Classifications

• • 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.
• Dual Phase or TRIP steel plates have been proposed, with a maximum resistance level of the order of 1000 MPa.
• 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.
• patent EP 1559798 describes the manufacture of steels with a composition of: 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.
• EP 1589126 also describes the manufacture of cold-rolled thin sheets, 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% 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 of 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>
• composition optionally comprising: 0.05% ⁇ V ⁇
• the subject of the invention is also a steel sheet of the above composition, with an elongation at break greater than 10%, characterized in that Mo ⁇
• the subject of the invention is also a steel sheet of the above composition, with a resistance greater than 1400 MPa, 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
• the subject of the invention is also a steel sheet of the above composition, with a resistance greater than 1600 MPa, with an elongation at break greater than
• the composition comprises: 0.19% ⁇ C ⁇ 0.23%
• the composition comprises: 1.5% ⁇ Mn ⁇ 2.5%
• the composition comprises: 1.2% ⁇ Si ⁇ 1.8%
• the composition comprises: 1, 2% ⁇ AI ⁇ 1.8%
• the composition comprises: 0.05% ⁇ V ⁇ 0.15%
• the composition comprises: 0.12% ⁇ V ⁇ 0.15%
• 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 0 of between 5 and 15 ° C./s up to a temperature Ti between Ac 3 and Ac 3 + 20 ° C., for a time ti of between 50 and 150 s, and then cooling is carried out.
• 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 of greater than 8%, according to which a composition steel is supplied: 0.10 % ⁇ C ⁇ 0.25%, 1% ⁇ Mn ⁇ 3%, Al> 0.010%, Si ⁇ 2.990%, with 1% ⁇ Si + AI ⁇ 3%, S ⁇ 0.015%, P ⁇ 0.1 %, N ⁇ 0.008%, Mo ⁇ 0.25%, Cr ⁇ 1.65%, with the proviso that Cr + (3 x Mo)> 0.3%, optionally 0.05% ⁇ V ⁇ 0.15%, B ⁇ 0.005%, Ti in amount such that Ti / N> 4 and Ti ⁇ 0.040%.
• the semi-finished product is cast from this steel, the semi-finished product is heated to a temperature above 115 ° C., and then the semi-finished product is hot-rolled to obtain a hot-rolled sheet. We reel the sheet, it is scoured, and then cold rolled sheet with a reduction rate of between 30 and 80% to obtain a cold rolled sheet.
• the cold-rolled sheet is heated to a speed V c of between 5 and
• the temperature Ti is preferably between Ac3 + 10 ° C and
• 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.
• FIG. 1 shows an exemplary structure of a steel sheet according to the invention, the structure being revealed by LePera reagent.
• FIG. 2 shows an exemplary structure of a steel sheet according to the invention, the structure being revealed by Nital reagent.
• the inventors have shown that the above problems were solved when the annealed cold-rolled thin steel sheet had a bainitic microstructure, in addition to islands of martensite and residual austenite, or "MA" islands.
• the microstructure contains a greater amount of 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 annealing heat treatment after cold rolling, it increases the hardenability and allows 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.
• the carbon also retards the formation of the pro-eutectoid ferrite after annealing heat treatment after cold rolling: otherwise, the presence of this phase of low hardness would cause excessive local damage at the interface with the matrix. Hardness is higher.
• the presence of pre-eutectoid ferrite resulting from 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.
• 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 pro- eutectoid 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 band structure harmful.
• Silicon and aluminum play an important role together according to the invention.
• An addition of silicon according to the invention helps to stabilize a sufficient quantity of residual austenite in the form of islets which subsequently transform and progressively become 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 discussed 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 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
• 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 uniform or breaking elongation is particularly increased.
• 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 quantity mentioned above makes it possible to obtain a resistance greater than 1400
• 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.
• FIG. 1 shows an example of microstructure of a steel sheet according to the invention.
• the morphology of the M-A islands was revealed by means of suitable chemical reagents: after attack, the M-A islands appear in white on a more or less dark bainitic matrix. Some small islands are located between the slats of bainite ferrite. The islands are observed at magnitudes ranging from about 500 to 150Ox over a statistically representative surface and the average size of the islands as well as the average distance between these islets is measured by means of image analysis software. In the case of FIG. 1, the surface percentage of the islets is
• the average size of the M-A islands is less than 1 micrometer.
