EP3167091B1 - Tôle d'acier laminée à chaud et procédé de fabrication associé - Google Patents

Tôle d'acier laminée à chaud et procédé de fabrication associé Download PDF

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Publication number
EP3167091B1
EP3167091B1 EP15753985.9A EP15753985A EP3167091B1 EP 3167091 B1 EP3167091 B1 EP 3167091B1 EP 15753985 A EP15753985 A EP 15753985A EP 3167091 B1 EP3167091 B1 EP 3167091B1
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weight
sheet
contents
expressed
hot
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French (fr)
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EP3167091A1 (fr
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Jean-Marc PIPARD
Astrid Perlade
Bastien WEBER
Aurélie MILANI
Florence PECHENOT
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ArcelorMittal SA
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ArcelorMittal SA
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    • 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
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
    • B21C37/00—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape
    • B21C37/02—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape of sheets
    • 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
    • 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
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C22C33/00—Making ferrous alloys
    • C22C33/04—Making ferrous alloys by melting
    • 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
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—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
    • C22C38/38—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
    • 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
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
    • C23C2/06—Zinc or cadmium or alloys based thereon
    • 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
    • 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
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/34—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the shape of the material to be treated
    • C23C2/36—Elongated material
    • C23C2/40—Plates; 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
    • 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
    • C21D2211/004—Dispersions; Precipitations
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing

Definitions

  • the invention mainly relates to a hot-rolled steel sheet.
  • the invention further relates to a method for making such a steel sheet.
  • TRIP Transformation Induced Plasticity
  • multiphase steels with predominantly bainitic structure have been proposed. These steels are used in industry, and particularly in the automotive industry, to produce structural parts.
  • This type of steel is described in the publication EP 2,020,451 .
  • the steels described in this publication include, in addition to the known presence of carbon, manganese and silicon, molybdenum and vanadium.
  • the microstructure of these steels essentially comprises upper bainite (at least 80%) as well as lower bainite, martensite and residual austenite.
  • certain automotive parts such as bumper beams and suspension arms, are manufactured by shaping operations combining different modes of deformation.
  • Certain microstructural characteristics of steel may be well adapted to a mode of deformation, but unfavorable vis-à-vis another mode.
  • Some parts of the parts must have a high resistance to elongation, others must have good aptitude for shaping a cut edge. This latter property is evaluated by the hole expansion method described in ISO 16630: 2009.
  • a type of steel that overcomes these disadvantages is free of molybdenum and vanadium, and comprises titanium and niobium in specific contents, these two elements conferring in particular on the sheet the desired strength, the necessary hardening and the expansion ratio of target hole.
  • the steel sheets which are the subject of the present invention are subjected to a hot winding, this operation notably making it possible to precipitate the titanium carbides and to give the sheet maximum curing.
  • the invention therefore aims to provide a sheet for which the high temperature winding operation does not cause the formation of the aforementioned surface defects.
  • the invention relates to a steel sheet in the uncoated or galvanized state.
  • the composition and mechanical properties of the steel must be compatible with the stresses and thermal cycles of continuous dipping zinc coating processes.
  • the object of the invention is also to propose a process for manufacturing a steel sheet that does not require large rolling forces, which makes it possible to manufacture them in a wide range of thickness, for example between 1.5 and 4.5 millimeters.
  • the invention relates to a hot-rolled steel sheet of economical manufacturing cost, having jointly a yield strength greater than 680 MPa at least in the direction of the rolling direction, and less than or equal to 840 MPa, a mechanical strength of between 780 MPa and 950 MPa, an elongation at break greater than 10% and a hole expansion ratio (Ac) greater than or equal to 45%.
  • the inventors have discovered that the surface defects present on certain sheets wound at high temperatures, especially above a temperature of 570 ° C., are mainly located at the core of the coil. In this region, the turns are contiguous, and the partial pressure of oxygen is such that only elements that are more oxidizable than iron, for example silicon, manganese or chromium, can still oxidize in contact with atoms of oxygen.
