EP1309734B2 - Acier et feuillard ou tole d'acier a resistance tres elevee, pouvant etre forme a froid, procede pour produire un feuillard d'acier et utilisations d'un tel acier - Google Patents

Acier et feuillard ou tole d'acier a resistance tres elevee, pouvant etre forme a froid, procede pour produire un feuillard d'acier et utilisations d'un tel acier Download PDF

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Publication number
EP1309734B2
EP1309734B2 EP02732754A EP02732754A EP1309734B2 EP 1309734 B2 EP1309734 B2 EP 1309734B2 EP 02732754 A EP02732754 A EP 02732754A EP 02732754 A EP02732754 A EP 02732754A EP 1309734 B2 EP1309734 B2 EP 1309734B2
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EP
European Patent Office
Prior art keywords
steel
strip
cold
producing
sheet
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.)
Expired - Lifetime
Application number
EP02732754A
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German (de)
English (en)
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EP1309734A1 (fr
EP1309734B1 (fr
Inventor
Harald Hofmann
Bernhard Engl
Manfred Menne
Thomas Heller
Werner Zimmermann
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ThyssenKrupp Steel Europe AG
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ThyssenKrupp Steel Europe AG
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Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • 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
    • 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
    • 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
    • C21D8/0221—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
    • C21D8/0236—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 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
    • C21D8/0273—Final recrystallisation annealing

