EP1558769B1 - Verfahren zur herstellung von wärmehärtbaren stahlblechen durch glühung, stahlbleche und davon hergestellte teile - Google Patents

Verfahren zur herstellung von wärmehärtbaren stahlblechen durch glühung, stahlbleche und davon hergestellte teile Download PDF

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Publication number
EP1558769B1
EP1558769B1 EP03775481A EP03775481A EP1558769B1 EP 1558769 B1 EP1558769 B1 EP 1558769B1 EP 03775481 A EP03775481 A EP 03775481A EP 03775481 A EP03775481 A EP 03775481A EP 1558769 B1 EP1558769 B1 EP 1558769B1
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Prior art keywords
steel
weight
less
process according
temperature
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EP03775481A
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English (en)
French (fr)
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EP1558769A1 (de
Inventor
Joël MARSAL
Fernande Kirch
Dominique Mescolini
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ArcelorMittal France SA
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ArcelorMittal France SA
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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 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
    • C21D8/0221—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
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold 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
    • C21D8/0273—Final recrystallisation annealing
    • 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
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • 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
    • 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

Definitions

  • the present invention relates to a method for manufacturing baking hardening steel sheet, said "bake hardening", and the sheets and steel parts obtained by the implementation of this method.
  • These sheets and these pieces of steel may include an anticorrosion coating, such as that obtained by hot dip galvanizing or electrogalvanizing.
  • the steel sheets are more particularly intended for the manufacture of automotive appearance parts, such as hoods for example, while the parts of greater thickness than the sheets, are more particularly intended for producing pieces of steel. structure for automobile, too.
  • the appearance parts for the automobile must be made of a material easy to implement by stamping, having at the end of this implementation a good resistance to indentation, and the lightest possible to to reduce the consumption of the vehicle.
  • bake hardening also called steels BH
  • steels BH have the particularity to have a low yield strength before shaping, which makes them easily embossissables.
  • bake hardening also called steels BH
  • the parts or the plates of steels with BH have a limit of elasticity which has increased significantly, giving them good resistance to indentation.
  • this hardening property during the baking of the coating is in particular used to reduce the thickness, and therefore the weight, of these parts.
  • Bake-hardenable steels are known whose composition comprises manganese and silicon and a substantial amount of phosphorus, at around 0.1% by weight. These steels have good mechanical properties and a gain in yield strength after baking (BH) of the order of 45 MPa, but have a significant natural aging.
  • BH yield strength after baking
  • the present invention therefore aims to provide baking hardenable steels having good mechanical characteristics, a gain in yield strength after baking (BH) of at least 60 MPa and which are less sensitive to natural aging than the steels of the prior art.
  • BH gain in yield strength after baking
  • the first cooling comprises a first slow portion carried out at a speed of less than 10 ° C / s, then a fast second portion carried out at a rate of between 20 and 50 ° C / s.
  • the carbon content of the composition according to the invention is between 0.03 and 0.06% by weight, since this element substantially lowers the ductility. It is however necessary to have a minimum of 0.03% by weight to avoid any problem of aging.
  • the manganese content of the composition according to the invention must be between 0.50 and 1.10% by weight. Manganese improves the yield strength of steel while greatly reducing its ductility. Below 0.50% by weight, there are problems of aging, while beyond 1.10% by weight, it is too much to ductility.
  • the silicon content of the composition according to the invention must be between 0.08 and 0.20% by weight. It greatly improves the yield strength of steel while reducing its ductility slightly, but increases significantly its aging tendency. If its content is less than 0.08% by weight, the steel does not have good mechanical characteristics, whereas if it exceeds 0.20% by weight, it faces problems of surface appearance on which appear tigers.
  • the ratio of the manganese content with respect to the silicon content is between 4 and 15 in order to avoid any problem of solder brittleness. Indeed, if one places oneself outside these values, one observes the formation of embrittling oxides during this welding operation.
