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EP2123786A1 - Verfahren zur Herstellung von kalt gewalzten Zweiphasen-Stahlblechen mit sehr hoher Festigkeit und so hergestellte Bleche - Google Patents

Verfahren zur Herstellung von kalt gewalzten Zweiphasen-Stahlblechen mit sehr hoher Festigkeit und so hergestellte Bleche Download PDF

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Publication number
EP2123786A1
EP2123786A1 EP08290474A EP08290474A EP2123786A1 EP 2123786 A1 EP2123786 A1 EP 2123786A1 EP 08290474 A EP08290474 A EP 08290474A EP 08290474 A EP08290474 A EP 08290474A EP 2123786 A1 EP2123786 A1 EP 2123786A1
Authority
EP
European Patent Office
Prior art keywords
product
temperature
steel sheet
rolled
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Withdrawn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
EP08290474A
Other languages
English (en)
French (fr)
Inventor
Catherine Vinci
Gloria Restrepo Garces
Antoine Moulin
Tom Waterschoot
Mohamed Goune
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
ArcelorMittal France SA
Original Assignee
ArcelorMittal France SA
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by ArcelorMittal France SA filed Critical ArcelorMittal France SA
Priority to EP08290474A priority Critical patent/EP2123786A1/de
Priority to CA2725290A priority patent/CA2725290C/fr
Priority to JP2011510017A priority patent/JP5425896B2/ja
Priority to CN2009801183844A priority patent/CN102046827B/zh
Priority to RU2010152214/02A priority patent/RU2470087C2/ru
Priority to PL09761870T priority patent/PL2291547T3/pl
Priority to US12/993,498 priority patent/US20110168300A1/en
Priority to BRPI0912879-4A priority patent/BRPI0912879B1/pt
Priority to PCT/FR2009/000574 priority patent/WO2009150319A1/fr
Priority to EP09761870A priority patent/EP2291547B1/de
Priority to AT09761870T priority patent/ATE555225T1/de
Priority to ES09761870T priority patent/ES2386701T3/es
Priority to UAA201015426A priority patent/UA100056C2/ru
Priority to MX2010012584A priority patent/MX2010012584A/es
Priority to KR1020107028478A priority patent/KR101328768B1/ko
Publication of EP2123786A1 publication Critical patent/EP2123786A1/de
Priority to ZA2010/07964A priority patent/ZA201007964B/en
Priority to MA33333A priority patent/MA32294B1/fr
Priority to US15/097,039 priority patent/US10190187B2/en
Priority to US16/213,455 priority patent/US20190106765A1/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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D7/00—Casting ingots, e.g. from ferrous metals
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/84—Controlled slow cooling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
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    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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
    • C21D8/021—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular fabrication or treatment of ingot or slab
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
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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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    • 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
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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
    • C21D8/0236—Cold rolling
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    • 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
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    • 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
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    • 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
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    • 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
    • C21D8/0273—Final recrystallisation annealing
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    • 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
    • C21D8/0278—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular surface treatment
    • 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
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    • 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
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    • 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
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    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
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    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
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    • 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
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    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
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    • 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
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
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    • C23C2/022—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating
    • C23C2/0224—Two or more thermal pretreatments
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    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
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    • C23C2/06—Zinc or cadmium or alloys based thereon
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    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
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    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Definitions

  • the invention relates to the manufacture of cold-rolled and annealed sheets of so-called "dual-phase" steels having a very high strength and a deformability for the manufacture of parts by shaping, in particular in the automotive industry.
  • the dual-phase steels whose structure includes martensite, possibly bainite, in a ferritic matrix, have developed a great deal because they combine high resistance with significant possibilities of deformation.
  • their yield strength is relatively low compared to their breaking strength, which gives them a very favorable ratio (yield strength / strength) during forming operations.
  • Their consolidation capacity is very large, which allows a good distribution of deformations in the case of a collision and obtaining a significantly higher yield strength on the part after forming.
  • EP0796928A1 also describes cold-rolled Dual Phase steels with a resistance greater than 550 MPa, composition 0.05-0.3% C, 0.8-3% Mn, 0.4-2.5% Al, 0, 01 to 0.2% Si.
  • the ferritic matrix contains martensite, bainite and / or residual austenite.
  • the examples presented show that the resistance does not exceed 660 MPa, even for a high carbon content (0.20-0.21%)
  • the document JP11350038 describes Dual Phase steels with a strength greater than 980 MPa, composition 0.10-0.15% C, 0.8-1.5% Si, 1.5-2.0% Mn, 0.01-0 , 05% P, less than 0.005% S, 0.01-0.07% Al in solution, less than 0.01% N, additionally containing one or more elements: 0.001-0.02% Nb, 0.001-0 , 02% V, 0.001-0.02% Ti.
