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US20170253941A1 - Method for Fabricating Steel Sheet for Press Hardening, and Parts Obtained by this Method - Google Patents

Method for Fabricating Steel Sheet for Press Hardening, and Parts Obtained by this Method Download PDF

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Publication number
US20170253941A1
US20170253941A1 US15/500,090 US201515500090A US2017253941A1 US 20170253941 A1 US20170253941 A1 US 20170253941A1 US 201515500090 A US201515500090 A US 201515500090A US 2017253941 A1 US2017253941 A1 US 2017253941A1
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United States
Prior art keywords
sheet
temperature
hot
content
steel
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US15/500,090
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English (en)
Inventor
Sebastian Cobo
Juan David Puerta Velasquez
Martin Beauvais
Catherine Vinci
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ArcelorMittal SA
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ArcelorMittal SA
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Application filed by ArcelorMittal SA filed Critical ArcelorMittal SA
Assigned to ARCELORMITTAL reassignment ARCELORMITTAL ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: PUERTA VELASQUEZ, Juan David, Vinci, Catherine, BEAUVAIS, MARTIN, COBO, SEBASTIAN
Publication of US20170253941A1 publication Critical patent/US20170253941A1/en
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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
    • C21D9/0068—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for particular articles not mentioned below
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D22/00—Shaping without cutting, by stamping, spinning, or deep-drawing
    • B21D22/02—Stamping using rigid devices or tools
    • B21D22/022—Stamping using rigid devices or tools by heating the blank or stamping associated with 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/06—Surface hardening
    • C—CHEMISTRY; METALLURGY
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    • 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
    • C—CHEMISTRY; METALLURGY
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    • 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
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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    • 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
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    • C21D8/0273—Final recrystallisation annealing
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    • 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
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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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite
    • 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
    • C21D2211/009—Pearlite

Definitions

  • the invention relates to a fabrication method for steel sheets intended to yield very high strength mechanical parts after press hardening.
  • hardening by quenching in press consists of heating steel blanks at a sufficiently high temperature to obtain an austenitic transformation, and then hot stamping the blanks by keeping them within the press tool so as to obtain quenched microstructures.
  • a cold pre-stamping can be done on the blanks in advance before heating and press hardening.
  • These blanks can be precoated, for example with aluminum or zinc alloy.
  • the precoating alloys with the steel substrate by diffusion so as to create a compound providing surface protection of the part against decarburizing and formation of scale. This compound is suited for hot forming.
  • the resulting parts are in particular used as structural elements in automotive vehicles for providing anti-intrusion or energy absorption functions.
  • automotive vehicles for providing anti-intrusion or energy absorption functions.
  • the following can be cited as implementation examples: bumper crossbeams, door or center pillar reinforcements or frame rails.
  • press hardened parts can also be used for example for fabricating tools or parts for agricultural machines.
  • the mechanical strength can reach a higher or lower level.
  • the publication EP 2,137,327 discloses a steel composition containing: 0.040% ⁇ C ⁇ 0.100%, 0.80% ⁇ Mn ⁇ 2.00%, Si ⁇ 0.30%, S ⁇ 0.005%, P ⁇ 0.030%, 0.010% ⁇ Al ⁇ 0.070%, 0.015% ⁇ Nb ⁇ 0.100%, 0.030% ⁇ Ti ⁇ 0.080%, N ⁇ 0.009%, Cu, Ni, Mo ⁇ 0.100%, Ca ⁇ 0.006%, with which a tensile mechanical strength Rm of over 500 MPa can be obtained after press hardening.
  • the publication FR 2,780,984 discloses a greater strength level being obtained: a steel sheet containing 0.15% ⁇ C ⁇ 0.5%, 0.5% ⁇ Mn ⁇ 3%, 0.1% ⁇ Si ⁇ 0.5%, 0.01% ⁇ Cr ⁇ 1%, Ti ⁇ 0.2%, Al and P ⁇ 0.1%, S ⁇ 0.05%, 0.0005% ⁇ B ⁇ 0.08% enables a strength Rm over 1000 even over 1500 MPa to be obtained.
  • quench-promoting and/or hardening elements in larger quantities can have consequences during thermomechanical treatment for fabrication because a variation of some parameters (end of rolling temperature, coiling temperature, variation of cooling speed over the width of the rolled strip) may lead to a variation of the mechanical properties within the sheet.
  • a steel composition less sensitive to a variation of certain fabrication parameters is therefore sought so as to fabricate a sheet having good mechanical property homogeneity.
  • a steel composition is also sought which can be easily coated, in particular through hot-dip, such that the sheet can be available in different forms: uncoated, or coated with aluminum alloy or zinc alloy depending on end-user specifications.
  • a process is also sought that provides a sheet having good suitability for the mechanical cutting step in order to obtain blanks intended for press hardening, i.e., whose mechanical strength would not be too high at that stage in order to avoid breakdown of the cutting or punching tools.