  • the 1-atmosphere iron-oxygen phase diagram shows that iron oxide, wustite, formed at high temperatures is no longer stable below 570 ° C and decomposes at thermodynamic equilibrium in two other phases: hematite and magnetite, one of the products of this reaction being oxygen.
  • the inventors have thus identified that the conditions are met so that in the coil core, the oxygen thus released combines with the more oxidizable elements than iron, namely notably manganese, silicon, chromium and aluminum present at the surface of the sheet.
  • the grain boundaries of the final microstructure naturally constitute diffusion short circuits for these elements with respect to homogeneous diffusion in the matrix. This results in more pronounced and deeper oxidation at the grain boundaries.
  • the oxides thus formed are also removed, leaving room for defects (lack of continuity) substantially perpendicular to the skin of the sheet of about 3 to 5 microns.
  • the inventors found a sheet composition which makes it possible to prevent the formation of intergranular oxidation at the coil core at the level of the grains of the final microstructure after pickling, the intergranular oxidation occurring on the grain boundaries of the final microstructure.
  • composition of the sheet must comprise chromium and molybdenum defined in particular contents. Surprisingly, the inventors have demonstrated that such sheets do not have the aforementioned surface defects.
  • the carbon weight content of the sheet is between 0.040% and 0.08%. This range of carbon content makes it possible simultaneously to obtain a high breaking elongation and a mechanical strength Rm greater than 780 MPa.
  • the maximum content by weight of carbon is set at 0.08%, which makes it possible to obtain a hole expansion ratio Ac% greater than or equal to 45%.
  • the content by weight of carbon is between 0.05% and 0.07%.
  • the weight content of manganese is between 1.2% and 1.9%.
  • manganese participates in the strength of the sheet and limits the formation of a central segregation band. It helps to obtain an Ac% hole expansion ratio greater than or equal to 45%.
  • the content by weight of manganese is between 1.4% and 1.6%.
  • An aluminum content by weight of between 0.005% and 0.1% ensures the deoxidation of the steel during its manufacture.
  • the content by weight of aluminum is between 0.01% and 0.07%.
  • Titanium is present in the steel of the sheet of the invention in an amount of between 0.07% and 0.125% by weight.
  • vanadium in an amount of between 0.001% and 0.2% by weight may be provided.
  • An increase in mechanical strength up to 250 MPa can be achieved by refinement of the microstructure and hardening precipitation of carbonitrides.
  • the weight content of nitrogen is between 0.002% and 0.01%. Although the nitrogen content can be extremely low, its limit value is set at 0.002% so that the production can be carried out under economically satisfactory conditions.
  • niobium its weight content in the composition of the steel is less than 0.045%. Beyond a content by weight of 0.045%, the recrystallization of the austenite is delayed. The structure then contains a significant fraction of elongated grains, which no longer makes it possible to achieve the target hole expansion ratio Ac%. Preferably, the content by weight of niobium is less than 0.04%.
  • composition of the invention also comprises chromium in an amount of between 0.10% and 0.55%.
  • chromium content makes it possible to improve the surface quality.
  • the chromium content is defined together with the molybdenum content.
  • the silicon is present in the chemical composition of the sheet, with a content by weight of between 0.1% and 0.3%. Silicon retards the precipitation of cementite. In the amounts defined according to the invention, it precipitates in a very small amount, that is to say in surface content less than 1.5% and in a very fine form. This finer morphology of the cementite makes it possible to obtain a high hole expansion capacity of greater than or equal to 45%.
  • the content by weight of silicon is between 0.15% and 0.3%.
  • the sulfur content of the steel according to the invention must not be greater than 0.004% in order to limit the formation of sulphides, especially of manganese sulphides.
  • the low levels of sulfur and nitrogen present in the composition of the sheet promote the ability to expand the hole.
