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EP1990431A1 - Procédé de fabrication de tôles d'acier laminées à froid et recuites à très haute résistance, et tôles ainsi produites - Google Patents

Procédé de fabrication de tôles d'acier laminées à froid et recuites à très haute résistance, et tôles ainsi produites Download PDF

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Publication number
EP1990431A1
EP1990431A1 EP07290598A EP07290598A EP1990431A1 EP 1990431 A1 EP1990431 A1 EP 1990431A1 EP 07290598 A EP07290598 A EP 07290598A EP 07290598 A EP07290598 A EP 07290598A EP 1990431 A1 EP1990431 A1 EP 1990431A1
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EP
European Patent Office
Prior art keywords
steel
sheet
rolled
temperature
cold
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Withdrawn
Application number
EP07290598A
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German (de)
English (en)
French (fr)
Inventor
Javier Gilotin
Antoin Moulin
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ArcelorMittal France SA
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ArcelorMittal France SA
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First worldwide family litigation filed litigation Critical https://patents.darts-ip.com/?family=38596874&utm_source=google_patent&utm_medium=platform_link&utm_campaign=public_patent_search&patent=EP1990431(A1) "Global patent litigation dataset” by Darts-ip is licensed under a Creative Commons Attribution 4.0 International License.
Application filed by ArcelorMittal France SA filed Critical ArcelorMittal France SA
Priority to EP07290598A priority Critical patent/EP1990431A1/fr
Priority to MX2009011927A priority patent/MX2009011927A/es
Priority to CN2008800153809A priority patent/CN101765668B/zh
Priority to US12/599,166 priority patent/US20100307644A1/en
Priority to RU2009145940/02A priority patent/RU2437945C2/ru
Priority to PCT/FR2008/000609 priority patent/WO2008145871A2/fr
Priority to PL08805523.1T priority patent/PL2155915T5/pl
Priority to HUE08805523A priority patent/HUE035549T2/en
Priority to KR1020097023517A priority patent/KR101523395B1/ko
Priority to CA2686940A priority patent/CA2686940C/fr
Priority to EP08805523.1A priority patent/EP2155915B2/fr
Priority to BRPI0821572-3A priority patent/BRPI0821572B1/pt
Priority to ES08805523T priority patent/ES2655476T5/es
Priority to JP2010506964A priority patent/JP5398701B2/ja
Priority to ARP080101971A priority patent/AR066508A1/es
Publication of EP1990431A1 publication Critical patent/EP1990431A1/fr
Priority to ZA200907430A priority patent/ZA200907430B/xx
Priority to MA32328A priority patent/MA31555B1/fr
Priority to US15/243,610 priority patent/US10612106B2/en
Priority to US16/592,341 priority patent/US11414722B2/en
Priority to US17/575,300 priority patent/US20220136078A1/en
Withdrawn legal-status Critical Current

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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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/001—Continuous casting of metals, i.e. casting in indefinite lengths of specific alloys
    • 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
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • 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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • C22C38/22—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
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with 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
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • 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
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23G—CLEANING OR DE-GREASING OF METALLIC MATERIAL BY CHEMICAL METHODS OTHER THAN ELECTROLYSIS
    • C23G1/00—Cleaning or pickling metallic material with solutions or molten salts
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23G—CLEANING OR DE-GREASING OF METALLIC MATERIAL BY CHEMICAL METHODS OTHER THAN ELECTROLYSIS
    • C23G1/00—Cleaning or pickling metallic material with solutions or molten salts
    • C23G1/02—Cleaning or pickling metallic material with solutions or molten salts with acid solutions
    • C23G1/08—Iron or steel

Definitions

  • the invention relates to the manufacture of cold-rolled and annealed thin sheets of steels having a strength greater than 1200 MPa and an elongation at break greater than 8%.
  • the automotive sector and the general industry are notably fields of application for these steel sheets.
  • steels having a "TRIP" (Transformation Induced Plasticity) behavior with very advantageous combinations of properties (resistance-ability to deformation) have been developed: these properties are related to the structure of these structures.
  • multiphase steels have a predominantly bainitic structure.
  • multi-phase steel sheets of medium thickness are used with advantage for structural parts such as bumper crosspieces, uprights, various reinforcements.
  • the patent EP1559798 discloses the manufacture of steels of composition: 0.10-0.25% C, 1.0-2.0% Si, 1.5-3% Mn, the microstructure consisting of at least 60% bainitic ferrite and at least 5% residual austenite, the polygonal ferrite being less than 20%.