  • a goal of the present invention is to resolve all of the problems discussed above by means of an economical fabrication method.
  • present invention provides a rolled steel sheet, for press hardening, for which the chemical composition comprises, with contents expressed by weight: 0.24% ⁇ C ⁇ 0.38%, 0.40% ⁇ Mn ⁇ 3%, 0.10% ⁇ Si ⁇ 0.70%, 0.015% ⁇ Al ⁇ 0.070%, 0% ⁇ Cr ⁇ 2%, 0.25% ⁇ Ni ⁇ 2%, 0.015% ⁇ Ti ⁇ 0.10%, 0% ⁇ Nb ⁇ 0.060%, 0.0005% ⁇ B ⁇ 0.0040%, 0.003% ⁇ N ⁇ 0.010%, 0.0001% ⁇ S ⁇ 0.005%, 0.0001% ⁇ P ⁇ 0.025%, with it being understood that the titanium and nitrogen content satisfy: Ti/N>3.42, and that the carbon, manganese, chromium and silicon content satisfy:
  • the chemical composition optionally comprising one or more of the following elements: 0.05% ⁇ Mo ⁇ 0.65%, 0.001% ⁇ W ⁇ 0.30%, 0.0005% ⁇ Ca ⁇ 0.005%, with the remainder made up of iron and inevitable impurities coming from preparation, the sheet containing a nickel content Ni surf at any point of the steel near the surface of said sheet over a depth ⁇ , such that Ni surf >Ni nom , where Ni nom designates the nominal nickel content of the steel, and such that Ni max designates the maximum nickel content within ⁇ :
  • the composition of the sheet comprises, by weight: 0.32% ⁇ C ⁇ 0.36%, 0.40% ⁇ Mn ⁇ 0.80%, 0.05% ⁇ Cr ⁇ 1.20%.
  • the composition of the sheet comprises, by weight: 0.24% ⁇ C ⁇ 0.28%, 1.50% ⁇ Mn ⁇ 3%.
  • the silicon content of the sheet is preferably such that: 0.50% ⁇ Si ⁇ 0.60%.
  • the composition comprises, by weight: 0.30% ⁇ Cr ⁇ 0.50%.
  • the composition of the sheet comprises, by weight: 0.30% ⁇ Ni s 1.20%, and very preferably: 0.30% ⁇ Ni ⁇ 0.50%.
  • the titanium content is preferably such that: 0.020% ⁇ Ti.
  • composition of the sheet advantageously comprises: 0.020% ⁇ Ti ⁇ 0.040%.
  • the composition comprises, by weight: 0.15% ⁇ Mo ⁇ 0.25%.
  • the composition preferably comprises by weight: 0.010% ⁇ Nb ⁇ 0.060%, and very preferably: 0.030% ⁇ Nb ⁇ 0.050%.
  • the composition comprises, by weight: 0.50% ⁇ Mn ⁇ 0.70%.
  • the microstructure of the steel sheet is ferritic-pearlitic.
  • the steel sheet is a hot rolled sheet.
  • the sheet is a hot rolled and annealed sheet.
  • the steel sheet is precoated with a metal layer of aluminum or aluminum alloy or aluminum-based alloy.
  • the steel sheet is precoated with a metal layer of zinc or zinc alloy or zinc-based alloy.
  • the steel sheet is precoated with one coat or several coats of inter-metallic alloys containing aluminum and iron and possibly silicon, where the precoating does not contain free aluminum, of phase ⁇ 5 of type Fe 3 Si 2 Al 12 , and ⁇ 6 of type Fe 2 Si 2 Al 9 .
  • the present invention also provides a part obtained by press hardening of a steel sheet of composition according to any one of the modes above with martensitic or martensitic-bainitic structure.
  • the press hardened part contains a nominal nickel content Ni nom , in which the nickel content Ni surf in the steel near the surface is greater than Ni nom over a depth ⁇ , and in that, Ni max designating the maximum nickel content within ⁇
  • the press hardened part has a mechanical strength Rm greater than or equal to 1800 MPa.
  • the press hardened part is coated with an aluminum or aluminum-based alloy, or a zinc or zinc-based alloy, resulting from the diffusion between the steel substrate and the precoating during the thermal treatment of press hardening.
  • the present invention also provides a fabrication method for a hot rolled steel sheet comprising the successive steps according to which an intermediate product with chemical composition according to the one of the embodiments presented above is cast, and then reheated to a temperature between 1250° C. and 1300° C. for a hold time at this temperature between 20 and 45 minutes.
  • the intermediate product is hot rolled until an end of rolling temperature, ERT, between 825° C. and 950° C. in order to obtain a heat rolled sheet, and then the hot rolled sheet is coiled at a temperature between 500° C. and 750° C. in order to obtain a hot rolled and coiled, and then the oxide layer formed during the preceding steps is removed by pickling.