Definitions

  • the invention relates to a Fe-Mn-Al-Si light carbon steel and a steel strip or sheet with good cold workability and higher strength. Moreover, the invention relates to a method for producing strips of such a steel and particularly suitable uses of such a steel.
  • a used for the production of body parts and the low temperature use lightweight steel is from the DE 197 27 759 C2 It contains besides Fe 10% to 30% Mn, 1% to 8% Al and 1 to 6% Si, the sum of the contents of Al and Si does not exceed 12%. In this known steel carbon is possibly contained in the impurity range.
  • carbon is provided as an optional alloying element.
  • the known lightweight steel has> 7% to 27% Mn,> 1% to 10% Al,> 0.7% to 4% Si, ⁇ 0.5% C, ⁇ 10% Cr, ⁇ 10% Nl and ⁇ 0, 3% Cu on. Further, in the steel, N, V, Nb, Ti, P may be contained, and the sum of these elements may not exceed 2%.
  • a comparable composite, high-strength and good cold-formable austenitic lightweight steel is in the DE 197 27 759 A1 described.
  • This steel contains (in% by weight) 9.5-12% (Al + Si), 10-30% Mn and the remainder essentially iron including common steel elements (C, P, S, O, N).
  • the Si content of this steel is 0.5-6% and its Al content 1-8% with a Mn content of 15-30%. Due to its particularly high tensile strength of up to 1100 MPa, this steel is particularly suitable for the production of body panels and stiffening structural assemblies of automobile bodies.
  • known light steel contains carbon, 0.001 to 1.6%.
  • this steel has 6 - 30% Mn, ⁇ 6% Al, 2.5% Si, ⁇ 10% Cr, ⁇ 10% Ni and ⁇ 5% Cu.
  • V, Ti, Nb, B, Zr and rare earths may be contained in the steel, the sum of their contents not exceeding 3%.
  • a method for producing gear parts by spin forming is known from DE 197 24 661 C2 According to this known method, a blank is formed from a microalloyed high strength structural steel having a lower yield strength of at least 500 N / mm 2 from a sheet. This blank is then cold worked by spin forming to the gearbox. In the course of forming the teeth, the sheet material is transformed to the limit of its forming capacity. Subsequently, a surface of the workpiece provided with the toothing is cured substantially free of thermal deformation while maintaining the temperature
  • the object of the invention is to provide, starting from the above-mentioned prior art, a light steel or a steel strip or sheet produced therefrom with good ductility and good strength, which can also be produced easily even on an industrial scale.
  • a method for producing a steel strip or plate and preferred uses for the steel are to be specified.
  • the object is achieved on the one hand by a light steel having the following composition (in% by weight): C: 0.1 - 1% Mn: 7.00 - 30.00% al: 1,00 - 10.00% Si: > 2.50 - 8.00% Al + Si: > 3.50 - 12.00% B: 0.002 - ⁇ 0.01% as well as optional Ni: ⁇ 8.00% Cu: ⁇ 3.00% N: ⁇ 0.60% Nb: ⁇ 0.30% Ti: ⁇ 0.30% V: ⁇ 0.30% P: ⁇ 0.01% Remaining iron and unavoidable impurities.
  • the impurities are sulfur and oxygen. attributed.
  • the targeted addition of boron in steels according to the invention leads to a marked improvement in the properties and the manufacturability.
  • the content of boron contained in the steel according to the invention causes a reduction of the yield strength, whereby the deformability is significantly improved.
  • the favorable influences of the alloy on the mechanical-technological properties of the invention are supported by the fact that the carbon content is 0.10-1.00% by weight, that is to say if a minimum of 0.10% by weight of carbon is present in the invention Steel is detectable.
  • steel or a steel strip or sheet produced therefrom has a significantly lower ⁇ r value compared to the sheets known from the prior art for the sheet material in question here in Rade.
  • composite cold rolled steel strips and sheets according to the invention are characterized by comparatively low yield strengths, improved ironing capability at elevated solidification exponents (n value), increased deep drawability (r value) and low planar anisotropy ( ⁇ r value) as well as an increased product of yield strength and elongation out.
  • the tensile strength of steel strips and sheets according to the invention is at least 680 MPa.
  • the product of tensile strength and elongation is at least 41,000 MPa.
  • the yield strength of steel sheets and strips according to the invention does not exceed 520 MPa.
  • steels according to the invention or sheets and strips produced therefrom have an extremely high degree of uniform expansion of from 20% to more than 45%. N values of up to 0.7 are achieved.
  • a particularly good kaltverformbares lightweight steel strip or sheet is obtained, which is particularly suitable for the production of components for automobile bodies due to its relatively high strength and low density.
  • the comparatively low weight of the steel sheet according to the invention and the high strength at the same time have a positive effect.
  • steel sheets according to the invention are particularly suitable for the production of non-magnetic components in the case of a purely austenitic microstructure.
  • the inventive maintain their strength even at very low temperatures. They are suitable as such, in particular for the production of components used in cryotechnology, such as containers or pipes for refrigeration.
  • the positive effects of boron in steel used according to the invention can be achieved particularly reliably if the boron content is 0.003 to 0.008% by weight.