  • This high strength is, however, obtained at the cost of a significant addition of silicon which certainly allows the formation of martensite, but may nevertheless lead to the formation of surface oxides which deteriorate the coating on quenching.
  • the object of the present invention is to provide a method of manufacturing dual-phase steel plates very high strength, cold rolled, bare or coated, not having the disadvantages mentioned above.
  • the invention also aims to provide a manufacturing method in which 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 invention also aims to provide an economical manufacturing process by avoiding the addition of expensive alloying elements.
  • the subject of the invention is a dual-phase cold-rolled and annealed steel sheet having a strength of between 980 and 1100 MPa, an elongation at break of greater than 9%, the composition of which comprises the contents being expressed in terms of weight: 0.055% ⁇ C ⁇ 0.095%, 2% ⁇ Mn ⁇ 2.6%, 0.005% ⁇ Si ⁇ 0.35%, S ⁇ 0.005%, P ⁇ 0.050%, 0.1 ⁇ Al ⁇ 0.3% , 0,05% ⁇ Mo ⁇ 0,25%, 0,2% ⁇ Cr ⁇ 0,5%, with the proviso that Cr + 2Mo ⁇ 0.6%, Ni ⁇ 0.1%, 0,010 ⁇ Nb ⁇ 0,040%, 0,010 ⁇ Ti ⁇ 0.050%, 0.0005 ⁇ B ⁇ 0.0025%, 0.002% ⁇ N ⁇ 0.007%, the balance of the composition consisting of iron and unavoidable impurities resulting from the preparation.
  • the composition of the steel contains, the content being expressed by weight: 0.12% ⁇ Al ⁇ 0.25%.
  • the composition of the steel contains, the content being expressed by weight: 0.10% ⁇ Si ⁇ 0.30%.
  • the composition of the steel preferably contains: 0.15% ⁇ Si ⁇ 0.28%.
  • the composition contains: P ⁇ 0.015%.
  • the microstructure of the sheet preferably contains 35 to 50% of martensite in surface proportion.
  • the complement of the microstructure consists of 50 to 65% of ferrite in surface proportion.
  • the complement of the microstructure consists of 1 to 10% of bainite and 40 to 64% of ferrite in surface proportion.
  • the surface fraction of non-recrystallized ferrite relative to the entire ferritic phase is preferably less than or equal to 15%.
  • the steel sheet preferably has a ratio between its elastic limit R e and its resistance R m such that: 0.6 RRe / R m ⁇ 0.8.
  • the sheet is galvanized continuously.
  • the sheet has a galvannealed coating.
  • the invention also relates to a manufacturing method according to one of the above characteristics , characterized in that the temperature T M is between 760 and 830 ° C.
  • the cooling rate V R is greater than or equal to 15 ° C / s.
  • the invention also relates to the use of a steel sheet according to any one of the above characteristics, or manufactured by a process according to any one of the above characteristics, for the manufacture of structures or safety for motor vehicles.
  • carbon plays an important role in the formation of the microstructure and in the mechanical properties: below 0.055% by weight, the resistance becomes insufficient. Beyond 0.095%, a lengthening of 9% can no longer be guaranteed. The weldability is also reduced.
  • manganese is an element that increases quenchability and reduces carbide precipitation. A minimum content of 2% by weight is necessary to obtain the desired mechanical properties. However, beyond 2.6%, its gammagenic character leads to the formation of a band structure too marked.
  • Silicon is a component involved in the deoxidation of liquid steel and hardening in solid solution. This element also plays an important role in the formation of the microstructure by preventing the precipitation of carbides and by promoting the formation of martensite which enters the structure of the Dual Phase steels. It plays an effective role beyond 0.005%.
  • an increase in the silicon content degrades the dip coating ability by promoting the formation of adherent oxides on the surface of the products: its content must be limited to 0.35% by weight, and preferably 0.30% to obtain a good coating.
  • the silicon decreases the weldability: a content of less than 0.28% makes it possible simultaneously to ensure very good weldability as well as good coating.
  • the ductility is reduced due to the excessive presence of sulfides such as MnS which decrease the ability to deform, especially during hole expansion tests.
  • Phosphorus is an element that hardens in solid solution but decreases spot weldability and hot ductility, particularly because of its ability to segregate at grain boundaries or co-segregate with manganese. For these reasons, its content must be limited to 0.050%, and preferably to 0.015% in order to obtain a good spot welding ability.