  • the present invention further provides a fabrication method for cold rolled and annealed sheet, characterized in that it comprises the successive steps according to which a hot rolled sheet is supplied, coiled and pickled, fabricated by the method described above and then this hot rolled, coiled and pickled sheet is cold rolled in order to obtain a cold rolled sheet.
  • This cold rolled sheet is annealed at a temperature between 740° C. and 820° C. in order to obtain a cold rolled and annealed sheet.
  • a rolled sheet fabricated according to one of the above methods is supplied and then a continuous precoating is performed by hot-dip, where the precoating is aluminum or an aluminum or aluminum-based alloy, or zinc or a zinc or zinc-based alloy.
  • the present invention even further provides a fabrication method for a precoated and pre-alloyed sheet according to which a sheet rolled according to one of the above methods is supplied and then a continuous hot-dip precoating is performed with an aluminum or aluminum-based alloy and then a thermal pretreatment of the precoated sheet is done at a temperature ⁇ 1 between 620 and 680° C. for a hold time t 1 between 6 and 15 hours, such that the pre-coating no longer contains free aluminum of phase ⁇ 5 of type Fe 3 Si 2 Al 12 , and ⁇ 6 of type Fe 2 Si 2 Al 9 , and such that an austenitic transformation is not caused in the steel substrate, where the pretreatment is done in a furnace under hydrogen and nitrogen atmosphere.
  • An the present invention also provides a fabrication method for a press hardened part comprising successive steps according to which a sheet fabricated by a method according to one of the modes above is supplied and then said sheet is cut in order to obtain a blank and then an optional step of deformation by cold stamping is performed on the blank.
  • the blank is heated to a temperature comprised between 810° C. and 950° C. in order to get a fully austenitic structure in the steel and then the blank is transferred inside a press.
  • the blank is hot stamped in order to obtain a part and then it is held inside the press in order to obtain a hardening by martensitic transformation of the austenitic structure.
  • An the present invention provides for the use of a press hardened part comprising the characteristics presented above or fabricated according to the method presented above for the fabrication of structural or reinforcing parts for vehicles.
  • FIG. 1 shows schematically the variation of nickel content near the surface of the press hardened sheets or parts and illustrates certain parameters defining the invention: Ni max , Ni surf , Ni nom and ⁇ .
  • FIG. 2 shows the mechanical strength of hot stamped and press hardened parts as a function of a parameter combining the C, Mn, Cr and Si contents of the sheets.
  • FIG. 3 shows the diffusible hydrogen content measured on hot stamped and press hardened parts as a function of a parameter expressing the total nickel content near the surface of the sheets.
  • FIG. 4 shows the diffusible hydrogen content measured on hot stamped and press hardened parts as a function of a parameter expressing the amount of enrichment with nickel in the surface layer of the sheets.
  • FIG. 5 shows the variation in nickel content near the surface of sheets having different compositions.
  • FIG. 6 shows the variation in nickel content near the surface of sheets of identical composition that have undergone two modes of surface preparation before press hardening.
  • FIG. 7 shows the variation of diffusible hydrogen content as a function of the amount of nickel enrichment in the surface layer, for sheets that have undergone two surface preparation modes before press hardening.
  • FIGS. 8 and 9 show the structures of hot rolled sheets according to the invention.
  • the thickness of the sheet metal implemented in the method according to the invention is preferably comprised between 0.5 mm and 4 mm, a thickness range notably used in the fabrication of structural or reinforcing parts for the automotive industry. This can be obtained by hot rolling or be the subject of a subsequent cold rolling and an annealing. This thickness range is suited to industrial press hardening tools, in particular hot stamping presses.
  • the steel contains the following elements, with the composition expressed by weight.
  • a carbon content comprising between 0.24% and 0.38%. This element plays a major role in the quenchability and the mechanical strength obtained after the cooling which follows the austenitization treatment. Below a content of 0.24% by weight, the 1800 MPa mechanical strength level cannot be reached after hardening by tempering in press, without further addition of costly elements. Above a content of 0.38% by weight, the risk of delayed cracking is increased and the ductile/brittle transition temperature, measured with Charpy type notched flexion tests, becomes greater than ⁇ 40° C., which is seen as a too significant reduction of the toughness.
  • the targeted properties can be obtained stably while keeping the weldability at a satisfactory level and limiting the production costs.
  • the suitability for spot welding is particularly good when the carbon content is comprised between 0.24% and 0.28%.
  • the carbon content must also be defined in conjunction with the manganese, chromium and silicon contents.
  • manganese plays a role in the quenchability: the content thereof must be greater than 0.40% by weight to obtain a sufficiently low transformation start temperature Ms (austenite ⁇ martensite) during cooling in press, which makes it possible to increase the strength Rm.
  • Ms austenite ⁇ martensite
  • An increased resistance to delayed cracking can be obtained by limiting the manganese content to 3%.