  • the C content lying in the range of 0.1% to 1.0% ensures improved manufacturability of steel sheets and strips according to the invention.
  • the formation of intermetallic phases is suppressed due to the presence of carbon. Cracks and instabilities in the strip edge area, as they occur in the steel strips produced from the known steels, are thus significantly reduced, with increasing C content, the instabilities in particular decrease. Further improvement in strip edge quality is achieved by the addition of boron. As a result, tape edge instabilities can be almost completely avoided by the combined addition of C and B.
  • inventively provided C and B contents open up a wide range of hot rolling parameters.
  • Steel strips and sheets according to the invention can preferably be produced by a method in which a starting material, such as slabs, thin slabs or strip, is cast from a composite according to the invention in the above-described manner, in which the cast starting material is heated to ⁇ 1100 ° C. is used directly at such a temperature, in which the preheated starting material is hot rolled to hot strip at a hot end temperature of at least 800 ° C and in which the finish rolled hot strip is coiled at a 450 ° C to 700 ° C amounting reel temperature.
  • a starting material such as slabs, thin slabs or strip
  • the hot-rolled strip according to the invention at hot-end temperatures of at least 800 ° C. and coiled at low temperatures, the mentioned positive effect of the carbon and in particular of the boron is fully utilized. Boron and carbon, for example, produce higher tensile strength and yield strength values for tapes which have been hot-rolled in this area, while the elongation at break values are still acceptable. As the hot rolling end temperature increases, the tensile strength and yield strength decrease while the elongation values increase.
  • the desired properties of the steel strip obtained can be selectively and easily influenced in a targeted manner and can influence the desired properties of the steel strip obtained in a targeted and simple manner.
  • hot strip is characterized by good Nutzseigenhack. If thinner sheets or strips are to be produced, then the hot strip can be cold rolled after being rolled into cold strip, wherein the cold rolling is advantageously carried out with a cold rolling degree of 30% to 75%.
  • the resulting cold strip is then subjected to an annealing, the annealing temperatures should be between 600 ° C to 1100 ° C.
  • the annealing can be carried out in the hood in the temperature range of 600 ° C to 750 ° C or in the annealing furnace at temperatures of 750 ° C to 1100 ° C.
  • a purely austenitic structure or a microstructure consisting of a mixture of ferrite and austenite with proportions of martensite can be incorporated into steel according to the invention.
  • the steels according to the invention can therefore be shaped much better. In the course of cold working, they solidify much more strongly than the high-strength microalloyed or multiphase steels known for production by pressure-rolling. Thus, depending on cold deformation, component strengths ranging from 1400 N / mm 2 to 2200 N / mm 2 can be achieved. An additional hardening of the components produced after the cold deformation can therefore be omitted. Also, it has a favorable effect, in particular in the production of toothed transmission components with respect to the intended use, that the steels used according to the invention for their production are reduced in density because of the high content of light elements, such as Si, Al.
  • the steel according to the invention allows the cost-effective Production of lightweight, heavy duty and dimensionally stable components by cold forming, in particular spin forming.
  • Table 1 the compositions of four steels A, B, C, D, E are indicated, of which the steels A and B correspond to the alloy provided according to the invention, while the steels C, D and E are comparative examples.
  • Table 1 stolen C Mn al Si B Fe, impurities A 0.5 15 3 3 0,003 rest B 0.5 20 3 3 0,003 rest C - 20 3 3 0,003 rest D - 14 3 3 - rest e - 19 3 3 - rest
  • the steels A to E of the respective compositions have been melted and cast into slabs. Subsequently, the slabs were preheated to a temperature of 1150 ° C. The preheated slabs are then hot rolled and then rewound.
  • the resulting hot strips are then cold-rolled with a strain of about 65% cold and annealed at 950 ° C. in one pass.
  • the mechanical properties of the cold-rolled steel sheets thus obtained are shown in Table 3 entered.
  • all variants of steel sheets according to the invention are particularly suitable for the production of body components, especially for the outer panels of an automobile body, wheels for vehicles, in particular motor vehicles, non-magnetic components, containers used in cryotechnology, internal high-pressure or external high-pressure deformed components Tubing intended in particular for the manufacture of high-strength engine parts, such as camshafts or piston rods, of impulse-impacting loads, such as bombardment, specific components or protective elements, such as armor plating, or body armor for the human or animal body.
  • high-strength transmission components can be produced from steel sheets according to the invention, which are distinguished by their low weight and good service properties, without the need for additional heat treatment.

