EP2707513B1 - Procede de fabrication d'acier martensitique a tres haute resistance et tôle ou piece ainsi obtenue - Google Patents

Procede de fabrication d'acier martensitique a tres haute resistance et tôle ou piece ainsi obtenue Download PDF

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EP2707513B1
EP2707513B1 EP12724656.9A EP12724656A EP2707513B1 EP 2707513 B1 EP2707513 B1 EP 2707513B1 EP 12724656 A EP12724656 A EP 12724656A EP 2707513 B1 EP2707513 B1 EP 2707513B1
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steel
sheet
temperature
blank
mean
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German (de)
English (en)
French (fr)
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EP2707513A1 (fr
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Kangying ZHU
Olivier Bouaziz
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ArcelorMittal SA
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ArcelorMittal 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
    • 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
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/62—Quenching devices
    • C21D1/673—Quenching devices for die quenching
    • 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
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—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
    • C21D8/0231—Warm rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • 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
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Definitions

  • the invention relates to a method for manufacturing sheet or steel parts with a martensitic structure, with a mechanical strength greater than that which could be obtained by austenitization and then simple fast cooling treatment with martensitic quenching, and properties of mechanical strength and durability. elongation allowing their application to the manufacture of energy absorbing parts in motor vehicles. In some applications, it is sought to produce steel parts combining high mechanical strength, high impact resistance and good corrosion resistance. This type of combination is particularly desirable in the automotive industry where significant vehicle lightening is sought. This can be achieved particularly through the use of steel parts with very high mechanical properties whose microstructure is martensitic or bainito-martensitic. Anti-intrusion parts, structure or participating in the safety of motor vehicles such as: bumper cross members, door or center pusher reinforcements, wheel arms, require for example the qualities mentioned above. Their thickness is preferably less than 3 millimeters.
  • the patent EP0971044 discloses the manufacture of a steel sheet coated with aluminum or an aluminum alloy, the composition of which comprises in weight content: 0.15-0.5% C, 0.5-3% Mn , 0.1-0.5% Si, 0.011% Cr, Ti ⁇ 0.2%, Al ⁇ 0.1%, P ⁇ 0.1%, S ⁇ 0.05%, 0.0005% ⁇ B ⁇ 0.08%, the rest being iron and impurities inherent in the elaboration.
  • This sheet is heated so as to obtain an austenitic transformation and hot stamped so as to produce a part, which is then cooled rapidly to obtain a martensitic or martensito-bainitic structure. In this way, it is possible to obtain, for example, a mechanical strength greater than 1500 MPa. However, we seek to obtain parts with even greater mechanical strength. We search still, at a given level of mechanical strength, to reduce the carbon content of the steel so as to improve its weldability.
  • the patent GB 1,166,042 discloses a steel composition suitable for this ausforming process, which comprises 0.1-0.6% C, 0.25-5% Mn, 0.5-2% Al, 0.5-3% Mo, 0.01-2% Si, 0.01-1% V.
  • These steels include significant additions of molybdenum, manganese, aluminum, silicon and / or copper. These are intended to create a larger metastability domain for austenite, ie to delay the onset of the transformation from austenite to ferrite, bainite or perlite, at the temperature at which performs hot deformation.
  • Most studies on ausforming have been conducted on steels with a carbon content greater than 0.3%.
  • these compositions adapted to the ausforming have the disadvantage of requiring special precautions for welding, and also have particular difficulties in the case where it is desired to perform a metal coating quenching.
  • these compositions have expensive addition elements.
  • (C) denotes the carbon content of the steel, expressed as a percentage by weight.
  • a method of manufacture is thus sought which makes it possible to obtain an ultimate tensile strength of 50 MPa for expression (1), ie a strength greater than 3220 (C ) + 958 MPa for this steel. It is sought to have a method for producing sheet metal with a very high yield strength, say greater than 1300 MPa. It is also sought to have a method for the manufacture of sheets or parts usable directly, that is to say without the need for a tempering treatment after quenching. It is also sought to have a manufacturing process for the manufacture of a sheet or a readily coated part by dipping in a metal bath.