  • manganese segregates to the austenitic grain boundaries and increases the risk of intergranular rupture in the presence of hydrogen.
  • the resistance to delayed cracking comes in particular from the presence of a nickel enriched surface layer.
  • the manganese content is preferably defined jointly with the carbon and possibly chromium content:
  • the carbon content comprises between 0.32% and 0.36% by weight, with a manganese content comprising between 0.40% and 0.80% and a chromium content comprising between 0.05% and 1.20%, an excellent resistance to delayed cracking because of the presence of a particularly effective nickel enriched surface layer and simultaneously a very good suitability for mechanical cutting of the sheets can be obtained.
  • the manganese content ideally comprises between 0.50% and 0.70% to conciliate the obtention of high mechanical strength and resistance to delayed cracking.
  • the carbon content comprises between 0.24% and 0.28% combined with a manganese content comprising between 1.50% and 3% the suitability for spot welding is particularly good.
  • composition ranges make it possible to obtain a cooling transformation (austenite ⁇ martensite) start temperature Ms comprised between about 320° C. and 370° C. and in this way it can be guaranteed that the heat hardened parts have a sufficiently high strength.
  • the silicon content of the steel must comprise between 0.10% and 0.70% by weight: with a silicon content over 0.10%, an additional hardening can be obtained and the silicon contributes to the deoxidation of the liquid steel.
  • the content thereof must however be limited to 0.70% in order to avoid the excessive formation of surface oxides during reheating and/or annealing steps and to not impair the hot-dip coatability.
  • the silicon content is preferably over 0.50% in order to avoid a softening of the fresh martensite, which can occur when the part is held in the press tool after the martensitic transformation.
  • the silicon content is preferably below 0.60% in order that the heating transformation temperature Ac3 (ferrite+pearlite ⁇ austenite) not be too high. Otherwise, this requires reheating the blanks to a higher temperature before hot stamping, which reduces the productivity of the method.
  • aluminum is an element enabling deoxidation in the liquid metal during elaboration, and the precipitation of nitrogen.
  • its content is over 0.070%, it can form coarse aluminates during steel-making which tend to reduce the ductility.
  • the content thereof is comprised between 0.020% and 0.060%.
  • Chromium increases the quenchability and contributes to the obtention of the Rm level desired after press hardening. Above a content equal to 2% by weight, the effect of chromium on the homogeneity of the mechanical properties in the press hardened part is saturated. At a quantity preferably comprised between 0.05% and 1.20%, this element contributes to increasing the strength. Preferably, the desired effects on the mechanical strength and delayed cracking can be obtained by adding chromium comprised between 0.30% and 0.50% while limiting the additional cost. When the manganese content is sufficient, i.e., comprised between 1.50% and 3% manganese, the addition of chromium is considered optional because the quenchability obtained through the manganese is considered sufficient.
  • FIG. 2 shows the mechanical strength of the press hardened blanks for different steel compositions with variable contents of carbon (between 0.22% and 0.36%), manganese (between 0.4% and 2.6%), chromium (between 0% and 1.3%) and silicon (between 0.1% and 0.72%) as a function of the parameter
  • the data shown in FIG. 2 relate to heated blanks in the austenitic domain at a temperature of 850° C. or 900° C. held at this temperature for 150 seconds and then hot stamped and quenched by holding in the tool.
  • the straight line 1 designates the lower envelope of the mechanical strength results.
  • a minimum value of 1800 MPa is obtained when the parameter P 1 is greater than 1.1%.
  • the Ms transformation temperature during press cooling is below 365° C. Under these conditions, the self-tempered martensite fraction, under the effect of holding in the press tool, is extremely limited, so that the very high quantity of untempered martensite allows a high mechanical strength value to be obtained.
  • Titanium has a high affinity for nitrogen. Considering the nitrogen content of the steels of the invention, the titanium content must be greater than or equal to 0.015% so as to obtain an effective precipitation. At quantities over 0.020% by weight, the titanium protects the boron such that this element is found in a free form for playing its full effect on the quenchability. The content thereof must be greater than 3.42 N, where this quantity is defined by the stoichiometry of the TiN precipitation so as to avoid the presence of free nitrogen. Beyond 0.10%, there is however a risk of forming course titanium nitrides in the liquid steel which play a harmful role on the toughness. The titanium content is preferably comprised between 0.020% and 0.040%, so as to create fine nitrides which limit the growth of austenitic grains during reheating of the blanks prior to hot stamping.
  • niobium forms niobium carbonitrides which may also limit the growth of austenitic grains during reheating of the blanks.
  • the content thereof must however be limited 0.060% because of its capacity to limit recrystallization during hot rolling which increases the rolling forces and the fabrication difficulty. The optimum effects are obtained when the niobium content is comprised between 0.030% and 0.050%.
