EP3853387B1 - Kaltgewalztes und beschichtetes stahlblech und verfahren zu seiner herstellung - Google Patents

Kaltgewalztes und beschichtetes stahlblech und verfahren zu seiner herstellung Download PDF

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Publication number
EP3853387B1
EP3853387B1 EP19772880.1A EP19772880A EP3853387B1 EP 3853387 B1 EP3853387 B1 EP 3853387B1 EP 19772880 A EP19772880 A EP 19772880A EP 3853387 B1 EP3853387 B1 EP 3853387B1
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steel sheet
rolled steel
cold rolled
temperature
anyone
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French (fr)
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EP3853387A1 (de
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Samaneh ALIBEIGI
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ArcelorMittal SA
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ArcelorMittal SA
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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
    • 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
    • B21C47/00—Winding-up, coiling or winding-off metal wire, metal band or other flexible metal material characterised by features relevant to metal processing only
    • B21C47/02—Winding-up or coiling
    • 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
    • C21D8/0221—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
    • 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
    • C21D8/0273—Final recrystallisation annealing
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • 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
    • C23C2/04—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
    • C23C2/12—Aluminium or alloys based thereon
    • 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
    • C21D2211/001—Austenite
    • 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
    • C21D2211/005—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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Definitions

  • the present invention relates to cold rolled and coated steel sheets suitable for use as steel sheet for automobiles.
  • Automotive parts are required to satisfy two inconsistent necessities, viz. ease of forming and strength but in recent years a third requirement of improvement in fuel consumption is also bestowed upon automobiles in view of global environment concerns.
  • automotive parts must be made of material having high formability in order that to fit in the criteria of ease of fit in the intricate automobile assembly and at same time have to improve strength for vehicle crashworthiness and durability while reducing weight of vehicle to improve fuel efficiency.
  • the purpose of the present invention is to solve these problems by making available cold-rolled steel and coated sheets that simultaneously have:
  • the steel sheets according to the invention may also present a yield strength 320 MPa or more
  • the steel sheets according to the invention may also present a yield strength to tensile strength ratio of 0.6 or more
  • such steel can also have a good suitability for forming, in particular for rolling with good weldability and coatability.
  • Another object of the present invention is also to make available a method for the manufacturing of these sheets that is compatible with conventional industrial applications while being robust towards manufacturing parameters shifts.
  • the cold rolled and heat treated steel sheet of the present invention may optionally be coated with zinc or zinc alloys, or with aluminium or aluminium alloys to improve its corrosion resistance.
  • Carbon is present in the steel between 0.13% and 0.18%. Carbon is an element necessary for increasing the strength of the steel sheet by producing low-temperature transformation phases such as bainite, further Carbon also plays a pivotal role in Austenite stabilization hence a necessary element for securing Residual Austenite. Therefore, Carbon plays two pivotal roles one in increasing the strength and another in retaining austenite to impart ductility. But Carbon content less than 0.13% will not be able to stabilize Austenite in an adequate amount required by the steel of present invention. On the other hand, at a Carbon content exceeding 0.18%, the steel exhibits poor spot weldability which limits its application for the automotive parts.
  • Manganese content of the steel of present invention is between 1.1 % and 1.8%. This element is gammagenous.
  • the purpose of adding Manganese is essentially to obtain a structure that contains Austenite and impart strength to the steel. An amount of at least 1.1% by weight of Manganese has been found in order to provide the strength and hardenability of the steel sheet as well as to stabilize Austenite. But when Manganese content is more than 1.8% it produces adverse effects such as it retards transformation of Austenite to Bainite during the over-aging holding for Bainite transformation. In addition the Manganese content of above 1.8% also reduces the ductility and also deteriorates the weldability of the present steel hence the elongation targets may not be achieved.
  • a preferable content for the present invention may be kept between 1.2% and 1.8%, further more preferably 1.3% and 1.7%.
