EP2155916B2 - Stahl von geringer dichte mit guten prägeeigenschaften - Google Patents

Stahl von geringer dichte mit guten prägeeigenschaften Download PDF

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EP2155916B2
EP2155916B2 EP08805524.9A EP08805524A EP2155916B2 EP 2155916 B2 EP2155916 B2 EP 2155916B2 EP 08805524 A EP08805524 A EP 08805524A EP 2155916 B2 EP2155916 B2 EP 2155916B2
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sheet
rolled
steel sheet
cold
temperature
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EP2155916A1 (de
EP2155916B1 (de
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Astrid Perlade
Xavier Garat
Jean-Louis Uriarte
Olivier Bouaziz
Josée Drillet
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ArcelorMittal France SA
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ArcelorMittal France 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • 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
    • 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
    • C21D8/0221—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
    • 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
    • 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
    • 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
    • C21D8/0421—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
    • C21D8/0436—Cold 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
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • 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
    • 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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • 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
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn

Definitions

  • the invention relates to a ferritic sheet of hot-rolled or cold-rolled steel, having a strength greater than 400 MPa and a density of less than about 7.3, and its manufacturing process.
  • the object of the invention is also to provide a manufacturing method compatible with the usual industrial installations.
  • the subject of the invention is a ferritic hot-rolled steel sheet whose composition comprises, the contents being expressed by weight: 0.001 ⁇ C ⁇ 0.15%, Mn ⁇ 1%, Si ⁇ 1.5% , 6% ⁇ Al ⁇ 10%, 0.020% ⁇ Ti ⁇ 0.5%, S ⁇ 0.050%, P ⁇ 0, 1% and, optionally, one or more elements selected from: Cr ⁇ 1%, Mo ⁇ 1%, Ni ⁇ 1%, Nb ⁇ 0.1%, V ⁇ 0.2%, B ⁇ 0.01%, the rest of the composition consisting of iron and unavoidable impurities resulting from the preparation, the average size of ferrite grain d IV measured on a surface perpendicular to the direction transverse to the rolling being less than 100 micrometers.
  • the composition comprises: 0.001% ⁇ C ⁇ 0.010%, Mn ⁇ 0.2%.
  • the composition comprises: 0.010% ⁇ C ⁇ 0.15%, 0.2% ⁇ Mn ⁇ 1%.
  • the composition comprises: 7.5% ⁇ Al ⁇ 10%.
  • the composition comprises: 7.5% ⁇ Al ⁇ 8.5%.
  • the carbon content in solid solution is preferably less than 0.005% by weight.
  • the strength of the sheet is greater than or equal to 400 MPa.
  • the strength of the sheet is greater than or equal to 600 MPa.
  • the subject of the invention is also a process for manufacturing a hot-rolled steel sheet according to which a steel of composition is supplied according to one of the above compositions, the steel is cast in the form of a semi-finished product. that is heated to a temperature greater than or equal to 1150 ° C.
  • the semi-finished product is hot-rolled to obtain a sheet, by means of at least two rolling steps carried out at temperatures above 1050 ° C., the reduction rate of each of the steps being greater than or equal to 30%, the time flowing between each of the rolling steps, and the next rolling step being greater than or equal to 10 s.
  • the rolling is completed at a temperature T FL greater than or equal to 900 ° C, the sheet is cooled so that the time interval tp flowing between 850 and 700 ° C is greater than 3 s, to obtain a precipitation of precipitates ⁇ , then the sheet is reeled at a temperature T bob of between 500 and 700 ° C.
  • the casting is carried out directly in the form of thin slabs or thin strips between contra-rotating rolls.
  • the invention also relates to a method of manufacturing a cold-rolled and annealed steel sheet according to which a hot-rolled steel sheet manufactured according to one of the above modes is supplied, then the sheet is cold-rolled. with a reduction ratio of between 30 and 90%, so as to obtain a cold-rolled sheet.
  • the cold-rolled sheet is then heated to a temperature T 'with a speed V c greater than 3 ° C./s, then the sheet is cooled at a speed V R less than 100 ° C./s, the temperature T' and the speed V R being selected so as to obtain complete recrystallization, a linear fraction f of intergranular precipitates ⁇ of less than 30% and a carbon content in solid solution of less than 0.005% by weight.