  • the present invention aims to solve the problems mentioned above. It aims in particular to provide sheets with a yield strength greater than 1300 MPa, a mechanical strength expressed in megapascals greater than (3220 (C) +958) MPa, and preferably a total elongation greater than 3%.
  • the blank is hot-stamped so as to obtain a workpiece, then the workpiece is held in the stamping tool so as to cool it at a speed V R2 greater than the critical speed of martensitic quenching. .
  • the blank is pre-coated with aluminum or an aluminum-based alloy.
  • the blank is pre-coated with zinc or a zinc-based alloy.
  • the sheet or piece of steel obtained by any one of the above manufacturing processes is subjected to a subsequent heat treatment of tempering at a temperature T 4 of between 150 and 600 ° C. for a period of time between 5 and 30 minutes.
  • the subject of the invention is also an unreturned steel sheet having a yield strength greater than 1300 MPa, with a mechanical strength greater than (3220 (C) +958) megapascals, with the proviso that (C) denotes the weight percent carbon content of the steel, obtained by any of the above manufacturing processes, having a totally martensitic structure, having a medium size of slats less than 1 micrometer, the average elongation factor of slats being between 2 and 5
  • the invention also relates to a piece of unreturned steel obtained by any one of the above part manufacturing processes, the part comprising at least one zone of totally martensitic structure having an average slat size of less than 1 micrometer, the average elongation factor of the slats being between 2 and 5, the yield strength in said zone being greater than 1300 MPa and the mechanical strength being greater than (3220 (C) +958) megapascals, it being understood that (C) refers to the percentage carbon content of the steel.
  • the subject of the invention is also a sheet or a piece of steel obtained by the process with the above treatment of income, the steel having a totally martensitic structure, having in at least one zone an average slat size of less than 1 , 2 micrometer, the average elongation factor of the slats being between 2 and 5.
  • the inventors have demonstrated that the problems described above were solved by means of a specific ausforming process implemented on a particular range of steel compositions. Contrary to previous studies which showed that ausforming required the addition of expensive alloying elements, the inventors have surprisingly demonstrated that this effect can be obtained thanks to substantially less charged compositions of alloying elements.
  • the carbon content of the steel is less than 0.15% by weight, the quenchability of the steel is insufficient given the process used and it is not possible to obtain a totally martensitic structure.
  • this content is greater than 0.40%, welded joints made from these sheets or these parts have insufficient toughness.
  • the optimum carbon content for the implementation of the invention is between 0.16 and 0.28%.
  • Manganese lowers the initial formation temperature of martensite and slows the decomposition of austenite. In order to obtain sufficient effects to allow the implementation of the ausforming, the manganese content must not be less than 1.5%. Moreover, when the manganese content exceeds 3%, segregated zones are present in excessive quantity which is detrimental to the implementation of the invention. A preferred range for the implementation of the invention is 1.8 to 2.5% Mn.
  • the silicon content must be greater than 0.005% so as to contribute to the deoxidation of the steel in the liquid phase.
  • the silicon should not exceed 2% by weight due to the formation of surface oxides which significantly reduce the processability in processes involving a continuous passage of the steel sheet in a coating metal bath.
  • Chromium and molybdenum are very effective in retarding the transformation of austenite and in separating the ferrito- pearlitic and bainitic transformation domains, ferrito- pearlitic transformation occurring at higher temperatures than bainitic transformation.
  • These transformation domains are in the form of two distinct "noses" in an isothermal transformation diagram TTT (Transformation-Temperature-Time) from the austenite, which allows the implementation of the method according to the invention.
  • the chromium content of the steel must be between 1.8% and 4% by weight in order for its delay effect on the transformation of the austenite to be sufficient.
  • the chromium content of the steel takes into account the content of other elements that increase the quenchability such as manganese and molybdenum: in fact, given the respective effects of manganese, chromium and molybdenum on the transformations from the austenite, a combined addition of these elements must be carried out respecting the following condition, the respectively noted quantities (Mn) (Cr) (Mo) being expressed in percentage by weight: 2.7% ⁇ 0.5 (Mn) + (Cr) 3 (MB) ⁇ 5,7%.
  • the molybdenum content must not exceed 2% because of its excessive cost.