  • Silicon content of the steel of present invention is between 0.5% and 0.9%. Silicon is a constituent that can retard the precipitation of carbides during overageing, therefore, due to the presence of Silicon, carbon rich Austenite is stabilized at room temperature. Further, due to poor solubility of Silicon in carbide it effectively inhibits or retards the formation of carbides, hence also promotes the formation of Bainitic structure which is sought as per the present invention to impart steel with its essential features. However, disproportionate content of Silicon does not produce the mentioned effect and leads to a problem such as temper embrittlement. Therefore, the concentration is controlled within an upper limit of 0.9%. A preferable content for the present invention may be kept between 0.6% and 0.8%
  • Aluminum is an essential element and is present in the steel between 0.6% and 1%.
  • Aluminum is an alphagenous element and imparts total elongation to the steel of present invention.
  • a minimum of 0.6% of Aluminum is required to have a minimum Ferrite thereby imparting the elongation to the steel of present invention.
  • Aluminum is also used for removing oxygen from the molten state of the steel to clean steel of present invention by and it also prevents oxygen from forming a gas phase. But whenever the Aluminum is more than 1% it forms AIN which is detrimental for the steel of Present invention therefore preferable range for the presence of the Aluminum is between 0.6% and 0.8%.
  • Phosphorus constituent of the steel of present invention is between 0.002% and 0.02%. Phosphorus reduces the spot weldability and the hot ductility, particularly due to its tendency to segregate at the grain boundaries or co-segregate with manganese. For these reasons, its content is limited to 0.02 % and preferably lower than 0.014%.
  • Sulfur is not an essential element but may be contained as an impurity in steel and from point of view of the present invention the Sulfur content is preferably as low as possible, but is 0.003% or less from the viewpoint of manufacturing cost. Further if higher Sulfur is present in steel it combines to form Sulfides especially with Manganese and reduces its beneficial impact on the steel of present invention.
  • Nitrogen is limited to 0.007% in order to avoid ageing of material and to minimize the precipitation of nitrides during solidification which are detrimental for mechanical properties of the Steel.
  • Chromium is an optional element for the present invention. Chromium content may be present in the steel of present invention is between 0.05% and 1%. Chromium is an essential element that provides strength and hardening to the steel but when used above 1% it impairs surface finish of steel. Further Chromium contents under 1% coarsen the dispersion pattern of carbide in Bainitic structures, hence; keep the density of carbides low in Bainite.
  • Molybdenum is an optional element that constitutes 0.001% to 0.5% of the Steel of present invention; Molybdenum plays an effective role in determining hardenability and hardness, delays the appearance of Bainite and avoids carbides precipitation in Bainite. However, the addition of Molybdenum excessively increases the cost of the addition of alloy elements, so that for economic reasons its content is limited to 0.5%.
  • Niobium is an optional element for the present invention.
  • Niobium content may be present in the steel of present invention between 0.001 and 0.1% and is added in the Steel of present invention for forming carbo-nitrides to impart strength of the Steel of present invention by precipitation hardening.
  • Niobium will also impact the size of microstructural components through its precipitation as carbo-nitrides and by retarding the recrystallization during heating process. Thus finer microstructure formed at the end of the holding temperature and as a consequence after the completion of annealing that will lead to the hardening of the Steel of present invention.
  • Niobium content above 0.1% is not economically interesting as a saturation effect of its influence is observed this means that additional amount of Niobium does not result in any strength improvement of the product.
  • Titanium is an optional element and may be added to the Steel of present invention between 0.001% and 0.1%. As Niobium, it is involved in carbo-nitrides formation so plays a role in hardening of the Steel of present invention. In addition Titanium also forms Titanium-nitrides which appear during solidification of the cast product. The amount of Titanium is so limited to 0.1% to avoid formation of coarse Titanium-nitrides detrimental for formability. In case the Titanium content is below 0.001% it does not impart any effect on the steel of present invention.
  • Copper may be added as an optional element in an amount of 0.01% to 2% to increase the strength of the steel and to improve its corrosion resistance. A minimum of 0.01% of Copper is required to get such effect. However, when its content is above 2%, it can degrade the surface aspects.
  • Nickel may be added as an optional element in an amount of 0.01 to 3% to increase the strength of the steel and to improve its toughness. A minimum of 0.01% is required to produce such effects. However, when its content is above 3%, Nickel causes ductility deterioration.