  • the cold-rolled sheet is preferably heated to a temperature T 'of between 750 and 950 ° C.
  • a sheet of composition is supplied: 0.010% ⁇ C ⁇ 0.15%, 0.2% ⁇ Mn ⁇ 1%, Si ⁇ 1.5%, 6% ⁇ Al ⁇ 10%, 0.020% ⁇ Ti ⁇ 0.5%, S ⁇ 0.050%, P ⁇ 0, 1% and, optionally, one or more elements selected from: Cr ⁇ 1%, Mo ⁇ 1 %, Ni ⁇ 1%, Nb ⁇ 0.1%, V ⁇ 0.2%, B ⁇ 0.01%, the rest of the composition consisting of iron and unavoidable impurities resulting from the preparation, and heating the cold-rolled sheet at a temperature T 'chosen so as to avoid the dissolution of precipitates ⁇ .
  • the invention also relates to the use of steel sheets according to one of the above modes or manufactured in one of the above modes for the manufacture of skin parts or structural parts in the automotive field .
  • the invention relates in particular to a manufacturing method for controlling the precipitation of intermetallic carbides, the microstructure, and the texture in steels including particular combinations of carbon, aluminum and titanium.
  • the rest of the composition consists of iron and unavoidable impurities that result from the elaboration.
  • the structure of the steels according to the invention comprises a homogeneous distribution of highly disoriented ferritic grains: the strong disorientation between neighboring grains makes it possible to avoid the crimping defect: this defect is characterized, during the cold forming of sheets, by the localized and premature appearance of strips in the direction of rolling, forming a relief. This phenomenon is due to the presence of recrystallized and weakly disoriented grain groups, since they originate from the same original grain before recrystallization.
  • a scuff sensitive structure is characterized by spatial texture distribution.
  • the steels according to the invention do not show any sensitivity to creasing during the shaping, because of their favorable texture.
  • the microstructure at ambient temperature of the steels consists of an equiaxed ferrite matrix whose average grain size is less than 50 micrometers.
  • Aluminum is mainly in solid solution in this matrix based on iron.
  • These steels contain kappa precipitates (" ⁇ ") which are a ternary Fe 3 AlC x intermetallic phase. The presence of these precipitates in the ferritic matrix leads to a significant hardening.
  • ⁇ precipitates must not be present in the form of a marked intergranular precipitation under penalty of a significant reduction in ductility: the inventors have shown that the ductility was reduced when the linear fraction of ferritic grain boundaries which present ⁇ precipitation was greater than or equal to 30%.
  • this linear fraction f is given to the figure 1 : If we consider a particular grain whose contour is limited by successive grain boundaries of length L 1 , L 2 , .. L i , observations by microscopy show that this grain may have precipitates ⁇ along the joints over a length d 1 , ..d i ...
  • ⁇ S Li represents the total length of the grain boundaries relative to the surface (S) considered.
  • the expression f thus translates the degree of recovery of ferritic grain boundaries by ⁇ precipitation.
  • the cast semifinished products are first brought to a temperature above 1150 ° C. in order to reach at all points a temperature favorable to the high deformations that the steel will undergo during the various rolling steps.
  • the hot rolling step of these semi-finished products starting at more than 1150 ° C. can be done directly after casting. that an intermediate heating step is not necessary in this case.
  • the sheet is then cooled at a speed V R of less than 100 ° C./s so as not to cause any embrittlement by excess of carbon in solid solution.
  • V R a speed of less than 100 ° C./s so as not to cause any embrittlement by excess of carbon in solid solution.
  • This result is particularly surprising in that it could be thought that a rapid cooling rate would be favorable to reduce embrittling precipitation.
  • the inventors have demonstrated that slow cooling, at a cooling rate of less than 100 ° C./s, led to a significant precipitation of carbides which thus reduced the carbon content in solid solution: this precipitation has the effect of increase the resistance without any detrimental effect on ductility.
  • a temperature T 'of between 750 and 950 ° C. is preferably chosen to obtain complete recrystallization.
  • the temperature T 'of in addition to preventing the dissolution of ⁇ precipitates present before the annealing. In fact, if these precipitates are dissolved, the subsequent precipitation at slow cooling will take place in embrittling intergranular form: a too high annealing temperature would lead to the redissolution of the precipitates ⁇ formed during the manufacture of the hot-rolled sheet and reduce the mechanical strength. .