  • the exemplary embodiments presented in this document show that the resistance does not exceed 1200 MPa.
  • the patent EP 1589126 also discloses the manufacture of cold-rolled thin sheet, the product of which (resistance x elongation) is greater than 20000 MPa%.
  • the composition of the steels contains: 0.10-0.28% C, 1.0-2.0% Si, 1-3% Mn, less than 0.10% Nb.
  • the structure consists of more than 50% bainitic ferrite, 5 to 20% residual austenite, and less than 30% of polygonal ferrite. Again, the examples presented show that the resistance is still below 1200 MPa.
  • the present invention aims to solve the problems mentioned above. It aims to provide a cold rolled and annealed thin steel sheet having a mechanical strength greater than 1200 MPa together with an elongation greater than 8% rupture and good cold forming ability. The invention also aims at providing a steel that is not very sensitive to damage during cutting by a mechanical method.
  • the invention aims to provide a method of manufacturing thin sheets, small variations in the parameters do not lead to significant changes in the microstructure or mechanical properties.
  • the invention also aims to provide a sheet of steel easily fabricated by cold rolling, that is to say whose hardness after the hot rolling step is limited so that the rolling forces remain moderate during of the cold rolling step.
  • the subject of the invention is a cold-rolled and annealed steel sheet with a resistance greater than 1200 MPa, the composition of which comprises the contents being expressed by weight: 0.10% ⁇ C ⁇ 0.25% , 1% ⁇ Mn ⁇ 3%, Al ⁇ 0.010%, Si ⁇ 2.990%, S ⁇ 0.015%, P ⁇ 0.1%, N ⁇ 0.008%, with the proviso that 1% ⁇ Si + Al ⁇ 3%, the composition optionally comprising: 0.05% ⁇ V ⁇ 0.15%, B ⁇ 0.005%, Mo ⁇ 0.25%, Cr ⁇ 1.65%, with the proviso that Cr + (3 ⁇ Mo) ⁇ 0.3%, Ti in an amount such that Ti / N ⁇ 4 and Ti ⁇ 0.040%, the remainder of the composition consisting of iron and unavoidable impurities resulting from the elaboration, the microstructure of said steel comprising 15 to 90% of bainite, the balance consisting of martensite and residual austenite.
  • the subject of the invention is also a steel sheet of the above composition, with a resistance greater than 1400 MPa, with an elongation at break greater than 8%, characterized in that it contains: Mo ⁇ 0.25%, Cr ⁇ 1.65%, it being understood that Cr + (3 x Mo) ⁇ 0.3%, the microstructure of the steel comprising 45 to 65% of bainite, the remainder being islands of martensite and residual austenite L
  • Another subject of the invention is a steel sheet of the above composition, with a resistance greater than 1600 MPa, with an elongation at break greater than 8%, characterized in that it contains: Mo ⁇ 0.25%, Cr ⁇ 1.65%, it being understood that: Cr + (3 x Mo) ⁇ 0.3%, the microstructure of the steel comprising 15 to 45% of bainite, the remainder consisting of martensite and residual austenite.
  • the composition comprises: 0.19% ⁇ C ⁇ 0.23% According to a preferred mode, the composition comprises: 1.5% ⁇ Mn ⁇ 2.5% Preferably, the composition comprises: 1.2% ⁇ Si ⁇ 1.8% Preferably, the composition comprises: 1.2% ⁇ AI ⁇ 1.8% According to one particular embodiment, the composition comprises: 0.05% ⁇ V ⁇ 0.15% 0.004 ⁇ N ⁇ 0.008%. In a preferred embodiment, the composition comprises: 0.0005 ⁇ B ⁇ 0.003%.
  • the average size of the islands of martensite and residual austenite is less than 1 micrometer, the average distance between the islands being less than 6 microns.
  • a semi-finished product is cast from this steel, then the semi-finished product is heated to a temperature above 1150 ° C. and the semi-finished product is hot-rolled to obtain a hot-rolled sheet.
  • the sheet is reeled and stripped and then cold rolled with a reduction ratio of between 30 and 80% so as to obtain a cold-rolled sheet.
  • the cold-rolled sheet is heated at a speed V c of between 5 and 15 ° C./s up to a temperature T 1 of between Ac 3 and Ac 3 + 20 ° C., for a time t 1 of between 50 and 150 seconds. cools the sheet at a speed V R1 greater than 40 ° C / s to a temperature T 2 between (M s -30 ° C and M s + 30 ° C).