  • Aluminum plays an important role in the invention by preventing the precipitation of carbides and promoting the formation of martensitic constituents upon cooling. These effects are obtained when the aluminum content is greater than 0.1%, and preferably when the aluminum content is greater than 0.12%.
  • AlN aluminum limits grain growth during annealing after cold rolling.
  • This element is also used for the deoxidation of the liquid steel in an amount usually less than about 0.050%. It is usually considered that higher levels increase the erosion of refractories and the risk of plugging the nozzles. In excessive amounts, aluminum reduces hot ductility and increases the risk of defects in continuous casting. It is also sought to limit inclusions of alumina, in particular in the form of clusters, in order to ensure sufficient elongation properties.
  • the inventors have demonstrated, in connection with the other elements of the composition, that an amount of aluminum up to 0.3% by weight could be added without adverse effect vis-à-vis other properties required particularly with respect to the deformability, and also provided the desired microstructural and mechanical properties.
  • An aluminum content of up to 0.25% by weight makes it possible to ensure the formation of a fine microstructure without large martensitic islands which would play a detrimental role on the ductility.
  • the inventors have shown that, surprisingly, it was possible to obtain a high level of resistance, between 980 and 1100 MPa, even in spite of the limitation of additions of aluminum and silicon. This is achieved by the particular combination of the alloying or microalloying elements according to the invention, in particular by virtue of the additions of Mo, Cr, Nb, Ti, B.
  • molybdenum plays an effective role on quenchability and delays the enlargement of ferrite and the appearance of bainite.
  • a content greater than 0.25% excessively increases the cost of the additions.
  • chromium in an amount greater than 0.2%, chromium, by its role on quenchability, also contributes to delay the formation of proeutectoid ferrite. Beyond 0.5%, the cost of the addition is too excessive.
  • chromium and molybdenum contents are such that: Cr + (2 ⁇ Mo) ⁇ 0.6%.
  • the coefficients in this relation reflect the respective influence of these two elements on the quenchability in order to favor the obtaining of a fine ferritic structure.
  • the titanium and niobium contents above make it possible to ensure that the nitrogen is completely trapped in the form of nitrides or carbonitrides, so that the boron is in free form and can play an effective role on the quenchability.
  • the minimum boron content to ensure effective quenchability is 0.0005%. Above 0.0025%, the effect on the quenchability is saturated and there is a detrimental effect on the coating and hot ductility.
  • nitrides and carbonitrides In order to form a sufficient amount of nitrides and carbonitrides, a minimum content of 0.002% nitrogen is required. The nitrogen content is limited to 0.007% to avoid the formation of BN which would decrease the amount of free boron required for the hardening of the ferrite.
  • Ni may be performed to provide additional hardening of the ferrite. This addition is, however, limited to 0.1% for cost reasons.
  • the cast semi-finished products are first brought to a temperature T R greater than 1150 ° C. in order to reach at all points a temperature favorable to the high deformations which the steel will undergo during rolling.
  • T R a temperature favorable to the high deformations which the steel will undergo during rolling.
  • the temperature T R is too high, the austenitic grains increase undesirably.
  • the only precipitates that can effectively control the size of the austenitic grain are titanium nitrides, and the reheat temperature should be limited to 1250 ° C to maintain a fine austenitic grain at this stage.
  • the hot rolling step of these semi-finished products starting at more than 1150 ° C. can be done directly after casting so well. that an intermediate heating step is not necessary in this case.
  • the semi-finished product is hot-rolled in a temperature range where the structure of the steel is totally austenitic: if T FL is lower than the start-of-transformation temperature of the austenite at cooling A r3 , the ferrite grains are hardened by rolling and ductility is reduced.
  • a rolling end temperature of greater than 850 ° C. will be chosen.
  • the hot-rolled product is then rolled at a temperature T bob of between 500 and 570 ° C.
  • T bob of between 500 and 570 ° C. This temperature range makes it possible to obtain a complete bainitic transformation during the quasi-isothermal maintenance associated with the winding.
  • the winding temperature is too low, the hardness of the product is increased, which increases the efforts required during the subsequent cold rolling.
  • the hot-rolled product is pickled according to a method known per se, then cold rolling is carried out with a reduction ratio preferably comprised between 30 and 80%.
  • the cold-rolled product is then heated, preferably in a continuous annealing installation, with an average heating rate Vc of between 1 and 5 ° C./s.