  • a temperature T 'of between 750 and 800 ° C. will preferably be chosen.
  • the semi-finished products were heated to a temperature of 1220 ° C. and hot-rolled to obtain a sheet having a thickness of about 3.5 mm.
  • the references I1-a, I1-b, I1-c, I1-d, I1-e designate for example five steel sheets manufactured under different conditions from the composition I1.
  • Table 3 shows the density measured on the plates of Table 2 and certain mechanical and microstructural characteristics.
  • the resistance Rm the uniform elongation A u , the elongation at break A t, have thus been measured in the cross-machine direction with respect to rolling.
  • the IV grain size was also measured by the method of linear intercepts according to the NF EN ISO 643 standard on a surface perpendicular to the direction transverse to the rolling. The measurement of d IV was carried out in the direction perpendicular to the thickness of the sheet. In order to obtain increased mechanical properties, it is more particularly desired to obtain a grain size of IV less than 100 microns.
  • Table 3 Properties of hot-rolled sheets obtained from I1 and I3 steels.
  • the steel sheets according to the invention are characterized by a grain size IV less than 100 micrometers and have a strength ranging from 505 to 645 MPa.
  • the sheet I1c was laminated with an insufficient number of rolling steps with a rate greater than 30%, a time interpasse and a time interval t p too short.
  • the consequences are identical to those noted on sheets I1b and I1e. Since the time interval t p is too low, a hardening precipitation of ⁇ precipitates and TiC carbides occurs only partially, which makes it impossible to take full advantage of the curing possibilities.
  • the steel R1 has an insufficient titanium content which leads to a solid solution carbon content that is too high: the folding ability is then reduced.
  • Steel R2 has an insufficient aluminum content which does not allow to obtain a density lower than 7.3.
  • R3, R4, R5 and R6 steels contain too much aluminum and possibly carbon: their ductility is reduced due to the excessive precipitation of intermetallic phases or carbides
  • Example 2 Cold-rolled and annealed sheets
  • Table 6 presents certain mechanical, chemical, microstructural and density characteristics of the sheets of Table 5.
  • the yield strength Re the resistance Rm, uniform elongation Au, elongation at break A t .
  • the soil sol carbon content in solid solution was also measured. The ability to bend and press was evaluated. It was also noted the possible presence of scuffing consecutive deformations.
  • the microstructure of these recrystallized sheets consists of equiaxed ferrite whose average ⁇ - grain size was measured in the transverse rolling direction. The rate of recovery of ferritic grain boundaries by ⁇ precipitation was also measured using the Aphelion TM image analysis software .
  • Table 6 Mechanical properties of cold-rolled and annealed sheets obtained from I1 and I3 steels.
  • the steel sheets I1a1 and I3a1 have a solid solution carbon content, a ferritic equiaxed grain size, and a grain boundary recovery ratio that satisfies the conditions of the invention. As a result, the ability to bend, stamping, scratch resistance of these sheets, is high.
  • the figure 4 illustrates the microstructure of the steel sheet I1a1 according to the invention.
  • the figure 5 illustrates the microstructure of another steel sheet according to the invention, I3a1: note the presence of ⁇ precipitates of which only a small amount is present in intergranular form, which allows to maintain a high ductility.
  • the steel sheet I1a2 was cooled at a too high speed after annealing: the carbon is then completely in solid solution, which causes a reduction in ductility of the matrix resulting in the local presence of fragile areas on the plates. facies of rupture.
  • the sheet I3a2 has been cooled too fast and also leads to an excessive content of solid solution.
  • the figure 6 illustrates the microstructure of the sheet I3a3: it was annealed at too high a temperature T ': the ⁇ precipitates present before the annealing were dissolved, their subsequent precipitation after cooling intervened in an excessive amount of intergranular form. This results in the local presence of fragile beaches on fracture facies.
  • the sheet 13a4 was also annealed at a temperature which causes partial dissolution of the ⁇ precipitates.
  • the carbon content in solid solution is excessive.
  • the steel sheet I1c1 was made from a hot-rolled sheet not satisfying the requirements of the invention: the equiaxial grain size is too large, the crimping resistance and the stamping ability are insufficient.