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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)
  • Heat Treatment Of Steel (AREA)

Claims (29)

  1. Acier léger avec une bonne aptitude au formage à froid et une résistance mécanique supérieure, composé comme suit (en pourcentage en poids) : C: 0,1 à 1 % Mn: 7,00 à 30,00 % Al: 1,00 à 10,00 % Si: > 2,50 à 8, 00 % Al+ Si: > 3,50 à 12,00 % B: 0,002 à < 0,01 %
    ainsi qu'au choix Ni : < 8,00 % Cu : < 3,00 % N : < 0,60 % Nb : < 0,30 % Ti : < 0,30 % V : < 0,30 % P : < 0, 01%
    le reste étant du fer et des impuretés inévitables.
  2. Acier léger selon la revendication 1, caractérisé en ce que la teneur en Si est > 2,70 % en poids.
  3. Acier léger selon l'une des revendications précédentes, caractérisé en ce que la teneur en bore est de 0,003 à 0,008 % en poids.
  4. Feuillard ou tôle fabriqué/e en acier composé selon les revendications 1 à 3.
  5. Feuillard ou tôle selon la revendication 4, caractérisé en ce que sa résistance à la traction est d'au moins 680 MPa.
  6. Feuillard ou tôle selon revendication 4 ou 5, caractérisé en ce que le produit de sa résistance à la traction et de son allongement est d'au moins 41000 MPa.
  7. Feuillard ou tôle selon l'une des revendications 4 à 6, caractérisé en ce que sa limite d'élasticité va jusqu'à 520 MPa.
  8. Procédé pour la fabrication d'un feuillard ou d'une tôle d'acier formable à froid de résistance supérieure,
    - dans lequel est moulé un produit de départ, comme brame, brame mince ou feuillard, en acier selon l'une des revendications 1 à 3,
    - dans lequel le produit de départ est chauffé à ≥ 1100° C ou mis en oeuvre directement à une telle température,
    - dans lequel le produit de départ préchauffé est laminé à chaud en feuillard à une température finale de laminage à chaud d'au moins 800° C,
    et
    - dans lequel le feuillard à chaud, après passage au train final, est bobiné à une température de bobinage située entre 450 °C et 700 °C.
  9. Procédé selon la revendication 8, caractérisé en ce que le feuillard à chaud est laminé à froid en feuillard à froid après le bobinage.
  10. Procédé selon la revendication 9, caractérisé en ce que le feuillard à froid est soumis à un recuit à une température de recuit de 600 °C à 1100 °C.
  11. Procédé selon la revendication 10, caractérisé en ce que le recuit est exécuté en tant que recuit dans le four à cloche, à une température de recuit de 600 °C à 750 °C.
  12. Procédé selon la revendication 10, caractérisé en ce que le recuit est exécuté en tant que recuit en continu à une température de recuit de 750° C à 1100° C.
  13. Procédé selon l'une des revendications 9 à 12, caractérisé en ce que le feuillard à froid est dressé.
  14. Procédé selon l'une des revendications 8 à 13, caractérisé en ce que le laminage à froid est exécuté à un degré de laminage à froid de 30 % à 75 %.
  15. Procédé selon l'une des revendications 8 à 14, caractérisé en ce que le feuillard à chaud ou à froid est utilisé à la fabrication d'ébauches qui sont ensuite transformées en pièces préfabriquées par formage de finition à froid.
  16. Procédé selon la revendication 15, caractérisé en ce que le formage à froid est exécuté par fluotournage
  17. Utilisation d'un acier ou d'un feuillard d'acier ou d'une tôle d'acier selon l'une des revendications 1 à 7 pour la fabrication de pièces de carrosseries.
  18. Utilisation d'un acier ou d'un feuillard d'acier ou d'une tôle d'acier selon l'une des revendications 1 à 7 pour la fabrication de pièces de carrosseries de véhicules automobiles visibles de l'extérieur.
  19. Utilisation d'un acier ou d'un feuillard d'acier ou d'une tôle d'acier selon l'une des revendications 1 à 7 pour la fabrication de roues pour véhicules, en particulier pour véhicules automobiles
  20. Utilisation d'un acier ou d'un feuillard d'acier ou d'une tôle d'acier selon l'une des revendications 1 à 7 pour la fabrication de pièces non magnétiques.
  21. Utilisation d'un acier ou d'un feuillard d'acier ou d'une tôle d'acier selon l'une des revendications 1 à 7 pour la fabrication d'éléments utilisés dans la technique cryogénique.
  22. Utilisation d'un acier ou d'un feuillard d'acier ou d'une tôle d'acier selon l'une des revendications 1 à 7 pour la fabrication de pièces déformées par formage sous pression interne ou externe.
  23. Utilisation d'un acier ou d'un feuillard d'acier ou d'une tôle d'acier selon l'une des revendications 1 à 6 pour la fabrication de tubes destinés en particulier à la fabrication de pièces de moteurs à haute résistance, comme arbres à cames ou tiges de pistons.
  24. Utilisation d'un acier ou d'un feuillard d'acier ou d'une tôle d'acier selon l'une des revendications 1 à 7 pour la fabrication de certaines pièces, telles que tôles de blindage pour la protection contre des sollicitations d'impact, comme tirs.
  25. Utilisation d'un acier ou d'un feuillard d'acier ou d'une tôle d'acier selon l'une des revendications 1 à 7 pour la fabrication d'éléments de protection déterminés, comme casques et protections corporelles pour la protection de personnes contre les sollicitations d'impact, comme tirs.
  26. Utilisation d'un acier ou d'un feuillard d'acier ou d'une tôle d'acier selon l'une des revendications 1 à 7 pour la fabrication de pièces par fluotournage.
  27. Utilisation d'un feuillard d'acier ou d'une tôle d'acier selon l'une des revendications 1 à 7 pour la fabrication de pièces d'engrenages.
  28. Utilisation selon la revendication 27, caractérisée en ce que les pièces d'engrenages sont pourvues de dentures.
  29. Utilisation selon revendication 27 ou 28, caractérisée en ce que les pièces d'engrenages sont fabriquées par fluotournage.
EP02732754A 2001-06-13 2002-06-13 Acier et feuillard ou tole d'acier a resistance tres elevee, pouvant etre forme a froid, procede pour produire un feuillard d'acier et utilisations d'un tel acier Expired - Lifetime EP1309734B2 (fr)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
DE10128544 2001-06-13
DE10128544A DE10128544C2 (de) 2001-06-13 2001-06-13 Höherfestes, kaltumformbares Stahlblech, Verfahren zu seiner Herstellung und Verwendung eines solchen Blechs
PCT/EP2002/006480 WO2002101109A1 (fr) 2001-06-13 2002-06-13 Acier et feuillard ou tole d'acier a resistance tres elevee, pouvant etre forme a froid, procede pour produire un feuillard d'acier et utilisations d'un tel acier