  • boron The main function of boron is to fix nitrogen by early precipitation of boron nitrides. It must therefore be present in sufficient quantity to prevent a large amount of nitrogen remains free, without however exceeding the stoichiometric amount because the free residual amount could cause metallurgical problems as well as a coloration of the coil banks. As an indication, it should be mentioned that the strict stoichiometry is reached for a B / N ratio of 0.77.
  • the aluminum content of the composition according to the invention is between 0.015 and 0.070% by weight, without it being of critical importance.
  • Aluminum is present in the grade according to the invention because of the casting process in which this element is added to deoxidize the steel. However, it is important not to exceed 0.070% by weight because then there would be problems of inclusions of aluminum oxides, harmful to the mechanical properties of steel.
  • Phosphorus is limited in the steel according to the invention to a content of less than 0.035% by weight, preferably less than 0.015% by weight. It makes it possible to increase the yield strength of the grade, but it also increases its aging tendency in heat treatments, which explains its limitation. It is also bad for ductility.
  • the titanium content of the composition must be less than 0.005% by weight, that of sulfur must be less than 0.015% by weight, that of nickel must be less than 0.040% by weight, that of copper must be less than 0.040% by weight. weight and that in molybdenum must be less than 0.010% by weight.
  • These different elements actually constitute the residual elements from the elaboration of the nuance that we meet most often. Their contents are limited because they are likely to form inclusions which diminish the mechanical characteristics of the shade.
  • these residual elements may also be niobium, which is not added to the composition, but which may be present in the form of traces, that is to say at a content of less than 0.004%, preferably less than 0.001%, and particularly preferably 0.
  • a second object of the invention which is defined in claim 8 is constituted by a baking curable sheet obtainable by the method according to the invention and which has a yield strength of between 260 and 360 MPa, a resistance to the tension between 320 and 460 MPa, a value of BH2 greater than 60 MPa and a plateau of elastic limit less than or equal to 0.2%.
  • the rest of the composition of the castings 1 to 5 is of course made of iron and possibly impurities resulting from the preparation.
  • a specimen is then subjected to a uniaxial tension of 2% and then a heat treatment of 170 ° C. for 20 minutes.
  • Slabs are made from castings 1 to 4 and then hot-rolled at a temperature above Ar 3. For these flows, the end of rolling temperature is between 854 and 880 ° C. The sheets thus obtained are reeled at a winding temperature between 580 and 620 ° C. for these pours, then they are cold rolled with a reduction rate which varies from 70 to 76%.
  • Specimens are then cut into these sheets and their yield strengths Re0 are measured. These specimens are then subjected to a 2% uniaxial tension and their yield strengths Re2% and their other mechanical characteristics are measured. Then, they are subjected to a conventional heat treatment at 170 ° C for 20 minutes and measured their new yield strengths ReTT. Their BH 2 are then calculated.
  • the castings 1 and 3 according to the invention have good mechanical characteristics, a good value of BH2 and have no or little yield point stop.
  • New specimens are then cut from the continuously annealed sheets and subjected to heat treatment at 75 ° C for 10 hours. This heat treatment is equivalent to a natural aging of 6 months at room temperature.
  • the following results are obtained: Specimen Re (MPa) rm (MPa) not P% AT% Casting 1 (fresh state) 296 384 0.208 0 36.6 Casting 1 (aged condition) 290 394 0,165 0.1 31.1 Casting 2 (fresh state) 305 422 0.189 0 33.1 Casting 2 (aged condition) 299 431 0,160 0 31.0 Casting 3 (fresh state) 284 379 0.194 0.2 35.3 Casting 3 (aged condition) 286 393 0.157 0.2 30.4
  • Slabs were made from castings 1 to 5 and then hot-rolled, the end-of-rolling temperature being 850/880 ° C.
  • the sheets thus obtained are reeled at a winding temperature of 580/620 ° C., then they are cold rolled with a reduction rate of 70/76% for these flows.
  • Specimens are then cut into these sheets and their yield strengths Re0 are measured. These specimens are then subjected to a 2% uniaxial tension and their yield strengths Re2% and their other mechanical characteristics are measured. Then, they are subjected to a conventional heat treatment at 170 ° C for 20 minutes and measured their new yield strengths ReTT. Their BH 2 are then calculated.
  • the castings 1 to 3 according to the invention have good mechanical characteristics, a very good value of BH 2 and show no or little yield strength stop, unlike casting which has 1.2% of bearing.
  • the castings 1 to 3 according to the invention do not exhibit a Z-type barrier (less than or equal to 0.2%), unlike the casting 5 which has a level of 1.8%.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical 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)
  • Heat Treatment Of Steel (AREA)
  • Metal Rolling (AREA)
  • Meat, Egg Or Seafood Products (AREA)