  • a nitrogen content over 0.003% makes it possible to obtain precipitation of TiN, Nb(CN) or (Ti, Nb)(CN) mentioned above in order to limit the growth of the austenitic grain.
  • the content must however be limited to 0.010% so as to avoid the formation of coarse precipitates.
  • the sheet may contain molybdenum in a quantity comprised between 0.05% and 0.65% by weight: this element forms a co-precipitate with niobium and titanium. These precipitates are thermally very stable, strengthening the limitation of the growth of the austenitic grain on heating. An optimal effect is obtained for a molybdenum content comprised between 0.15% and 0.25%.
  • the steel can also comprise tungsten in a quantity comprised between 0.001% and 0.30% by weight.
  • this element increases the quenchability and the hardenability because of the formation of carbides.
  • the steel may also contain calcium in a quantity comprised between 0.0005% and 0.005% by combining with oxygen and sulfur, the calcium makes it possible to avoid the formation of large-size inclusions which negatively affect the ductility of the sheets or parts fabricated in that way.
  • the phosphorus content is comprised between 0.001% and 0.025% by weight. At an excessive content, this element segregates into the joints of the austenitic grains and increases the risk of delayed cracking by intergranular rupture.
  • Nickel is an important element of the invention: in fact, the inventors have shown that this element, in a quantity comprised between 0.25% and 2% by weight, very substantially reduces the sensitivity to delayed fracture when it is located concentrated at the surface of the sheet or parts in a specific form.
  • FIG. 1 schematically shows some characteristic parameters of the invention: the variation of the nickel content of a steel near the surface of the sheet, for which a surface enrichment was noted, is presented.
  • the steel has a nominal nickel content Ni nom . Due to the fabrication method which will be described later, the steel sheet is enriched with nickel in the area of its surface, up to a maximum Ni max . This maximum Ni max can be found at the surface of the sheet, as shown in FIG. 1 , or slightly under this surface, a few tens or hundreds of nanometers therebelow, without that changing the following description and the results of the invention. Similarly, the variation in the nickel content may not be linear, as shown schematically in FIG. 1 , but adopt a characteristic profile resulting from diffusion phenomena.
  • the nickel enriched surface zone is therefore characterized by the fact that in any point, the local nickel content Ni surf of the steel is such that: Ni surf >Ni nom .
  • This enriched zone has a depth ⁇ .
  • This first parameter describes the overall nickel content in the enriched layer ⁇ and corresponds to the hashed area shown in FIG. 1 .
  • the second parameter P 3 is defined by:
  • This second parameter describes the average nickel content gradient, i.e., the amount of enrichment within the layer ⁇ .
  • this method provides steel blanks, whether bare or precoated with a metal coating (aluminum or aluminum alloy, or zinc or zinc alloy) that are heated and next transferred into a hot stamping press.
  • a metal coating aluminum or aluminum alloy, or zinc or zinc alloy
  • water vapor possibly present in the furnace in a more or less significant quantity is adsorbed on the surface of the blank.
  • Hydrogen arising from the dissociation of the water can be dissolved in the austenitic steel substrate at high temperature.
  • the introduction of hydrogen is therefore facilitated by a furnace atmosphere with a high dewpoint, a significant austenitization temperature and a long hold time. During cooling, the solubility of the hydrogen drops sharply.
  • the coating formed by alloying between the possible metal precoating and the steel substrate forms a practically sealed barrier to hydrogen desorption.
  • a significant diffusible hydrogen content will therefore increase the risks of delayed cracking for a steel substrate with martensitic structure.
  • the inventors have therefore sought means with which to lower the diffusible hydrogen content over a hot stamped part to a very low level, i.e., less than or equal to 0.16 ppm. This level serves to guarantee that a part stressed in flexion under a stress equal to that of the yield stress of the material, for 150 hours, will not exhibit cracking.
  • FIG. 3 established for press hardened parts with strength Rm comprising between 1800 MPa and 2140 MPa shows that the diffusible hydrogen content depends on the parameter P 2 above. A diffusible hydrogen content below 0.16 ppm is obtained when
  • curve 2 corresponding to the lower envelope of the results, is shown.
  • the remainder of the composition of the steel is made up of iron and inevitable impurities resulting from elaboration.
  • This intermediate product may be in slab shape of thickness typically comprising between 200 mm and 250 mm, or thin slab shape whose typical thickness is on the order of a few tens of millimeters, or any other appropriate shape. It is brought to a temperature comprised between 1250° C. and 1300° C. and held in this temperature range for a time comprised between 20 and 45 minutes.
  • an oxide layer essentially rich in iron and manganese forms by reaction with the oxygen from the atmosphere of the furnace; in that layer the nickel solubility is very low and the nickel remains in metallic form.