  • the phosphorus content of the steel according to the invention is less than 0.020% in order to promote hole expansion ability and weldability.
  • the composition of the sheet comprises chromium and molybdenum in specific contents.
  • Tables 1 to 4 show the influence of the composition of a sheet and the manufacturing conditions of this sheet on the elastic limit, the maximum tensile strength, the total elongation at break, the hole expansion and an oxidation criterion taken in the middle or core coil and strip axis, these notions of coil core and strip axis being explained later.
  • the hole expansion method is described in ISO 16630: 2009 as follows: after making a hole by cutting in a sheet, a frustoconical tool is used so as to expand at the edges of this hole. hole. It is during this operation that one can observe an early damage in the vicinity of the edges of the hole during the expansion, this damage starting on particles of second phase or the interfaces between the different microstructural constituents in the 'steel.
  • the hole expansion method thus consists in measuring the initial diameter Di of the hole before stamping, then the final diameter Df of the hole after stamping, determined at the moment when there are observed through-cracks in the thickness of the sheet on the edges of the hole.
  • Ac thus makes it possible to quantify the ability of a sheet to withstand stamping at a cut orifice.
  • the initial diameter is 10 millimeters.
  • the inventors have demonstrated that two criteria relating to the presence of defects of the wound sheet should be satisfied to obtain excellent fatigue performance. More precisely, these criteria must be respected in a zone of the coil which is subjected to specific conditions: this zone is situated in the core of the coil and in the axis of the strip where the partial pressure of oxygen is lower but sufficient for elements more oxidizable than iron can be oxidized. This phenomenon is observed when the winding is made in contiguous turns at a minimum winding voltage of 3 tons-force.
  • the coil core is defined as being the length zone of the coil to which, on either side, an end zone is subtracted, the length of each of the end zones being equal to 30% of the total length of the coil.
  • the strip axis is similarly defined as being an area centered on the middle of the strip in the direction transverse to the rolling direction, and of width equal to 60% of the width of the strip.
  • these two oxidation criteria are evaluated on a sheet 1 in the middle of the coil and in the axis of the strip over an observation length l ref .
  • This observation length is chosen to characterize the surface state in a representative manner.
  • the observation length l ref is set at 100 micrometers, but can be up to 500 micrometers or more if one wishes to reinforce the requirements in terms of oxidation criterion.
  • the defects due to the oxidation 2 are distributed over n oxidation zones Oi of said coiled sheet 1, i being between 1 and n.
  • Each oxidation zone Oi extends along a length l i , and is considered to be distinct from the neighboring zone Oi + 1 if these two zones Oi, Oi + 1 are separated by a zone free from any oxidation defect. at least 3 microns in length.
  • the first criterion [1] to which the defects 2 of the sheet 1 must satisfy is a maximum depth criterion corresponding to P i max ⁇ 8 micrometers, P i max being the maximum depth of a fault due to the oxidation 2 on each oxidation zone Oi.
  • the second criterion [2] to which the defects 2 of the sheet 1 must satisfy is a mean depth criterion reflecting the greater or lesser presence of the oxidation zones on the observation zone of length l ref .
  • This second criterion is defined by 1 l r e f ⁇ i not P i m o there ⁇ l i ⁇ 2.5 micrometers, P i moy being the average depth of defects due to oxidation on an oxidation zone Oi.
  • Table 1 shows the results obtained for compositions not falling within the scope of the sheet of the invention.
  • Table 2a shows sheet compositions according to the invention and Table 2b shows the results obtained for the sheet compositions of Table 2a, which sheets are intended to be uncoated and wound at a constant temperature of 590.degree. except for example 5.
  • Table 3 shows the results obtained for compositions of the sheet of the invention, which is also intended to be uncoated and for winding temperatures ranging from 526 ° C to 625 ° C.