• the microstructure is composed of 45 to 65% of bainite, the balance being 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.
• a steel of composition according to the invention is supplied
• This casting can be carried out in ingots or continuously in the form of slabs of the order of 200mm thickness.
• the casting can also be carried out in the form of thin slabs of a few tens of millimeters thick, or thin strips, between contra-rotating steel rolls.
• 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 115 ° 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.
• 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 the 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 so as to give it a surface state suitable for cold rolling. This is done by reducing the thickness of the hot-rolled sheet by 30 to 80%.
• An annealing heat treatment is then carried out, preferably by continuous annealing, which comprises the following phases:
• V 0 is greater than 15 ° C / s, the recrystallization of the cold-worked sheet by the cold rolling may not be complete.
• a minimum value of 5 ° C / s is required for productivity.
• a speed V 0 of between 5 and 15 ° C./s makes it possible to obtain an austenite grain size that is particularly suitable for the desired final microstructure.
• the temperature Ti is between A C3 and A C3 + 20 ° C, the temperature A C3 corresponding to the total conversion to austenite during heating.
• a c3 depends on the composition of the steel and the heating rate and can be determined for example by dilatometry. Total austenitization limits the subsequent formation of proeutectoid ferrite. It is important that the temperature Ti be less than A C3 + 20 ° C in order to avoid exaggerated magnification of the austenitic grain. Within this range (A C3 - A C3 + 20 o C), the characteristics of the final product are insensitive to a temperature variation T 1 .
• the temperature " Pi is between Ac 3 + 10 ° C and Ac 3 + 20 ° C.
• the inventors have demonstrated that the austenitic grain size is more homogeneous and finer, which leads to subsequently to the formation of a final microstructure which also has these characteristics.
• the next step in the process is the same, whether or not the product contains chromium and / or molybdenum: a VR 2 speed below 30 ° C / s to room temperature.
• a VR 2 speed below 30 ° C / s to room temperature.
• the cooling at a speed VR 2 of less than 30 ° C./s causes a return of the islands of newly formed martensite, which is favorable in terms of of use properties.
• Steels have been developed, the composition of which is given in the table below, expressed in percentage by weight.
• the composition of steels R-1 to R-5 used for the manufacture of reference sheets has been indicated for comparison purposes. .
• microstructural constituents measured by quantitative microscopy were also reported: surface fraction of bainite, martensite and residual austenite.
• Islets M-A have been evidenced by LePera's reagent. Their morphology was examined using an image analysis software
• the tensile mechanical properties obtained were given in Table 3 below. The Re / Rm ratio was also indicated.
• the breaking energy was determined at -40 ° C. from Charpy V type resilience specimens reduced to a thickness of 1.4 mm. 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 have a particularly advantageous combination of mechanical properties: on the one hand a resistance mechanical higher 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. 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 bainit content between 65 and 90%, the balance consisting of M-A islands.
• FIG. 1 thus shows the microstructure of the steel sheet I3a comprising 88% of bainite and 12% of islets MA 1 revealed by a LePera reagent attack.
• Figure 2 shows 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 11-b and 11-c have been annealed at a temperature Ti too low, the austenitic transformation is not complete.
• the microstructure comprises proeutectoid ferrite (40% for Mb, 20% for 11-c) and an excessive content of M-A 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 higher temperature gives rise to a coarser structure and leads to insufficient mechanical strength.
• the cooling rate VRI after annealing is not sufficient, the microstructure formed is more heterogeneous and the elongation at break is reduced to below 10%.
• the holding temperature T2 is less than Ms-20 ° C: consequently, the cooling VRI 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 MA islands 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 Ti lower than A C3 leads to an excessive content of proeutectoid ferrite and cementite, and insufficient strength.
• R4 steel is deficient in (Si + AI) cooling rate
• VRI is particularly weak. 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.
• a 12-d steel sheet was manufactured according to a process having identical characteristics, with the exception of the temperature Ti equal to 830 ° C., ie the temperature A C 3 in the case where J ⁇ is equal to A C3, suitability for conical hole expansion is
• 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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• 2007
  • 2007-05-11 EP EP07290598A patent/EP1990431A1/de not_active Withdrawn
• 2008
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