  • the sheet is maintained at said temperature T 2 for a time t 2 of between 150 and 350 seconds and then cooling is carried out at a speed V R2 of less than 30 ° C./s up to room temperature.
  • the subject of the invention is also a process for manufacturing a cold-rolled steel sheet with a resistance greater than 1200 MPa and an elongation at break greater than 8%, according to which a steel with a composition of 0.10 is supplied.
  • a semifinished product is cast from this steel, the semi-finished product is heated to a temperature above 1150 ° C., and then the semi-finished product is hot-rolled to obtain a hot-rolled sheet.
  • the sheet is reeled, the latter is scoured, then the sheet is cold-rolled with a reduction ratio of between 30 and 80% so as to obtain a cold-rolled sheet.
  • the cold-rolled sheet is heated to a speed V c of between 5 and 15 ° C / s to a temperature T 1 between Ac3 and Ac3 + 20 ° C, for a time t 1 between 50 and 150s and then cooled at a speed V R1 greater than 25 ° C / s up to a temperature T 2 between B s and (M s - 20 ° C)
  • the sheet is maintained at the temperature T 2 for a time t 2 of between 150 and 350 s and then cooling is carried out at a lower speed V R2 at 30 ° C / s to room temperature.
  • the invention also relates to the use of a cold rolled steel sheet annealed in one of the above modes, or manufactured by a method according to one of the above modes, for the manufacture structural parts or reinforcement elements, in the automotive field.
  • the inventors have demonstrated that the above problems were solved when the annealed cold-rolled thin steel sheet exhibited a bainitic microstructure, with in addition islands of martensite and residual austenite, or "M-A" islands.
  • M-A martensite and residual austenite
  • carbon plays a very important role in the formation of the microstructure and in the mechanical properties: in combination with other elements of the composition (Cr, Mo, Mn) and with the heat treatment of annealing after cold rolling, it increases the quenchability and makes it possible to obtain a bainitic transformation.
  • the carbon contents according to the invention also lead to the formation of islands of martensite and residual austenite whose quantity, morphology, composition make it possible to obtain the properties referred to above.
  • Carbon also retards the formation of pro-eutectoid ferrite after thermal annealing treatment after cold rolling: otherwise, the presence of this phase of low hardness would cause excessive local damage at the interface with the matrix whose hardness is higher. The presence of proeutectoid ferrite resulting from the annealing must therefore be avoided in order to obtain high levels of mechanical strength.
  • the carbon content is between 0.10 and 0.25% by weight: Below 0.10%, sufficient strength can not be obtained and the stability of the residual austenite is not not satisfactory. Beyond 0.25%, the weldability is reduced due to the formation of quenching microstructures in the heat-affected zone.
  • the carbon content is between 0.19 and 0.23%: within this range, the weldability is very satisfactory, and the quantity, the stability and the morphology of the islets MA are particularly adapted to obtain a favorable pair of mechanical properties (resistance-elongation)
  • an addition of manganese makes it possible to avoid the formation of proeutectoid ferrite during cooling after annealing after cold rolling.
  • Manganese also helps to deoxidize steel during liquid phase processing.
  • the addition of manganese also contributes to effective solid solution hardening and increased strength.
  • the manganese is between 1.5 and 2.5% so that these effects are obtained, and without risk of formation of harmful band structure.
  • Silicon and aluminum play an important role together according to the invention.
  • Silicon delays the precipitation of cementite during cooling from the austenite after annealing.
  • An addition of silicon according to the invention thus contributes to stabilizing a sufficient amount of residual austenite in the form of islets which subsequently and progressively transform into martensite under the effect of a deformation. Another part of the austenite is transformed directly into martensite during cooling after annealing.
  • Aluminum is a very effective element for the deoxidation of steel. As such, its content is greater than or equal to 0.010%. Like silicon, it stabilizes residual austenite.
  • the silicon content is preferably between 1.2 and 1.8% to stabilize a sufficient amount of residual austenite and to avoid intergranular oxidation during the hot winding step preceding the cold rolling. This also avoids the formation of strongly adherent oxides and the possible appearance of surface defects leading in particular to a lack of wettability in dip galvanizing operations.
  • the aluminum content is preferably between 1.2 and 1.8%.