Claims (8)

  1. Verfahren zur Herstellung von durch Glühen wärmehärtbaren (bake-hardening) Stahlblechen, umfassend:
    - Verhütten eines Stahls, dessen Zusammensetzung Folgendes, ausgedrückt in Gewichtsprozent, umfasst:
    0,03 ≤ C ≤ 0,06
    0,50 ≤ Mn ≤ 1,10
    0,08 ≤ Si ≤ 0,20
    0,015 ≤ Al ≤ 0,070
    N ≤ 0,007
    Ni ≤ 0,040
    Cu ≤ 0,040
    P ≤ 0,035
    S ≤ 0,015
    Mo ≤ 0,010
    Ti ≤ 0,005
    wobei es sich versteht, dass sie auch Bor in einer solchen Menge umfasst, dass gilt: 0 , 64 ≤ B N ≤ 1 , 60
    Figure imgb0007
    wobei der Rest der Zusammensetzung aus Eisen und Verunreinigungen besteht, die aus der Verhüttung resultieren,
    - Gießen einer Bramme aus diesem Stahl, dann Warmwalzen dieser Bramme, um ein Blech zu erhalten, wobei die Walzendtemperatur höher ist als die des Punkts Ar3,
    - Wickeln des Blechs bei einer Temperatur im Bereich zwischen 500 und 700 °C, dann
    - Kaltwalzen des Blechs mit einem Reduktionsgrad von 50 bis 80 %,
    - kontinuierliches Wärmebehandeln durch Glühen mit einer Dauer von weniger als 15 Minuten, umfassend:
    ■ Erwärmen des Stahls bis er eine Temperatur im Bereich zwischen 750 und 850 °C erreicht,
    ■ isothermes Halten,
    ■ ein erstes Abkühlen bis auf eine Temperatur im Bereich zwischen 380 und 500 °C, und
    ■ isothermes Halten, dann
    ■ ein zweites Abkühlen bis auf Umgebungstemperatur,
    - Verfestigen, das mit einem Reduktionsgrad im Bereich zwischen 1,2 und 2,5 % realisiert wird.
  2. Verfahren nach Anspruch 1, dadurch gekennzeichnet, dass das erste Abkühlen einen ersten langsamen Teil, der mit einer Geschwindigkeit von weniger als 10 °C/Sek. durchgeführt wird, dann einen zweiten schnellen Teil umfasst, der mit einer Geschwindigkeit im Bereich zwischen 20 und 50 °C/Sek. durchgeführt wird.
  3. Verfahren nach einem der Ansprüche 1 oder 2, dadurch gekennzeichnet, dass ferner der Mangangehalt und der Siliciumgehalt des Stahls derart sind, dass gilt: 4 ≤ % Mn % Si ≤ 15
    Figure imgb0008
  4. Verfahren nach einem der Ansprüche 1 bis 3, dadurch gekennzeichnet, dass ferner der Mangangehalt des Stahls im Bereich zwischen 0,55 und 0,65 Ges.-% liegt und der Siliciumgehalt des Stahls im Bereich zwischen 0,08 und 0,12 Gew.-% liegt.
  5. Verfahren nach einem der Ansprüche 1 bis 3, dadurch gekennzeichnet, dass ferner der Mangangehalt des Stahls im Bereich zwischen 0,95 und 1,05 Gew.-% liegt und der Siliciumgehalt des Stahls im Bereich zwischen 0,16 und 0,20 Gew.-% liegt.
  6. Verfahren nach einem der Ansprüche 1 bis 5, dadurch gekennzeichnet, dass ferner der Stickstoffgehalt des Stahls kleiner al.s 0,005 Gew.-% ist.
  7. Verfahren nach einem der Ansprüche 1 bis 6, dadurch gekennzeichnet, dass ferner der Phosphorgehalt des Stahls kleiner als 0,015 Gew.-% ist.
  8. Durch Glühen wärmehärtbares Blech, das durch das Verfahren gemäß einem der Ansprüche 1 bis 7 erhalten werden kann, dadurch gekennzeichnet, dass es eine Streckgrenze im Bereich zwischen 260 und 360 MPa, eine Zugfestigkeit im Bereich zwischen 320 und 460 MPa, einen BH2-Wert größer als 60 MPa und einen Fließbereich kleiner oder gleich 0,2 % aufweist.
EP03775481A 2002-10-14 2003-10-10 Verfahren zur herstellung von wärmehärtbaren stahlblechen durch glühung, stahlbleche und davon hergestellte teile Expired - Lifetime EP1558769B1 (de)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
FR0212753 2002-10-14
FR0212753A FR2845694B1 (fr) 2002-10-14 2002-10-14 Procede de fabrication de toles d'acier durcissables par cuisson, toles d'acier et pieces ainsi obtenues
PCT/FR2003/002985 WO2004035838A1 (fr) 2002-10-14 2003-10-10 Procede de fabrication de toles d'acier durcissables par cuisson, toles d'acier et pieces ainsi obtenues