  • the aluminum content of the steel according to the invention is not less than 0.005% so as to obtain sufficient deoxidation of the steel in the liquid state.
  • the aluminum content is greater than 0.1% by weight, casting problems can occur. It is also possible to form inclusions of alumina in too large a quantity or size which play a detrimental role on the tenacity:
  • the sulfur and phosphorus contents of the steel are respectively limited to 0.05 and 0.1% in order to avoid a reduction in the ductility or toughness of the parts or sheets produced according to the invention.
  • the steel may optionally contain niobium and / or titanium, which makes it possible to refine further refinement of the grain. Due to the heat curing these additions confer, they must however be limited to 0.050% for niobium and between 0.01 and 0.1% for titanium so as not to increase the forces during hot rolling. .
  • the steel can also contain boron: indeed, the significant deformation of the austenite can accelerate the conversion to ferrite on cooling, a phenomenon that should be avoided. Addition of boron in an amount of between 0.0005 and 0.005% by weight makes it possible to guard against early ferritic transformation.
  • the steel may also contain calcium in an amount between 0.0005 and 0.005%: by combining with oxygen and sulfur, calcium prevents the formation of large inclusions, harmful to the ductility of the sheets or parts thus manufactured.
  • the rest of the composition of the steel consists of iron and unavoidable impurities resulting from the elaboration.
  • the sheets or steel parts manufactured according to the invention are characterized by a totally slab martensite structure of great fineness: due to the specific thermomechanical cycle and composition, the average size of the martensitic slats is less than 1 micrometer and their average elongation factor is between 2 and 5.
  • These microstructural characteristics are determined for example by observing the microstructure by scanning electron microscopy using a field effect gun ("MEB-FEG” technique) at a magnification higher than 1200x, coupled to an EBSD detector ("Electron Backscatter Diffraction"). It is defined that two contiguous slats are distinct when their disorientation is greater than 5 degrees.
  • the average slat size is defined by the intercepts method known per se: the mean size of the intercepted slats is evaluated by randomly defined lines with respect to the microstructure. The measurement is performed on at least 1000 martensitic slats in order to obtain a representative average value.
  • the morphology of the individual slats is determined by image analysis using known software in themselves: the maximum I max and minimum I min dimension of each martensitic slat and its elongation factor are determined. l max l min . In order to be statistically representative, this observation concerns at least 1000 martensitic slats.
  • the average elongation factor l max ⁇ l min is then determined for all of these slats observed.
  • the method according to the invention makes it possible to manufacture either rolled sheets or hot-stamped or heat-formed parts. These two modes will be successively exposed.
  • the cumulative reduction rate of the various stages of rolling at roughing is noted ⁇ a .
  • e ia denotes the thickness of the semi-finished product before the hot rolling of roughing
  • e fa the thickness of the sheet after this rolling
  • the reduction rate cumulated by ⁇ at Ln e ia e f at .
  • the cumulative reduction ratio ⁇ a during the rough rolling must be greater than 30%. Under these conditions, the austenite obtained is completely recrystallized with an average grain size of less than 40 micrometers or even 5 microns when the strain ⁇ a is greater than 200% and when the temperature T 2 is between 950 and 880 ° C. .
  • the sheet is then not completely cooled, that is to say up to an intermediate temperature T 3 , so as to avoid transformation of the austenite, at a speed V R1 greater than 2 ° C./s up to a temperature T 3 between 600 ° C and 400 ° C, temperature range in which the austenite is metastable, that is to say in a field where it should not be present under conditions of thermodynamic equilibrium.
  • a finishing hot rolling is then carried out at the temperature T 3 , the cumulative reduction ratio ⁇ b being greater than 30%. Under these conditions, a plastically deformed austenitic structure is obtained in which no action is taken. recrystallization.
  • the sheet is then cooled at a speed V R2 greater than the critical martensitic quenching speed.
  • the invention is not limited to this geometry and to this type of products, and can be used for the manufacture of long products, bars, profiles, by successive stages of hot deformation.
  • This flat blank is obtained by cutting a sheet or a coil in a form related to the final geometry of the target part.
  • This blank may be uncoated or optionally pre-coated.