  • the effects of aluminum are indeed similar to those described above for silicon, but the risk of occurrence of superficial defects is however less.
  • the steels according to the invention optionally comprise molybdenum and / or chromium: molybdenum increases quenchability, avoids the formation of pro-eutectoid ferrite and effectively refines the bainitic microstructure. However, a content greater than 0.25% by weight increases the risk of forming a predominantly martensitic microstructure to the detriment of bainite formation.
  • Chromium also helps to prevent the formation of pro-eutectoid ferrite and the refinement of the bainitic microstructure. Beyond 1.65%, the risk of obtaining a predominantly martensitic structure is important.
  • the chromium and molybdenum contents are such that: Cr + (3x Mo) ⁇ 0.3%.
  • the coefficients of chromium and molybdenum in this relationship reflect their influence on the quenchability, in particular the respective ability of these elements to avoid the formation of pro-eutectoid ferrite under the particular cooling conditions of the invention.
  • the steel may comprise very low or zero molybdenum and chromium contents, ie contents of less than 0.005% by weight for these two elements, and 0% boron.
  • the phosphorus content is limited to 0.1% so as to maintain sufficient hot ductility.
  • the nitrogen content is limited to 0.008% to avoid possible aging.
  • the steel according to the invention optionally contains vanadium in an amount of between 0.05 and 0.15%.
  • vanadium in an amount of between 0.05 and 0.15%.
  • the nitrogen content is between 0.004 and 0.008%, the precipitation of vanadium can occur during annealing after cold rolling in the form of fine carbonitrides which give additional hardening.
  • the steel may optionally comprise boron in an amount of less than or equal to 0.005%.
  • the steel preferentially contains between 0.0005 and 0.003% of boron, which contributes to the suppression of pro-eutectoid ferrite in the presence of chromium and / or molybdenum.
  • the addition of boron in the amount mentioned above makes it possible to obtain a resistance greater than 1400 MPa.
  • the steel may optionally comprise titanium in an amount such as Ti / N ⁇ 4 and Ti ⁇ 0.040%, which allows the formation of titanium carbonitrides and increases the hardening.
  • the rest of the composition consists of unavoidable impurities resulting from the elaboration.
  • the contents of these impurities, such as Sn, Sb, As, are less than 0.005%.
  • the microstructure of the steel is composed of 65 to 90% of bainite, these contents referring to surface percentages, the balance consists of islands of martensite and residual austenite (islets of MA compounds)
  • This bainitic structure which does not contain proeutectoid ferrite of low hardness, has an elongation capacity greater than 10%.
  • the M-A islands regularly dispersed in the matrix have an average size of less than 1 micrometer.
  • the figure 1 shows an example of microstructure of a steel sheet according to the invention.
  • the morphology of the islets MA was revealed by means of appropriate chemical reagents: after attack, the islets MA appear in white on a bainitic matrix more or less dark. Some small islands are located between the slats of bainite ferrite. The islands are observed at magnitudes ranging from 500 to 1500x on a statistically representative surface and the average size of the islands as well as the average distance between these islets is measured using an image analysis software. In the case of figure 1 , the surface percentage of the islets is 12% and the average size of the islets MA is less than 1 micrometer.
  • the microstructure is composed of 45 to 65% of bainite, the balance consisting of islands of martensite and residual austenite.
  • the microstructure is composed of 15 to 45% of bainite, the balance being consisting of martensite and residual austenite.
  • the cast semifinished products are first brought to a temperature higher than 1150 ° C. to reach at any point a temperature favorable to the high deformations which the steel will undergo during rolling.
  • 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 semi-finished product is hot-rolled.
  • An advantage of the invention is that the final characteristics and the microstructure of the cold-rolled and annealed sheet are relatively independent of the end-of-rolling temperature and the cooling after hot rolling.
  • the sheet is then reeled hot.
  • the winding temperature is preferably less than 550 ° C to limit the hardness of the hot-rolled sheet and intergranular oxidation at the surface. Too much hardness of the hot-rolled sheet leads to excessive forces during subsequent cold rolling and possibly to edge defects.
  • the hot-rolled sheet is then etched according to a method known per se in order to give the latter a surface condition suitable for cold. This is done by reducing the thickness of the hot-rolled sheet by 30 to 80%.
  • microstructural constituents measured by quantitative microscopy were also reported: surface fraction of bainite, martensite and residual austenite.
  • the tensile mechanical properties obtained were given in Table 3 below.