  • Vc average heating rate
  • T M annealing temperature
  • the heating is carried out up to an annealing temperature T M between the temperature A c1 (allotropic transformation start temperature at heating) + 40 ° C, and A c3 (end of allotropic transformation temperature at heating) - 30 ° C, that is to say in a particular temperature range of the intercritical domain: when T M is less than (A c1 + 40 ° C), the structure may further comprise non-recrystallized ferrite zones, the surface fraction of which may reach 15%. This proportion of non-recrystallized ferrite is evaluated as follows: after having identified the ferritic phase within the microstructure, the surface percentage of non-recrystallized ferrite relative to the entire ferritic phase is quantified.
  • An annealing temperature T M makes it possible to obtain an amount of austenite sufficient to subsequently form the cooling of the martensite in an amount such that the desired characteristics are attained.
  • a temperature T M lower than (A c3 - 30 ° C) also makes it possible to ensure that the carbon content of the austenite islands formed at the temperature T M indeed leads to a subsequent martensitic transformation: when the annealing temperature is too high The carbon content of the austenite islands becomes too low, leading to subsequent transformation into bainite or unfavorable pearlite.
  • too high a temperature leads to an increase in the size of niobium precipitates which lose some of their curing ability. The final mechanical strength is then reduced.
  • a temperature T M of between 760 ° C. and 830 ° C. is preferably chosen for this purpose.
  • a minimum holding time t M of 30s at the temperature T M allows the dissolution of the carbides, a partial transformation into austenite is carried out. The effect is saturated beyond a duration of 300 s.
  • a holding time greater than 300s is also difficult to comply with the productivity requirements of continuous annealing equipment, in particular the speed of scrolling.
  • the holding time t M is between 30 and 300s.
  • This cooling can be carried out from the temperature T M in one or several steps and may involve in the latter case different cooling modes such as cold or boiling water baths, jets of water or gas . These possible accelerated cooling modes can be combined to obtain a complete martensitic transformation of the austenite. After this martensitic transformation, the sheet is cooled to room temperature.
  • the microstructure of steels whose matrix is ferritic, has also been determined.
  • the surface fractions of bainite and martensite have been quantified after Picral and LePera reagent attack respectively, followed by image analysis using Aphelion TM software.
  • the non-recrystallized ferrite surface fraction was also determined by optical and scanning electron microscopy observations in which the ferritic phase was identified and the recrystallized fraction within this ferritic phase quantified.
  • Non-recrystallized ferrite is generally in the form of elongated islands by rolling.
  • the folding ability was quantified as follows: sheets were folded in a block on themselves in several turns. In this way, the bending radius decreases each turn. The foldability is then evaluated by noting the presence of cracks on the surface of the folded block, the rating being expressed from 1 (low foldability) to 5 (very good ability). satisfactory.
  • the sheets according to the invention have good weldability, in particular resistance, the equivalent carbon being less than 0.25.
  • the steel plates IX3 (galvanized) and IX6 (galvannealed) were annealed at a temperature T M too low: consequently, the fraction of non-recrystallized ferrite is excessive as well as the martensite fraction.
  • T M temperature
  • the figure 2 illustrates the microstructure of the steel sheet IX3: note the presence of non-recrystallized ferrite in the form of elongate islands (marked (A)) coexisting with recrystallized ferrite and martensite, the latter constituting appearing darker on the micrograph.
  • a Micrograph in Scanning Electron Microscopy ( figure 3 ) makes it possible to finely distinguish the zones of non recrystallized ferrite (A) from those recrystallized (B).
  • Sheet IX5 is a galvannealed sheet annealed at a temperature T M too high: the carbon content of austenite at high temperature then becomes too low and the appearance of bainite is favored at the expense of the formation of martensite. Coalescence of niobium precipitates is also observed, which causes a loss of hardening. The resistance is then insufficient, the ratio Re / R m being too high.
  • IX7 galvannealed sheet was cooled at a speed V R too slow after the annealing step: the transformation of the austenite formed into ferrite then occurs in this cooling step excessively, the steel sheet containing at the stage final a proportion of bainite too important and a proportion of martensite too low, which leads to insufficient resistance.
  • the composition of the steel sheet R does not correspond to the invention, its carbon content being too high, and its content of manganese, aluminum, niobium, titanium, boron being too low. As a result, the martensite fraction is too weak so that the mechanical strength is insufficient.
  • the steel sheets according to the invention will be used profitably for the manufacture of structural parts or safety in the automotive industry.