  • Calcium content in the steel of present invention is between 0.0001% and 0.005%. Calcium is added to steel of present invention as an optional element especially during the inclusion treatment. Calcium contributes towards the refining of Steel by arresting the detrimental Sulfur content in globular form, thereby, retarding the harmful effects of Sulfur.
  • Vanadium is effective in enhancing the strength of steel by forming carbides or carbo-nitrides and the upper limit is 0.1% due to the economic reasons.
  • Other elements such as Cerium, Boron, Magnesium or Zirconium can be added individually or in combination in the following proportions by weight: Cerium ⁇ 0.1%, Boron ⁇ 0.003%, Magnesium ⁇ 0.010% and Zirconium ⁇ 0.010%. Up to the maximum content levels indicated, these elements make it possible to refine the grain during solidification. The remainder of the composition of the Steel consists of iron and inevitable impurities resulting from processing.
  • the microstructure of the Steel sheet comprises: Ferrite constitutes from 60% to 75% of microstructure by area fraction for the Steel of present invention. Ferrite constitutes the primary phase of the steel as a matrix. In the present invention, Ferrite cumulatively comprises of Polygonal ferrite and acicular ferrite Ferrite imparts high strength as well as elongation to the steel of present invention. To ensure an elongation of 31% and preferably 33% or more it is necessary to have 60% of Ferrite. Ferrite is formed during the cooling after annealing in steel of present invention. But whenever ferrite content is present above 75% in steel of present invention the strength is not achieved.
  • Bainite constitutes from 20% to 30% of microstructure by area fraction for the Steel of present invention.
  • Bainite cumulatively consists of Lath Bainite and Granular Bainite, To ensure tensile strength of 620 MPa and preferably 630 MPa or more it is necessary to have 20% of Bainite. Bainite is formed during over-aging holding.
  • Residual Austenite constitutes from 10% to 15% by area fraction of the Steel. Residual Austenite is known to have a higher solubility of Carbon than Bainite and, hence, acts as effective Carbon trap, therefore, retarding the formation of carbides in Bainite. Carbon percentage inside the Residual Austenite of present invention is preferably higher than 0.9% and preferably lower than 1.1%. Residual Austenite of the Steel according to the invention imparts an enhanced ductility.
  • Martensite is an optional constituent and may be present between 0% and 5 % of microstructure by area fraction and found in traces.
  • Martensite for present invention includes both fresh martensite and tempered martensite.
  • Present invention form martensite due to the cooling after annealing and get tempered during overaging holding.
  • Fresh Martensite also form during cooling after the coating of cold rolled steel sheet.
  • Martensite imparts ductility and strength to the Steel of present invention when it is below 5%. When Martensite is in excess of 5 % it imparts excess strength but diminishes the elongation beyond acceptable limit.
  • the preferable limit for martensite is between 0% and 3%.
  • a total amount of Ferrite and Residual Austenite must always be between 70% and 80% to have total elongation of 31% and a minimum of 70% is required to ensure the total elongation above 31% while having a tensile strength of 600MPa.
  • Ferrite and residual austenite are soft phase in comparison to martensite and bainite therefore imparts for elongation and ductility but whenever the cumulative presence is more than 80% the strength drops beyond the acceptable limits.
  • the microstructure of the cold rolled and heat treated steel sheet is free from microstructural components, such as pearlite and cementite without impairing the mechanical properties of the steel sheets.
  • a steel sheet according to the invention can be produced by any suitable method.
  • a preferred method consists in providing a semi-finished casting of steel with a chemical composition according to the invention. The casting can be done either into ingots or continuously in form of thin slabs or thin strips, i.e. with a thickness ranging from approximately 220mm for slabs up to several tens of millimeters for thin strip.
  • a slab having the above-described chemical composition is manufactured by continuous casting wherein the slab optionally underwent the direct soft reduction during the continuous casting process to avoid central segregation and to ensure a ratio of local Carbon to nominal Carbon kept below 1.10.
  • the slab provided by continuous casting process can be used directly at a high temperature after the continuous casting or may be first cooled to room temperature and then reheated for hot rolling.
  • the temperature of the slab which is subjected to hot rolling, isat least 1150° C and must be below 1280°C.