  • the Re / Rm ratio was also indicated.
  • the breaking energy at -40 ° C was determined from Charpy V type resilience specimens reduced to 1.4 mm thickness. Damage related to a cut (for example, shearing or punching) has also been evaluated which could possibly reduce the capacity for subsequent deformation of a cut piece. For this purpose, 20 ⁇ 80 mm 2 specimens were cut by shearing. Some of these specimens were then polished at the edges. The specimens were coated with photodeposited grids and then subjected to uniaxial traction until rupture.
  • the sheets of composition according to the invention and manufactured according to the conditions of the invention (I1-a, I2-ab, 13-a, I4, I5) have a combination particularly advantageous mechanical properties: on the one hand a mechanical strength greater than 1200 MPa, on the other hand an elongation at break always greater than or equal to 10%.
  • the steels according to the invention also have a Charpy V fracture energy at -40 ° C. of greater than 40 Joules / cm 2 . This allows the manufacture of parts resistant to the sudden propagation of a fault especially in case of dynamic stresses.
  • the microstructures of the steels with a minimum strength of 1200 MPa and a minimum breaking elongation of 10% according to the invention comprise a bainite content of between 65 and 90%, the balance consisting of MA islands.
  • the figure 1 thus presents the microstructure of the steel sheet 13a comprising 88% bainite and 12% islets MA, revealed by a LePera reagent attack.
  • the figure 2 presents this microstructure revealed by a Nital attack.
  • the steels according to the invention have a bainite content of between 45 and 65%, the balance being MA islands.
  • the steels according to the invention have a bainite content of between 15 and 35%, the balance being martensite and residual austenite.
  • the steel sheets according to the invention have an island size of less than 1 micrometer MA, the inter-island distance being less than 6 micrometers.
  • the steels according to the invention also have good resistance to damage in case of cutting since the damage factor ⁇ is limited to -23%.
  • a steel sheet that does not have these characteristics (R5) may have a 43% damage factor.
  • the sheets according to the invention have good hole expansion capability.
  • the steels according to the invention also have good weldability: for welding parameters adapted to the thicknesses mentioned above, the welded joints are free of cold or hot cracks.
  • the steel sheets I1-b and 11-c were annealed at a temperature T 1 too low, the austenitic transformation is not complete. As a result, the microstructure contains proeutectoid ferrite (40% for I1b, 20% for I1-c) and an excessive content of MA islands. The mechanical strength is then reduced by the presence of proeutectoid ferrite.
  • the holding temperature T 2 is greater than Ms + 30 ° C: the bainitic transformation which occurs at a higher temperature gives rise to a coarser structure and leads to insufficient mechanical strength.
  • the cooling rate V R1 after annealing is not sufficient, the microstructure formed is more heterogeneous and the elongation at break is reduced to less than 10%.
  • the holding temperature T 2 is less than Ms-20 ° C: consequently, the cooling V R1 causes the appearance of a bainite formed at low temperature and martensite, associated with insufficient elongation .
  • the steel R1 has an insufficient (silicon + aluminum) content, the holding temperature T 2 is less than Ms-20 ° C. Due to the insufficient content of (Si + Al), the amount of islets MA formed is insufficient to obtain a resistance greater than or equal to 1200 MPa.
  • R2 and R3 steels have insufficient carbon, manganese, silicon + aluminum contents.
  • the amount of MA compounds formed is less than 10%.
  • the annealing temperature T 1 lower than A c3 leads to an excessive content of proeutectoid ferrite and cementite, and insufficient strength.
  • the steel R4 has an insufficient content of (Si + Al)
  • the cooling rate V R1 is in particular too low.
  • the enrichment of carbon austenite during cooling is then insufficient to allow the formation of martensite and to obtain the strength and elongation properties of the invention.
  • Steel R5 also has an insufficient content of (Si + Al)
  • the insufficiently fast cooling rate after annealing leads to excessive proeutectoid ferrite content and insufficient mechanical strength.
  • the invention allows the manufacture of steel sheets combining a very high strength and high ductility.
  • the steel sheets according to the invention are used profitably for the manufacture of structural parts or reinforcement elements in the automotive field and general industry.

