 一种延展性优异的高强度钢及其制造方法
CN114196803B (zh) * 2021-11-16 2024-04-19 北京钢研高纳科技股份有限公司 一种紧固件用gh2132合金不对称截面异型丝及其制备方法

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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN101263239B (zh) * 2005-08-04 2012-06-27 安赛乐米塔尔法国公司 生产具有优异延展性的高强度钢板的方法和由此生产的板材

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US20030084973A1 (en) 2003-05-08
US6475308B1 (en) 2002-11-05
PT1099769E (pt) 2004-06-30
FR2801061B1 (fr) 2001-12-14
BR0005331A (pt) 2001-07-03
US6797078B2 (en) 2004-09-28
CA2325892C (fr) 2009-09-22
DE60009002D1 (de) 2004-04-22
DE60009002T2 (de) 2005-03-03
ES2216840T3 (es) 2004-11-01
FR2801061A1 (fr) 2001-05-18
ATE262046T1 (de) 2004-04-15
EP1099769A1 (de) 2001-05-16
CA2325892A1 (fr) 2001-05-12

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