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EP1558769A1 EP1558769A1 (de) 2005-08-03
EP1558769B1 true EP1558769B1 (de) 2010-06-09

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US (1) US7540928B2 (de)
EP (1) EP1558769B1 (de)
JP (2) JP4892190B2 (de)
KR (1) KR101044741B1 (de)
CN (1) CN100366760C (de)
AT (1) ATE470729T1 (de)
AU (1) AU2003283507A1 (de)
BR (1) BR0315255B1 (de)
CA (1) CA2502079C (de)
DE (1) DE60332951D1 (de)
ES (1) ES2345045T3 (de)
FR (1) FR2845694B1 (de)
MX (1) MXPA05003938A (de)
PL (1) PL200655B1 (de)
RU (1) RU2338792C2 (de)
UA (1) UA80448C2 (de)
WO (1) WO2004035838A1 (de)
ZA (1) ZA200502882B (de)

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RU2516212C1 (ru) * 2012-10-18 2014-05-20 Открытое акционерное общество "Магнитогорский металлургический комбинат" Способ производства горячекатаного широкополосного рулонного проката
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KR20050055006A (ko) 2005-06-10
CA2502079A1 (fr) 2004-04-29
PL200655B1 (pl) 2009-01-30
PL374746A1 (en) 2005-10-31
KR101044741B1 (ko) 2011-06-28
RU2338792C2 (ru) 2008-11-20
JP4892190B2 (ja) 2012-03-07
MXPA05003938A (es) 2005-06-17
ZA200502882B (en) 2005-12-28
US20060157166A1 (en) 2006-07-20
CN1705757A (zh) 2005-12-07
CN100366760C (zh) 2008-02-06
BR0315255A (pt) 2005-08-23
CA2502079C (fr) 2011-08-09
JP2011006792A (ja) 2011-01-13
FR2845694B1 (fr) 2005-12-30
BR0315255B1 (pt) 2011-03-09
EP1558769A1 (de) 2005-08-03
ATE470729T1 (de) 2010-06-15
DE60332951D1 (de) 2010-07-22
US7540928B2 (en) 2009-06-02
AU2003283507A1 (en) 2004-05-04
RU2005114614A (ru) 2005-10-10
UA80448C2 (en) 2007-09-25
WO2004035838A1 (fr) 2004-04-29
ES2345045T3 (es) 2010-09-14
FR2845694A1 (fr) 2004-04-16
JP2006503183A (ja) 2006-01-26

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