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EP07290598A 2007-05-11 2007-05-11 Procédé de fabrication de tôles d'acier laminées à froid et recuites à très haute résistance, et tôles ainsi produites Withdrawn EP1990431A1 (fr)

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EP07290598A EP1990431A1 (fr) 2007-05-11 2007-05-11 Procédé de fabrication de tôles d'acier laminées à froid et recuites à très haute résistance, et tôles ainsi produites
JP2010506964A JP5398701B2 (ja) 2007-05-11 2008-04-28 極めて高い強度を有する冷延焼鈍鋼板を製造するプロセスおよびこれにより製造された板
EP08805523.1A EP2155915B2 (fr) 2007-05-11 2008-04-28 Procédé de fabrication de tôles d'acier laminées à froid et recuites à très haute résistance, et tôles ainsi produites
ES08805523T ES2655476T5 (es) 2007-05-11 2008-04-28 Procedimiento de fabricación de chapas de acero laminadas en frío y recocidas con una resistencia muy alta, y chapas producidas de tal forma
US12/599,166 US20100307644A1 (en) 2007-05-11 2008-04-28 Process for manufacturing cold-rolled and annealed steel sheet with a very high strength, and sheet thus produced
RU2009145940/02A RU2437945C2 (ru) 2007-05-11 2008-04-28 Способ изготовления высокопрочных холоднокатaных и отожженных стальных листов и листы, полученные этим способом
PCT/FR2008/000609 WO2008145871A2 (fr) 2007-05-11 2008-04-28 Procede de fabrication de tôles d'acier laminees a froid et recuites a tres haute resistance, et tôles ainsi produites
PL08805523.1T PL2155915T5 (pl) 2007-05-11 2008-04-28 Sposób produkcji blach stalowych walcowanych na zimno i wyżarzanych o bardzo wysokiej wytrzymałości oraz blachy tak wytworzone
HUE08805523A HUE035549T2 (en) 2007-05-11 2008-04-28 Procedure for the manufacture of cold rolled and tempered steel sheets of very high strength and the plates thus produced
KR1020097023517A KR101523395B1 (ko) 2007-05-11 2008-04-28 고강도의 냉간 압연 및 어닐링된 강판의 제조 공정, 및 이렇게 제조된 강판
CA2686940A CA2686940C (fr) 2007-05-11 2008-04-28 Procede de fabrication de toles d'acier laminees a froid et recuites a tres haute resistance, et toles ainsi produites
MX2009011927A MX2009011927A (es) 2007-05-11 2008-04-28 Metodo para la fabricacion de chapas de acero laminadas en frio y recocidas de muy alta resistencia, y chapas asi producidas.
BRPI0821572-3A BRPI0821572B1 (pt) 2007-05-11 2008-04-28 Chapa de aço laminada a frio e recozida e processo de fabricação de chapa de aço laminada a frio e recozidas
CN2008800153809A CN101765668B (zh) 2007-05-11 2008-04-28 具有极高强度的冷轧并退火钢片材的制造方法及这样生产的片材
ARP080101971A AR066508A1 (es) 2007-05-11 2008-05-09 Un proceso para fabricar una chapa de acero recocido y laminada en frio, con una muy alta resistencia , y una chapa producida de esta manera
ZA200907430A ZA200907430B (en) 2007-05-11 2009-10-23 Process for manufacturing cold-rolled and annealed steel sheet with a very high strength, and sheet thus produced
MA32328A MA31555B1 (fr) 2007-05-11 2009-11-03 Procede de fabrication de tôles d'acier laminees a froid et recuites a tres haute resistance, et tôles ainsi produites
US15/243,610 US10612106B2 (en) 2007-05-11 2016-08-22 Process for manufacturing cold-rolled and annealed steel sheet with a very high strength, and sheet thus produced
US16/592,341 US11414722B2 (en) 2007-05-11 2019-10-03 Process for manufacturing cold-rolled and annealed steel sheet with a very high strength, and sheet thus produced
US17/575,300 US20220136078A1 (en) 2007-05-11 2022-01-13 Process for manufacturing cold-rolled and annealed steel sheet with a very high strength, and sheet thus produced