  • the hot-rolled sheet I3b which does not satisfy the criteria of the invention, is not suitable for deformation since transverse cracks appear during cold rolling.
  • the steels according to the invention have good continuous galvanizing properties, in particular during an annealing cycle at 800 ° C. with a dew point temperature higher than -20 ° C.
  • the steels according to the invention thus have a combination of properties (density, mechanical strength, deformability, weldability, coating) particularly interesting. These steel sheets are used with advantage for the manufacture of skin parts or structure in the automotive field.

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

Claims (16)

  1. Warmgewalztes ferritsches Blech aus Stahl, dessen Zusammensetzung, wobei die Gehalte in Gewicht ausgedrückt sind, umfasst: 0 , 001 ≤ C ≤ 0 , 15 %
    Figure imgb0028
     Mn ≤ 1 %
    Figure imgb0029
     Si ≤ 1 , 5 %
    Figure imgb0030
     6 % ≤ Al ≤ 10 %
    Figure imgb0031
     0 , 020 % ≤ Ti ≤ 0 , 5 %
    Figure imgb0032
     S ≤ 0 , 050 %
    Figure imgb0033
     P ≤ 0 , 1 %
    Figure imgb0034
    und optional ein oder mehrere Elemente, ausgewählt aus: Cr ≤ 1 %
    Figure imgb0035
     Mo ≤ 1 %
    Figure imgb0036
     Ni ≤ 1 %
    Figure imgb0037
     Nb ≤ 0 , 1 %
    Figure imgb0038
     V ≤ 0 , 2 %
    Figure imgb0039
     B ≤ 0 , 010 %
    Figure imgb0040
    wobei der Rest der Zusammensetzung aus Eisen und unvermeidlichen Unreinheiten im Ergebnis der Herstellung besteht,
    wobei die durchschnittliche Ferritkorngröße dIV, gemessen auf einer Fläche lotrecht zur transversen Richtung im Verhältnis zum Walzen, kleiner als 100 Mikrometer ist, wobei das Blech einen Niederschlag von Kappa- und TiC-Karbid-Präzipitaten umfasst.
  2. Kaltgewalztes und geglühtes ferritisches Blech, hergestellt aus einem warmgewalzten Blech nach Anspruch 1, dadurch gekennzeichnet, dass seine Struktur aus gleichachsigem Ferrit besteht, dessen durchschnittliche Korngröße dα kleiner als 50 Mikrometer ist, und dass die lineare Fraktion f intergranularer Präzipitate k kleiner als 30 % ist, wobei die lineare Fraktion f definiert ist durch f = ∑ S di ∑ S Li ,
    Figure imgb0041
    wobei ∑ S di
    Figure imgb0042
     die Gesamtlänge der Kornfugen bezeichnet, die Präzipitate k relativ zu einer betrachteten Fläche (S) aufweisen, wobei ∑ S Li
    Figure imgb0043
     die Gesamtlänge der Kornfugen relativ zu der betrachteten Fläche (S) bezeichnet.
  3. Stahlblech nach Anspruch 1 oder 2, dadurch gekennzeichnet, dass seine Zusammensetzung, wobei die Gehalte in Gewicht ausgedrückt sind, umfasst: 0 , 001 % ≤ C ≤ 0 , 010 %
    Figure imgb0044
     Mn ≤ 0 , 2 % .
    Figure imgb0045
  4. Stahlblech nach Anspruch 1 oder 2, dadurch gekennzeichnet, dass seine Zusammensetzung, wobei die Gehalte in Gewicht ausgedrückt sind, umfasst: 0 , 010 % < C ≤ 0 , 15 %
    Figure imgb0046
     0 , 2 % < Mn ≤ 1 % .
    Figure imgb0047
  5. Stahlblech nach einem der Ansprüche 1 bis 4, dadurch gekennzeichnet, dass seine Zusammensetzung, wobei die Gehalte in Gewicht ausgedrückt sind, umfasst: 7 , 5 % ≤ Al ≤ 10 % .
    Figure imgb0048
  6. Stahlblech nach einem der Ansprüche 1 bis 4, dadurch gekennzeichnet, dass seine Zusammensetzung, wobei die Gehalte in Gewicht ausgedrückt sind, umfasst: 7 , 5 % ≤ Al ≤ 8 , 5 % .