  • Table 4 shows the results obtained for compositions of the sheet of the invention, which is intended to be galvanized and for a winding temperature ranging from 535 ° C. to 585 ° C.
  • Table 2b illustrates the results obtained for a composition of the sheet comprising chromium and molybdenum in respective contents of between 0.15% and 0.55% for chromium and between 0.05% and 0.32% for chromium and molybdenum. molybdenum.
  • Table 3 illustrates the results obtained for a composition of the sheet comprising chromium and molybdenum in respective contents of between 0.30% and 0.32% for chromium and between 0.15% and 0.17% for chromium and molybdenum. molybdenum.
  • Table 4 illustrates the results obtained for a composition of the sheet comprising chromium and molybdenum in respective contents of between 0.31% and 0.32% for chromium and between 0.15% and 0.16% for molybdenum.
  • Tables 2, 3 and 4 meet the oxidation criteria defined above.
  • the figure 7 illustrates the presence of surface defects for a sheet 9 which does not meet the previously defined oxidation criteria and whose composition comprises 0.3% chromium and 0.02% molybdenum.
  • FIGS 8 and 9 illustrate the surface state of two sheets 10, 11 which satisfy the oxidation criteria and whose respective composition includes for the figure 8 0.3% chromium, and 0.093% molybdenum, and for the figure 9 0.3% chromium and 0.15% molybdenum.
  • the experimental points obtained for counterexamples and examples are shown at a winding temperature of 590 ° C. More precisely, the experimental points 3 correspond to the counterexamples of the table 1, the experimental points 4a correspond to the examples of the tables 2a and 2b for which the surface oxidation is low and the experimental points 4b correspond to the examples of Tables 2a and 2b for which the surface oxidation is zero or very low.
  • a first experimental point 3 corresponds to counterexample 11 for which the precise content of chromium is 0.150
  • a second experimental point 4a corresponds to Example 11 for which the precise chromium content is 0.152.
  • the composition of the sheet of the invention comprises chromium and molybdenum with a content by weight of chromium which is strictly greater than 0.15% and less than or equal to 0.6 % when the molybdenum content is between 0.05% and 0.11% and a chromium content of between 0.10% and 0.6% where the molybdenum content is strictly greater than 0.11% and less than or equal to 0.35%.
  • the molybdenum content is thus between 0.05% and 0.35% while respecting the chromium contents previously expressed.
  • the content by weight of chromium is between 0.16% and 0.55% when the content by weight of molybdenum is between 0.05% and 0.11%, and the content by weight of chromium is included between 0.10% and 0.55% when the content by weight of molybdenum is between 0.11% and 0.25%.
  • the content by weight of chromium is between 0.27% and 0.52% and the content by weight of molybdenum is between 0.05% and 0.18%.
  • the microstructure of the sheet of the invention comprises granular bainite.
  • Granular bainite is distinguished from upper and lower bainite.
  • the granular bainite composing the microstructure of the sheet of the invention is defined as having a large proportion of adjacent grains strongly disoriented and an irregular morphology of the grains.
  • the surface percentage of granular bainite is greater than 70%.
  • the ferrite is present in a surface fraction not exceeding 20%.
  • the optional supplement consists of lower bainite, martensite and residual austenite, the sum of the martensite and residual austenite contents being less than 5%.
  • the figure 10 represents the microstructure of a sheet of the invention thus comprising granite bainite 12, islands of martensite and austenite 13 and ferrite 14.
  • the effective titanium Tieff represents the amount of excess titanium capable of precipitating in the form of carbides.
  • Tables 2 to 4 show the effective titanium values for each composition tested.
  • FIGS. 3 to 6 illustrate the results obtained respectively in yield strength and maximum tensile strength, as a function of the effective titanium content for different compositions for which the titanium and nitrogen contents vary.