  • this oxide layer In parallel with the growth of this oxide layer, nickel diffuses towards the interface between the oxide and the steel substrate thus causing the appearance of a layer enriched in nickel within the steel. At this stage, the thickness of this layer depends in particular on the nominal nickel content of the steel and the temperature and holding conditions previously defined. During the subsequent fabrication cycle, this initial enriched layer simultaneously undergoes:
  • the fabrication cycle of a hot rolled sheet typically comprises:
  • steps of hot rolling e.g., rough rolling, finishing
  • steps of hot rolling in a temperature range extending from 1250° C. to 825° C.
  • the inventors have shown that a variation of the hot rolling and coiling parameters, in the ranges defined by the invention, does not substantially modify the mechanical properties, since the process tolerated some variation within these ranges so well, without notable impact on the resulting products.
  • the hot rolled sheet whose thickness can typically be 1.5 mm to 4.5 mm, is pickled by a process known per se, which eliminates the oxide layer, such that the nickel enriched layer is located near the surface of the sheet.
  • cold rolling is done with a suitable reduction rate, for example comprised between 30% and 70% and then annealing at a temperature typically comprised between 740° C. and 820° C. so as to obtain a recrystallization of the work-hardened metal.
  • a suitable reduction rate for example comprised between 30% and 70%
  • annealing at a temperature typically comprised between 740° C. and 820° C. so as to obtain a recrystallization of the work-hardened metal.
  • the sheet can be cooled so as to obtain an uncoated sheet, or continuously hot-dip coated in a bath, using methods known per se, and finally cooled.
  • the inventors have shown that, among the fabrication steps detailed above, the step of reheating the slabs in a specific temperature range and holding time was the step that had the predominant influence on the characteristics of the nickel enriched layer on the final sheet.
  • the annealing cycle of the cold rolled sheet whether it comprises a coating step or not, has only a secondary influence on the characteristics of the nickel enriched surface layer.
  • the characteristics of the nickel enrichment of this layer are practically identical on a hot rolled sheet and on a sheet which additionally undergoes cold rolling and annealing, whether this comprises a step of hot-dip precoating or not.
  • This precoating can be aluminum, an aluminum alloy (comprising over 50% aluminum) or an aluminum-based alloy (where the aluminum is the majority constituent).
  • this precoating is an aluminum-silicon alloy comprising by weight 7% to 15% silicon, 2% to 4% iron and optionally between 15 ppm and 30 ppm calcium, the remainder being aluminum and inevitable impurities resulting from elaboration.
  • the precoating may also be an aluminum alloy containing 40% to 45% Zn, 3% to 10% Fe, 1% to 3% Si, the balance being aluminum and inevitable impurities resulting from elaboration.
  • the precoating can be an aluminum alloy, this being in intermetallic form containing iron.
  • This type of precoating is obtained by a thermal pretreatment of the sheet precoated with aluminum or aluminum alloy. This thermal pretreatment is done at a temperature ⁇ 1 during a hold time t 1 , such that the pre-coating no longer contains free aluminum of phase ⁇ 5 of type Fe 3 Si 2 Al 12 and ⁇ 6 of type Fe 2 Si 2 Al 9 and so as not to cause austenitic transformation in the steel substrate.
  • the temperature ⁇ 1 is comprised between 620° C. and 680° C.
  • the holding time t 1 is comprised between 6 and 15 hours. In this way a diffusion of the iron from the steel sheet to the aluminum or aluminum alloy is obtained.
  • This type of precoating then makes it possible to heat the blanks, before the hot stamping step, with a distinctly higher rate, which allows the high-temperature holding time during reheating of the blanks to be minimized, meaning reducing the quantity of hydrogen adsorbed during the step of heating the blanks.
  • the precoating can be galvanized or galvanized-alloyed, i.e., have a quantity of iron comprised between 7% to 12% after thermal alloying treatment performed in the in-line process immediately after the galvanization bath.
  • the precoating can also be composed of a superposition of layers deposited in successive steps, where at least one of the layers can be aluminum or an aluminum alloy.
  • the sheets are cut or punched by methods known per se so as to obtain blanks whose geometry is related to the final geometry of the stamped and press hardened part.
  • cutting sheets comprising in particular between 0.32% and 0.36% C, between 0.40% and 0.80% Mn and between 0.05% and 1.20% Cr is particularly easy because of the relatively low mechanical strength at this stage, associated with a ferritic-pearlitic microstructure.
  • These blanks are heated up to a temperature comprised between 810° C. and 950° C. so as to austenitize completely the steel substrate, hot stamped, and then held in the press tool so as to obtain a martensitic transformation.
  • the strain ratio applied during the hot stamping step can be smaller or larger according to whether a cold deformation step (stamping) has been done prior to the austenitization treatment.
  • the inventors have shown that the thermal heating cycles for press hardening, which consist of heating the blanks near the Ac3 transformation temperature, and then holding them at this temperature for several minutes, do not cause noticeable change in the nickel enriched layer.
  • the characteristics of the nickel enriched surface layer are similar on the sheet before press hardening and on the part obtained from the sheet after press hardening.