  • the pre-coating may be aluminum or an aluminum-based alloy.
  • the sheet may advantageously be obtained by continuously dipping in a bath of aluminum-silicon alloy comprising by weight 5-11% of silicon, 2 to 4% of iron, optionally between 15 and 30 ppm of calcium, the rest being aluminum and unavoidable impurities resulting from the elaboration.
  • the blank may also be pre-coated with zinc or a zinc-based alloy.
  • the pre-coating may be in particular of the type galvanized with continuous dipping ("GI”) or galvanized-alloyed ("GA")
  • the blank is heated to a temperature T 1 between A c3 and A c3 + 250 ° C.
  • the heating is preferably carried out in an oven under ordinary atmosphere; during this step, an alloying between the steel and the precoat is observed.
  • the alloyed coating protects the underlying steel from oxidation and decarburization and is suitable for subsequent hot deformation.
  • We keep the blank the temperature T 1 to ensure the homogeneity of the temperature within it.
  • the holding time at the temperature T 1 varies from 30 seconds to 5 minutes.
  • the blank is stamped or shaped at a temperature T 3 of between 400 and 600 ° C., this hot deformation can be carried out in a single step or in several successive steps, as in the case of the mentioned roll-forming. above. Starting from an initial flat blank, the stamping makes it possible to obtain a part whose shape is not developable. Regardless of the hot layout mode, the cumulative deformation ⁇ c must be greater than 30% so as to obtain a non-recrystallized deformed austenite.
  • the hot forming mode is chosen so that the condition ⁇ c > 30% is satisfied anywhere in the formed part.
  • the workpiece After hot deformation, the workpiece is cooled at a speed V R2 greater than the critical speed of martensitic quenching so as to obtain a totally martensitic structure.
  • this cooling can be achieved by maintaining the piece in the tool with close contact therewith.
  • This cooling by thermal conduction can be accelerated by cooling the stamping tool, for example through channels machined in the tool for the circulation of a refrigerant.
  • the hot stamping process of the invention differs from the usual process of starting hot stamping as soon as the blank has been positioned in the press.
  • the flow limit of the steel is the lowest at high temperature and the forces required by the press are the lowest.
  • the method according to the invention consists in observing a waiting time so that the blank reaches a temperature range suitable for the ausforming, then hot stamping the blank at a significantly lower temperature than in the usual process.
  • the stamping force required by the press is slightly higher but the final structure obtained thinner than in the usual process leads to greater mechanical properties of yield strength, strength and stability. ductility. To meet a specification corresponding to a given level of stress, it is therefore possible to reduce the thickness of the blanks and thereby reduce the stamping force of the parts according to the invention.
  • the hot deformation immediately after stamping must be limited, this high temperature deformation tending to favor the formation of ferrite in the most deformed areas, which is sought to avoid.
  • the method according to the invention does not include this limitation.
  • the sheets or the steel parts may be used as such or subjected to a heat treatment of tempering, carried out at a temperature T 4 of between 150 and 600 ° C. for a period of time. between 5 and 30 minutes.
  • This treatment of income has the effect of increasing the ductility at the price of a decrease in yield strength and strength.
  • the inventors have, however, demonstrated that the process according to the invention, which gives a tensile strength Rm of at least 50 MPa higher than that obtained after conventional quenching, retained this advantage, even after treatment of tempering with temperatures. ranging from 150 to 600 ° C.
  • the fineness characteristics of the microstructure are preserved by this treatment of income, the average size of slats being less than 1.2 micrometer, the average elongation factor of slats being between 2 and 5.
  • Steel semi-finished products have been supplied whose compositions, expressed in contents by weight (%), are as follows: Steel VS mn Yes Cr MB al S P Nb Ti B 0.5Mn + Cr + 3MB AT 0.195 1,945 0.01 1,909 0.05 003 0,003 0.02 0.01 0.012 0.0014 3.03 B 0.24 1.99 0.01 1.86 0,008 0027 0,003 0.02 0,008 - - 2.88
  • the microstructure of the Scanning Electron Microscopy plates was also observed using a field effect gun (MEB-FEG technique) and EBSD detector and quantified the average size. slats of the martensitic structure and their average elongation factor l max ⁇ l min .