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EP08290474A 2008-05-21 2008-05-21 Verfahren zur Herstellung von kalt gewalzten Zweiphasen-Stahlblechen mit sehr hoher Festigkeit und so hergestellte Bleche Withdrawn EP2123786A1 (de)

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EP08290474A EP2123786A1 (de) 2008-05-21 2008-05-21 Verfahren zur Herstellung von kalt gewalzten Zweiphasen-Stahlblechen mit sehr hoher Festigkeit und so hergestellte Bleche
EP09761870A EP2291547B1 (de) 2008-05-21 2009-05-15 Verfahren zur herstellung von kaltgewalzten dualphasenstahlblechen mit sehr hoher festigkeit und so hergestellte bleche
AT09761870T ATE555225T1 (de) 2008-05-21 2009-05-15 Verfahren zur herstellung von kaltgewalzten dualphasenstahlblechen mit sehr hoher festigkeit und so hergestellte bleche
CN2009801183844A CN102046827B (zh) 2008-05-21 2009-05-15 非常高强度的冷轧双相钢片材的制造方法和这样生产的片材
RU2010152214/02A RU2470087C2 (ru) 2008-05-21 2009-05-15 Способ производства холоднокатаных листов из двухфазной стали, обладающей очень высокой прочностью, и полученные таким способом листы
PL09761870T PL2291547T3 (pl) 2008-05-21 2009-05-15 Sposób wytwarzania blach ze stali dwufazowej, walcowanych na zimno, o bardzo dużej wytrzymałości i blachy w ten sposób wytwarzane
US12/993,498 US20110168300A1 (en) 2008-05-21 2009-05-15 Manufacturing method for very high-strength cold-rolled dual-phase steel sheets and sheets so produced
BRPI0912879-4A BRPI0912879B1 (pt) 2008-05-21 2009-05-15 Chapa de aço bifásico laminada a frio e recozida e processo de fabricação de uma chapa de aço bifásico laminada a frio e recozida
PCT/FR2009/000574 WO2009150319A1 (fr) 2008-05-21 2009-05-15 Procede de fabrication de toles d'aciers dual phase laminees a froid a tres haute resistance et toles ainsi produites
CA2725290A CA2725290C (fr) 2008-05-21 2009-05-15 Procede de fabrication de toles d'aciers dual phase laminees a froid a tres haute resistance et toles ainsi produites
JP2011510017A JP5425896B2 (ja) 2008-05-21 2009-05-15 極めて高い強度の冷間圧延された二相鋼板を製造する方法およびこれにより製造された鋼板
ES09761870T ES2386701T3 (es) 2008-05-21 2009-05-15 Procedimiento de fabricación de chapas de acero de doble fase laminadas en frío con resistencia muy elevada y chapas así obtenidas
UAA201015426A UA100056C2 (ru) 2008-05-21 2009-05-15 Способ производства холоднокатаного и отожженного листа из двухфазной стали, полученный таким способом лист, способ производства холоднокатаного, отожженного и оцинкованного листа из двухфазной стали (варианты) и использование указанного стального листа
MX2010012584A MX2010012584A (es) 2008-05-21 2009-05-15 Metodo de fabricacion de chapas de acero de fase dual laminadas en frio de muy alta resistencia y laminas asi producidas.
KR1020107028478A KR101328768B1 (ko) 2008-05-21 2009-05-15 초고강도의 냉간 압연된 2 상 강판의 제조 방법 및 이에 의해 제조된 강판
ZA2010/07964A ZA201007964B (en) 2008-05-21 2010-11-08 Manufacturing method for very high-strength cold-rolled dual-phase steel sheets and sheets so produced
MA33333A MA32294B1 (fr) 2008-05-21 2010-11-11 Procede de fabrication de toles d'aciers dual phase laminees a froid a tres haute resistance et toles ainsi produites
US15/097,039 US10190187B2 (en) 2008-05-21 2016-04-12 Manufacturing method for very high-strength, cold-rolled, dual-phase steel sheets
US16/213,455 US20190106765A1 (en) 2008-05-21 2018-12-07 Very high-strength, cold-rolled, dual steel sheets

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BRPI0912879A2 (pt) 2017-05-16
KR101328768B1 (ko) 2013-11-13
EP2291547A1 (de) 2011-03-09
US20160222486A1 (en) 2016-08-04
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BRPI0912879B1 (pt) 2018-06-26
CA2725290A1 (fr) 2009-12-17
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UA100056C2 (ru) 2012-11-12
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JP2011523440A (ja) 2011-08-11
EP2291547B1 (de) 2012-04-25
ZA201007964B (en) 2011-07-27
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RU2470087C2 (ru) 2012-12-20

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