  • compositions from the invention have a lower Ac3 transformation temperature than conventional steel components, it is possible to austenitize the blanks with reduced temperatures-holding times, which serves to reduce the possible absorption of hydrogen in the heating furnaces.
  • TDA thermal desorption analysis
  • the variation of the nickel content in the steel near the surface was also measured on the sheets implemented by hot stamping using glow discharge spectroscopy (GDOES, “Glow Discharge Optical Emission Spectrometry,” a technique known per se).
  • GDOES glow discharge spectroscopy
  • Ni max , Ni surf , Ni nom and ⁇ can be defined this way.
  • the sheets A-D are particularly well-suited to cutting because of their ferritic-pearlitic structure.
  • the press hardened sheets and parts A-F have characteristics in terms of composition and nickel enhanced surface layer corresponding to the invention.
  • the examples A-D show that a composition containing in particular a C content comprised between 0.32% and 0.36%, Mn content comprised between 0.40% and 0.80%, a chromium content comprised between 0.05% and 1.20% in combination with a nominal nickel content of 0.30% to 1.20% and a specific layer enriched in this element serve to result in a strength Rm over 1950 MPa and a diffusible hydrogen content at a value less than or equal to 0.16 ppm.
  • test A shows that the nickel content can be lowered between 0.30% and 0.50% which serves to obtain satisfactory results in terms of mechanical resistance and resistance to delayed cracking under economical fabrication conditions.
  • the examples E-F show that satisfactory results can be obtained with a composition containing in particular a carbon content comprising between 0.24% and 0.28% and a manganese content comprising between 1.50% and 3%.
  • examples G-K have a diffusible hydrogen content over 0.25 ppm because the steels do not have a nickel enriched surface layer.
  • examples J-K correspond to steel compositions for which the parameter P 1 is below 1.1% such that a strength Rm of 1800 MPa is not obtained after press hardening.
  • FIG. 5 shows the nickel content as a function of depth measured compared to the surface of the sheet as measured by GDOES technique.
  • the reference letters appearing beside each curve in this figure correspond to the steel reference.
  • the sheets according to the invention have an enrichment in the surface layer.
  • a variation of the chromium content from 0.51% to 1.05% serves to preserve enrichment in the surface layer, satisfying the conditions of the invention.
  • FIG. 6 which shows the nickel content measured by glow discharge spectroscopy from the surface of the sheet F, shows that in the preparation mode X, a nickel enriched surface layer is present (curve labeled X), whereas the grinding eliminated the oxide layer and the nickel enriched sublayer (curve labeled Y).
  • Part E Diffusible Part F: Diffusible Prior preparation hydrogen content hydrogen content of the sheet (ppm) (ppm) Pickling retaining the 0.09 0.08 nickel enriched layer Grinding eliminating the 0.21 0.19 nickel enriched layer
  • FIG. 7 shows the diffusible hydrogen content as a function of the steel composition and the preparation mode.
  • the reference EX relates to the sheet and hot stamped part made from steel composition E with preparation mode X.
  • FIGS. 8 and 9 show hot rolled sheets from the tests T and V respectively. It can be seen that the ferritic-pearlitic microstructures are very similar for the two conditions.
  • the hot rolled sheets were continuously pickled so as to remove only the oxide layer formed in the prior steps while leaving the nickel enriched layer in place.
  • the sheets were next rolled to a target thickness of 1.4 mm. Whatever the hot rolling condition, the desired thickness was able to be achieved; the rolling forces being similar for the various conditions.
  • the sheets were then annealed at a temperature of 760° C., which is immediately above the Ac1 transformation temperature, and then cooled and continuously aluminated by tempering in a bath containing 9% silicon by weight, 3% iron by weight and the remainder aluminum and inevitable impurities.
  • the result is thus sheets with a coating on the order of 80 g/m 2 per surface; this coating has a very regular defect-free thickness.
  • Hot stamping parameters furnace parameters Quenching Hold Transfer Applied time in Test Dewpoint Temp. time time pressure tool condition (° C.) (° C.) (min.) (sec.) (kN) (sec.) 5 ⁇ 10 900 5 8 5500 6 6 ⁇ 10 900 15 8 5500 6
  • press hardened parts simultaneously having a very high mechanical strength and a resistance to delayed cracking can be fabricated with the invention.
  • These parts will be profitably used as structural or reinforcing parts in the field of automotive manufacturing.