  • the figures 3 and 5 illustrate these properties in the rolling direction of the sheet, and the figures 4 and 6 illustrate these properties in the transverse direction of rolling of sheet metal
  • the experimental points 5.5a represented by solid circles correspond to a composition for which the titanium content varies between 0.071% and 0.076% and the nitrogen content varies between 0.0070% and 0.0090%
  • the experimental points 6 , 6a represented by solid diamonds correspond to a composition for which the titanium content varies between 0.087% and 0.091% and the nitrogen content varies between 0.0060% and 0.0084%
  • the experimental points 7.7a materialized by solid triangles correspond to a composition for which the titanium content varies between 0.088% and 0.092%, and the nitrogen content varies between 0.0073% and 0.0081%
  • the experimental points 8.8a represented by solid squares correspond to to a composition for wherein the titanium content varies between 0.098% and 0.104% and the nitrogen content varies between 0.0048% and 0.0070%.
  • the criteria in elastic limit and in maximum tensile strength are respected for an effective titanium content varying between 0.055% and 0.095%.
  • the criteria in yield strength and maximum tensile strength are met for an effective titanium content ranging between 0.040% and 0.070%.
  • composition may comprise an effective titanium content varying between 0.040% and 0.095%, preferably between 0.055% and 0.070% where the criteria are met both in the rolling direction and in the cross direction.
  • the advantage presented by the consideration of the effective titanium resides in particular in the possibility of using a high nitrogen content to avoid limiting the nitrogen content which is binding for the process of making the sheet.
  • titanium [Ti] is added so that the quantities of titanium [Ti] and nitrogen [N] dissolved in the liquid metal satisfy% [Ti]% [N] ⁇ 6.10 -4 % 2 .
  • the liquid metal is then carried out either in a vacuum treatment or in a silica-calcium (SiCa) treatment, in which case it will be provided that the composition further comprises a content by weight of 0.0005 ⁇ Ca ⁇ 0.005%.
  • the titanium nitrides do not precipitate early in the coarse form in the liquid metal, which would have the effect of reducing the ability to expand the hole.
  • the precipitation of titanium occurs at lower temperatures in the form of fine carbonitrides distributed uniformly. This fine precipitation contributes to the hardening and refinement of the microstructure.
  • the steel is cast to obtain a cast half-product.
  • This can be done preferably by continuous casting.
  • the casting may be carried out between counter-rotating rolls to obtain a semi-finished product in the form of thin slabs or thin strips. Indeed, these modes of casting lead to a decrease in the size of the precipitates, favorable to the expansion of hole on the product obtained in the final state.
  • the half-product obtained is then heated to a temperature of between 1160 and 1300 ° C. Below 1160 ° C, the target tensile strength of 780 MPa is not achieved.
  • the hot rolling stage of the half-products starting at more than 1160 ° C. can be done directly after casting, ie without cooling the half product until at room temperature, and therefore without it being necessary to perform a heating step.
  • said cast half-product is hot rolled with an end-of-rolling temperature of between 880 and 930 ° C., the reduction rate of the penultimate pass being less than 0.25, the rate of the last pass being less than 0.15, the sum of the two reduction rates being less than 0.37, the next-to-last pass rolling start temperature being less than 960 ° C, so as to obtain a hot-rolled product.
  • the material is rolled at a temperature below the non-recrystallization temperature, which prevents the recrystallization of austenite. It is thus intended not to cause excessive deformation of the austenite during these last two passes.
  • the hot-rolled product After rolling, the hot-rolled product is cooled at a rate of between 20 and 150 ° C./s, preferably between 50 and 150 ° C./s, so as to obtain a hot-rolled steel sheet.
  • the sheet obtained is reeled at a temperature of between 525 and 635 ° C.
  • the winding temperature will be between 525 and 635 ° C so that the precipitation is the densest and most hardening possible allowing to satisfy a mechanical tensile strength greater than 780 MPa in both the long and the transverse directions. According to the results presented in these tables, these winding temperatures make it possible to obtain a sheet for which the oxidation criterion is satisfied.