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EP08805523.1A Active EP2155915B2 (fr) 2007-05-11 2008-04-28 Procédé de fabrication de tôles d'acier laminées à froid et recuites à très haute résistance, et tôles ainsi produites

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CN (1) CN101765668B (es)
AR (1) AR066508A1 (es)
BR (1) BRPI0821572B1 (es)
CA (1) CA2686940C (es)
ES (1) ES2655476T5 (es)
HU (1) HUE035549T2 (es)
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EP1589126A1 (en) * 2004-04-22 2005-10-26 Kabushiki Kaisha Kobe Seiko Sho High-strenght cold rolled steel sheet having excellent formability and plated steel sheet

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CN101928875A (zh) * 2009-06-22 2010-12-29 鞍钢股份有限公司 具有良好成形性能的高强度冷轧钢板及其制备方法
US9809874B2 (en) 2012-04-10 2017-11-07 Nippon Steel & Sumitomo Metal Corporation Steel sheet suitable for impact absorbing member and method for its manufacture
EP2837707A4 (en) * 2012-04-10 2016-02-17 Nippon Steel & Sumitomo Metal Corp STEEL PLATE SUITABLE AS A SHOCK ABSORPTION ELEMENT AND METHOD FOR THE PRODUCTION THEREOF
US10907232B2 (en) 2014-07-03 2021-02-02 Arcelormittal Method for producing a high strength coated steel sheet having improved strength, formability and obtained sheet
US11718888B2 (en) 2014-07-03 2023-08-08 Arcelormittal Method for producing a high strength coated steel sheet having improved strength, formability and obtained sheet
US10626478B2 (en) 2014-11-18 2020-04-21 Salzgitter Flachstahl Gmbh Ultra high-strength air-hardening multiphase steel having excellent processing properties, and method for manufacturing a strip of said steel
WO2016078644A1 (de) * 2014-11-18 2016-05-26 Salzgitter Flachstahl Gmbh Höchstfester lufthärtender mehrphasenstahl mit hervorragenden verarbeitungseigenschaften und verfahren zur herstellung eines bandes aus diesem stahl
US10954580B2 (en) 2015-12-21 2021-03-23 Arcelormittal Method for producing a high strength steel sheet having improved strength and formability, and obtained high strength steel sheet
CN109894812A (zh) * 2019-02-13 2019-06-18 舞阳钢铁有限责任公司 一种小单重坯料生产Cr-Mo钢板的方法
CN113215493A (zh) * 2021-05-11 2021-08-06 北京理工大学 一种高强度榴弹弹钢及其制备方法
CN113403533A (zh) * 2021-05-28 2021-09-17 广西柳钢华创科技研发有限公司 高速棒材生产hrb500e螺纹钢筋的方法及高速棒材生产的hrb500e螺纹钢筋
CN113403533B (zh) * 2021-05-28 2022-04-12 广西柳钢华创科技研发有限公司 高速棒材生产hrb500e螺纹钢筋的方法及高速棒材生产的hrb500e螺纹钢筋
CN113699456A (zh) * 2021-09-01 2021-11-26 山东盛阳金属科技股份有限公司 一种254SMo超级奥氏体不锈钢热连轧板卷及其生产工艺
CN113699456B (zh) * 2021-09-01 2022-06-21 山东盛阳金属科技股份有限公司 一种254SMo超级奥氏体不锈钢热连轧板卷生产工艺

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ZA200907430B (en) 2010-07-28
PL2155915T3 (pl) 2018-03-30
RU2009145940A (ru) 2011-06-20
CN101765668A (zh) 2010-06-30
US20100307644A1 (en) 2010-12-09
MA31555B1 (fr) 2010-08-02
CN101765668B (zh) 2011-12-21
JP5398701B2 (ja) 2014-01-29
US20160355900A1 (en) 2016-12-08
KR20100016438A (ko) 2010-02-12
US20200032366A1 (en) 2020-01-30
BRPI0821572B1 (pt) 2019-10-01
PL2155915T5 (pl) 2022-09-05
ES2655476T5 (es) 2022-09-29
WO2008145871A8 (fr) 2019-09-06
AR066508A1 (es) 2009-08-26
WO2008145871A2 (fr) 2008-12-04
ES2655476T3 (es) 2018-02-20
RU2437945C2 (ru) 2011-12-27
US11414722B2 (en) 2022-08-16
KR101523395B1 (ko) 2015-05-27
HUE035549T2 (en) 2018-05-28
US20220136078A1 (en) 2022-05-05
WO2008145871A3 (fr) 2009-02-19
JP2010526935A (ja) 2010-08-05
EP2155915B2 (fr) 2022-04-27
US10612106B2 (en) 2020-04-07
EP2155915B1 (fr) 2017-10-25
EP2155915A2 (fr) 2010-02-24
BRPI0821572A2 (pt) 2015-06-16
MX2009011927A (es) 2009-11-18
CA2686940A1 (fr) 2008-12-04

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