  • Tests A1 and A2 designate tests carried out on the composition of steel A under two different conditions, the test B1 was made from the composition of steel B. Test conditions and mechanical results obtained Trial Temperature T 3 (° C) Re (MPa) Rm (MPa) AT (%) 3220% C + 908 (MPa) ⁇ Rm (MPa) Average size of slats ( ⁇ m) Invention A1 550 1588 1889 5.9 1536 353 0.9 3 B1 550 1572 1986 6.5 1681 306 0.8 4 Reference A2 Without 1223 1576 6.9 1536 40 2 7 Underlined values: not in accordance with the invention
  • figure 1 shows the microstructure obtained in the case of test A1.
  • figure 2 shows the microstructure of the same steel simply heated to 1250 ° C., held for 30 minutes at this temperature and then quenched with water (test A2).
  • the process according to the invention makes it possible to obtain a martensite with a significantly greater average slat size. thin and less elongated than in the reference structure.
  • the values of ⁇ Rm are 353 and 306 MPa respectively.
  • the method according to the invention therefore makes it possible to obtain mechanical strength values that are clearly higher than those which would be obtained by a simple martensitic quenching.
  • This increase in strength (353 or 306 MPa) is equivalent to that which would be obtained from equation (1) by simple martensitic quenching applied to steels in which an additional addition of 0.11% or 0.09 about% would have been achieved.
  • the carbon-based process would have adverse consequences with respect to weldability and toughness, whereas the process according to the invention makes it possible to achieve very high values of mechanical strength without these disadvantages.
  • the sheets manufactured according to the invention because of their lower carbon content, have good weldability by conventional methods, in particular spot resistance welding.
  • the figure 3 shows the microstructure obtained in condition B3 according to the invention, characterized by a very thin slat size (0.9 micrometer) and a low elongation factor.
  • the invention allows the manufacture of sheets, or bare or coated parts, with very high mechanical characteristics, under very satisfactory economic conditions.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Crystallography & Structural Chemistry (AREA)
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  • Thermal Sciences (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
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EP12724656.9A 2011-05-12 2012-04-20 Procede de fabrication d'acier martensitique a tres haute resistance et tôle ou piece ainsi obtenue Active EP2707513B1 (fr)

Priority Applications (1)

Application Number Priority Date Filing Date Title
PL12724656T PL2707513T3 (pl) 2011-05-12 2012-04-20 Sposób wytwarzania stali martenzytycznej o bardzo wysokiej wytrzymałości i blacha lub część tak otrzymane

Applications Claiming Priority (2)

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PCT/FR2011/000294 WO2012153008A1 (fr) 2011-05-12 2011-05-12 Procede de fabrication d'acier martensitique a tres haute resistance et tole ou piece ainsi obtenue
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CN103562417B (zh) 2015-07-29
CA2835533A1 (fr) 2012-11-15
KR20140019838A (ko) 2014-02-17
CA2835533C (fr) 2018-12-04
HUE031878T2 (en) 2017-08-28
EP2707513A1 (fr) 2014-03-19
KR101590689B1 (ko) 2016-02-01
UA113628C2 (xx) 2017-02-27
PL2707513T3 (pl) 2017-04-28
MX2013013220A (es) 2014-06-23
KR20150095949A (ko) 2015-08-21
BR122018069395B1 (pt) 2019-04-24
ZA201309348B (en) 2014-07-30
JP2014517149A (ja) 2014-07-17
ES2612514T3 (es) 2017-05-17
RU2013155181A (ru) 2015-06-20
JP6114261B2 (ja) 2017-04-12
RU2580578C2 (ru) 2016-04-10
US20140076470A1 (en) 2014-03-20
US10337090B2 (en) 2019-07-02
MA35058B1 (fr) 2014-04-03
WO2012153012A1 (fr) 2012-11-15
MX359665B (es) 2018-10-05
CN103562417A (zh) 2014-02-05
BR112013028931B1 (pt) 2019-03-06
US20190226060A1 (en) 2019-07-25
WO2012153008A1 (fr) 2012-11-15
BR112013028931A2 (pt) 2017-02-07

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