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US15/500,090 2014-07-30 2015-07-29 Method for Fabricating Steel Sheet for Press Hardening, and Parts Obtained by this Method Abandoned US20170253941A1 (en)

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PCT/IB2014/001428 WO2016016676A1 (fr) 2014-07-30 2014-07-30 Procédé de fabrication de tôles d'acier, pour durcissement sous presse, et pièces obtenues par ce procédé
PCT/IB2015/001273 WO2016016707A1 (fr) 2014-07-30 2015-07-29 Procédé de fabrication de tôles d'acier pour durcissement sous presse, et pièces obtenues par ce procédé

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Family Cites Families (18)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP3375205B2 (ja) * 1994-08-29 2003-02-10 日本鋼管株式会社 耐遅れ破壊特性に優れたクラッド鋼線
FR2780984B1 (fr) 1998-07-09 2001-06-22 Lorraine Laminage Tole d'acier laminee a chaud et a froid revetue et comportant une tres haute resistance apres traitement thermique
DE50303605D1 (de) * 2002-09-13 2006-07-06 Daimler Chrysler Ag Verfahren zur herstellung eines pressgehärteten bauteils
JP3993831B2 (ja) * 2002-11-14 2007-10-17 新日本製鐵株式会社 熱間成形加工後の硬化能および衝撃特性に優れた鋼板およびその使用方法
JP4500124B2 (ja) * 2004-07-23 2010-07-14 新日本製鐵株式会社 ホットプレス用めっき鋼板の製造方法
EP1749895A1 (fr) * 2005-08-04 2007-02-07 ARCELOR France Procédé de fabrication de tôles d'acier présentant une haute résistance et une excellente ductilité, et tôles ainsi produites
EP1767659A1 (fr) 2005-09-21 2007-03-28 ARCELOR France Procédé de fabrication d'une pièce en acier de microstructure multi-phasée
FI3290199T4 (fi) * 2006-10-30 2025-11-26 Arcelormittal Pinnoitettuja teräsnauhoja ja sen käyttö, leimausaihioita valmistettu samasta, leimattuja tuotteja valmistettu samasta, valmistustuotteet jotka sisältävät tällaisen leimatun tuotteen
WO2008110670A1 (fr) 2007-03-14 2008-09-18 Arcelormittal France Acier pour formage a chaud ou trempe sous outil a ductilite amelioree
EP2143816B1 (en) * 2007-04-11 2020-02-26 Nippon Steel Corporation Hot dip plated high-strength steel sheet for press forming use excellent in low-temperature toughness and process for production thereof
JP5023871B2 (ja) * 2007-08-03 2012-09-12 住友金属工業株式会社 熱間プレス鋼板部材の製造方法
RU2362815C2 (ru) * 2007-09-12 2009-07-27 Ооо "Карат" Низколегированная сталь и изделие, выполненное из нее
EP2123786A1 (fr) * 2008-05-21 2009-11-25 ArcelorMittal France Procédé de fabrication de tôles d'aciers dual phase laminées à froid à trés haute résistance et tôles ainsi produites
WO2012127125A1 (fr) * 2011-03-24 2012-09-27 Arcelormittal Investigatión Y Desarrollo Sl Tôle d'acier laminée à chaud et procédé de fabrication associé
UA112771C2 (uk) 2011-05-10 2016-10-25 Арселормітталь Інвестігасьон І Десароло Сл Сталевий лист з високою механічною міцністю, пластичністю і формованістю, спосіб виготовлення та застосування таких листів
WO2012153008A1 (fr) * 2011-05-12 2012-11-15 Arcelormittal Investigación Y Desarrollo Sl Procede de fabrication d'acier martensitique a tres haute resistance et tole ou piece ainsi obtenue
JP5811020B2 (ja) * 2012-04-25 2015-11-11 新日鐵住金株式会社 高い靱性と高い加工性および成形性とを有し水素脆化起因による遅れ破壊特性に優れた高強度鋼板
JP5835622B2 (ja) * 2012-07-06 2015-12-24 新日鐵住金株式会社 熱間プレス鋼板部材およびその製造方法ならびに熱間プレス用鋼板

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CO2017001981A2 (es) 2017-05-19
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KR101820273B1 (ko) 2018-01-19
EP3175006A1 (fr) 2017-06-07
CA3071152A1 (fr) 2016-02-04
BR112017007999A2 (pt) 2018-02-20
PL3175006T3 (pl) 2019-08-30
US20170298465A1 (en) 2017-10-19
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US20250354239A1 (en) 2025-11-20
MX375051B (es) 2025-03-06
CA2956537C (fr) 2020-03-24
TR201908459T4 (tr) 2019-07-22
CA3071136A1 (fr) 2016-02-04
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EP3175006B1 (fr) 2019-03-06
CA2956537A1 (fr) 2016-02-04
KR20170132908A (ko) 2017-12-04
UA118298C2 (uk) 2018-12-26
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CN106574348A (zh) 2017-04-19
CA3071152C (fr) 2022-05-10
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US9845518B2 (en) 2017-12-19
JP6698128B2 (ja) 2020-05-27
WO2016016707A1 (fr) 2016-02-04
HUE043636T2 (hu) 2019-08-28
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RU2017106289A3 (ru) 2018-08-28
WO2016016676A1 (fr) 2016-02-04

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