    Figure imgb0049
  7. Stahlblech nach einem der Ansprüche 1 bis 6, dadurch gekennzeichnet, dass der Kohlenstoffgehalt in fester Lösung kleiner als 0,005 Gew.-% ist.
  8. Stahlblech nach einem der Ansprüche 1 bis 7, dadurch gekennzeichnet, dass seine Festigkeit Rm größer oder gleich 400 MPa ist.
  9. Stahlblech nach Anspruch 4, dadurch gekennzeichnet, dass seine Festigkeit Rm größer oder gleich 600 MPa ist.
  10. Herstellungsverfahren eines warmgewalzten Stahlblechs, wobei:
    - ein Stahl in einer Zusammensetzung nach einem der Ansprüche 1 bis 6 bereitgestellt wird,
    - der Stahl in Form eines Halbfertigprodukts gegossen wird, dann
    - das Halbfertigprodukt auf eine Temperatur über oder gleich 1150 °C gebracht wird, dann
    - das Halbfertigprodukt warmgewalzt wird, um in mindestens zwei Walzschritten, die bei Temperaturen über 1050 °C durchgeführt werden, ein Blech zu erhalten, wobei der Reduktionsgrad bei jedem der mindestens zwei Schritte über oder gleich 30 % ist, wobei die Zeit, die zwischen jedem der mindestens zwei Walzschritte und dem nächsten Walzschritt vergeht, über oder gleich 10 s ist, dann
    - das Walzen bei einer Temperatur TFL über oder gleich 900 °C beendet wird, dann
    - das Blech derart abgekühlt wird, dass das Zeitintervall tp, das zwischen 850 und 700 °C vergeht, über 3 s ist, um einen Niederschlag von Präzipitaten k zu erhalten, dann
    - das Blech bei einer Temperatur Tbob zwischen 500 und 700 °C aufgespult wird.
  11. Herstellungsverfahren eines warmgewalzten Stahlblechs nach Anspruch 10, dadurch gekennzeichnet, dass der Abstich direkt in Form eines Gusses schlanker Brammen oder schlanker Bänder zwischen gegendrehende Zylinder durchgeführt wird.
  12. Herstellungsverfahren eines kaltgewalzten und geglühten Stahlblechs, wobei:
    - ein warmgewalztes Stahlblech, das nach Anspruch 10 oder 11 hergestellt ist, bereitgestellt wird, dann
    - das Bleich mit einem Reduktionsgrad zwischen 30 und 90 % derart kaltgewalzt wird, dass ein Kaltwalzblech entsteht, dann
    - das kaltgewalzte Blech auf eine Temperatur T' mit einer Geschwindigkeit Vc über 3 °C/s erwärmt wird, dann
    - das Blech mit einer Geschwindigkeit VR unter 100 °C/s abgekühlt wird,
    - wobei die Temperatur T' und die Geschwindigkeit VR derart ausgewählt sind, dass eine vollständige Rekristallisierung, eine lineare Fraktion f intergranularer Präzipitate k unter 30 % und ein Kohlenstoffgehalt in fester Lösung unter 0,005 Gew.-% erreicht wird.
  13. Herstellungsverfahren nach Anspruch 12, dadurch gekennzeichnet, dass das kaltgewalzte Blech auf eine Temperatur T' zwischen 750 und 950 °C inklusive erwärmt wird.
  14. Herstellungsverfahren nach Anspruch 12, dadurch gekennzeichnet, dass ein Blech mit einer Zusammensetzung nach Anspruch 4 bereitgestellt wird und dass das kaltgewalzte Blech auf eine Temperatur T' erwärmt wird, die derart ausgewählt ist, dass die Auflösung von Präzipitaten k vermieden wird.
  15. Herstellungsverfahren nach Anspruch 12, dadurch gekennzeichnet, dass ein Blech mit einer Zusammensetzung nach Anspruch 4 bereitgestellt wird und dass das kaltgewalzte Blech auf eine Temperatur T' zwischen 750 und 800 °C inklusive erwärmt wird.
  16. Verwendung von Stahlblechen nach einem der Ansprüche 1 bis 9 oder hergestellt nach einem der Ansprüche 10 bis 15 für die Herstellung von Haut- oder Strukturteilen auf dem Gebiet von Kraftfahrzeugen.
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