  • the winding temperature will be between 530 and 600 ° C., regardless of the desired direction of the properties in the direction of rolling or in the cross direction and to compensate for the additional precipitation occurring during the heat treatment associated with the galvanizing operation. According to the results presented in this table, these winding temperatures make it possible to obtain a sheet for which the oxidation criterion is satisfied.
  • the wound sheet is then etched according to a conventional technique well known in itself, and then heated to a temperature between 550 and 750 ° C.
  • the sheet will then be cooled at a speed of between 5 and 20 ° C./s, and then coated with zinc in a suitable zinc bath.
  • All the steel sheets according to the invention were rolled with a lower reduction ratio of 0.15 in the penultimate rolling pass, and a reduction rate of less than 0.07 in the last rolling pass, the cumulative deformation during these two passes being less than 0.37. At the end of the hot rolling, we obtain a little deformed austenite.
  • the invention makes it possible to provide steel sheets having high tensile mechanical characteristics and good formability by stamping.
  • the stampings made from these sheets have a high fatigue resistance due to the minimization or absence of surface defects after stamping.
  • Table 2a Sheet metal compositions according to the invention Chemical composition (in%) VS mn Yes al Cr MB Nb Ti P S NOT Tieff
  • Example 1 0.06 1.6 0.2 0.06 0.29 0.09 0.031 0.110 0,015 0,002 0,007 0.086
  • Example 2 0.06 1.6 0.2 0.04 0.29 0.05 0,034 0.115 0,015 0,001 0.006 0.094
  • Example 3 0.06 1.6 0.2 0.04 0.29 0.11 0,034 0.111 0,015 0,001 0.006 0.090
  • Example 4 0.06 1.5 0.2 0.06 0.38 0.15 0,026 0,100 0,017 0,001 0.006 0.078
  • Example 5 0.07 1.5 0.2 0.04 0.30 0.16 0,030 0,100 0.016 0,001 0.005 0.083
  • Example 6
  • Example 19 0.05 1.4 0.25 0.03 0.30 0.20 0,032 0.089 0,013 0,002 0,008 0,061
  • Example 20 0.05 1.5 0.25 0.04 0.55 0.05 0,030 0.089 0.012 0,002 0,009 0.058
  • Example 21 0.05 1.5 0.25 0.04 0.54 0.11 0,030 0.087 0.012 0,002 0,008 0.059
  • Example 22 0.05 1.4 0.24 0.03 0.16 0.20 0,030 0.088 0,013 0,002 0,008 0,060
  • Example 23 0.05 1.4 0.24 0.03 0.19 0.20 0,030 0.088 0,013 0,002 0,008 0,060
  • Example 24 0.05 1.4 0.24 0.04 0.

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BR112017000405B1 (pt) 2021-08-17
US10858716B2 (en) 2020-12-08
US11447844B2 (en) 2022-09-20
CA2954830C (fr) 2019-02-12
PL3167091T3 (pl) 2019-02-28
BR112017000405A2 (pt) 2018-01-23
ZA201608396B (en) 2019-10-30
JP6391801B2 (ja) 2018-09-19
CA2954830A1 (fr) 2016-01-14
RU2017104317A (ru) 2018-08-13
UA117790C2 (uk) 2018-09-25
WO2016005780A1 (fr) 2016-01-14
MX2017000496A (es) 2017-04-27
US20170183753A1 (en) 2017-06-29
ES2704472T3 (es) 2019-03-18
EP3167091A1 (fr) 2017-05-17
KR101928675B1 (ko) 2018-12-12
WO2016005811A1 (fr) 2016-01-14
MA39523A1 (fr) 2017-06-30
JP2017526812A (ja) 2017-09-14
RU2674360C2 (ru) 2018-12-07
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HUE042353T2 (hu) 2019-06-28
CN106536780B (zh) 2018-12-21

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