Publications (3)

Publication Number Publication Date
EP1309734A1 EP1309734A1 (fr) 2003-05-14
EP1309734B1 EP1309734B1 (fr) 2007-08-15
EP1309734B2 true EP1309734B2 (fr) 2012-06-20

Family

ID=7688074

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EP02732754A Expired - Lifetime EP1309734B2 (fr) 2001-06-13 2002-06-13 Acier et feuillard ou tole d'acier a resistance tres elevee, pouvant etre forme a froid, procede pour produire un feuillard d'acier et utilisations d'un tel acier

Country Status (12)

Country Link
US (1) US20030145911A1 (fr)
EP (1) EP1309734B2 (fr)
JP (1) JP4227010B2 (fr)
KR (1) KR100536645B1 (fr)
CN (1) CN1215188C (fr)
AT (1) ATE370258T1 (fr)
CA (1) CA2414138C (fr)
DE (2) DE10128544C2 (fr)
DK (1) DK1309734T3 (fr)
ES (1) ES2292762T5 (fr)
PT (1) PT1309734E (fr)
WO (1) WO2002101109A1 (fr)

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DE102005010243A1 (de) * 2005-03-05 2006-09-07 Sms Demag Ag Verfahren und Anlage zur Herstellung eines Leichtbaustahls mit einem hohen Mangan-Gehalt
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CN1215188C (zh) 2005-08-17
DE10128544A1 (de) 2003-01-02
EP1309734A1 (fr) 2003-05-14
ES2292762T5 (es) 2012-10-29
DE50210689D1 (de) 2007-09-27
CN1463297A (zh) 2003-12-24
WO2002101109A1 (fr) 2002-12-19
US20030145911A1 (en) 2003-08-07
JP4227010B2 (ja) 2009-02-18
PT1309734E (pt) 2007-11-28
CA2414138A1 (fr) 2002-12-02
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DE10128544C2 (de) 2003-06-05
EP1309734B1 (fr) 2007-08-15

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