  • the temperature of the slab is preferably sufficiently high so that hot rolling can be completed in the temperature range of Ac1 +50°C to Ac1+250°C and preferably between Ac1+50°C and Ac1+200°C while always having final rolling temperature remains above Ac1+50°C. Reheating at temperatures above 1280°C must be avoided because they are industrially expensive.
  • a final rolling temperature range between Ac1 +50°C to Ac1+250°C is preferred to have a structure that is favorable to recrystallization and rolling. It is necessary to have final rolling pass to be performed at a temperature greater than Ac1 +50°C, because below this temperature the steel sheet exhibits a significant drop in rollability.
  • the sheet obtained in this manner is then cooled at a cooling rate above 30°C/s to the coiling temperature which must be below 625°C. Preferably, the cooling rate will be less than or equal to 200° C/s.
  • the hot rolled steel sheet is then coiled at a coiling temperature below 625°C to avoid ovalization and preferably below 600°C to avoid scale formation.
  • the preferred range for such coiling temperature is between 350° C and 600° C.
  • the coiled hot rolled steel sheet may be cooled down to room temperature before subjecting it to optional hot band annealing.
  • the hot rolled steel sheet may be subjected to an optional scale removal step to remove the scale formed during the hot rolling before optional hot band annealing.
  • the hot rolled sheet may then subjected to an optional Hot Band Annealing at temperatures between 400°C and 750°C for at least 12 hours and not more than 96 hours, the temperature remaining below 750°C to avoid transforming partially the hot-rolled microstructure and, therefore, losing the microstructure homogeneity.
  • an optional scale removal step of this hot rolled steel sheet may performed through, for example, pickling of such sheet.
  • This hot rolled steel sheet is subjected to cold rolling to obtain a cold rolled steel sheet with a thickness reduction between 35 to 90%.
  • the cold rolled steel sheet obtained from cold rolling process is then subjected to annealing to impart the steel of present invention with microstructure and mechanical properties.
  • step one cold rolled steel sheet is heated at a heating rate between 10°C/s and 40°C/s to a temperature range between 550°C and 650°C. Thereafter in subsequent second step of heating the cold rolled steel sheet is heated at a heating rate between 1°C/s and 5°C/s to the soaking temperature of annealing.
  • the cold rolled steel sheet is preferably held at the soaking temperature during 10 to 500 seconds to ensure at least 30% transformation to Austenite microstructure of the strongly work-hardened initial structure. Then the cold rolled steel sheet is then cooled in two step cooling to an over-aging holding temperature. In step one of cooling the cold rolled steel sheet is cooled at cooling rate less than 5°C/s and preferably less than 3°C/s to a temperature range between 600°C and 720°C and preferably between 625°C and 720°C. During this step one of cooling ferrite matrix of the present invention is formed.
  • the cold rolled steel sheet is cooled to an overaging temperature range between 250°C and 470°C at a cooling rate between 10°C/s and 100°C/s. Then the cold rolled steel sheet is held in the over-aging temperature range during 5 to 500 seconds. The cold rolled steel sheet is then brought to the temperature to a coating bath temperature range of 400°C and 480°C to facilitate coating of the cold rolled steel sheet. Then the cold rolled steel sheet is coated by any of the known industrial processes such as Electro-galvanization, JVD, PVD, Hot dip(GI) etc.
  • Table 1 Steel sheets made of steels with different compositions are gathered in Table 1, where the steel sheets are produced according to process parameters as stipulated in Table 2, respectively. Thereafter Table 3 gathers the microstructures of the steel sheets obtained during the trials and table 4 gathers the result of evaluations of obtained properties.
  • Table 1 Sample Steels C Mn Si Al P S N Other elements present A 0.155 1.54 0.696 0.728 0.014 0.002 0.003 - B 0.157 1.54 0.690 0.721 0.014 0.002 0.003 - C 0.148 1.54 0.698 0 0.013 0.0027 0.0044 - D 0.114 1.62 0.293 0.031 0.027 0.0028 0.005 -Ni:0.025, Cr: 0.345 underlined values: not according to the invention.
  • Table 2 gathers the annealing process parameters implemented on steels of Table 1.
  • the Steel compositions A and B serve for the manufacture of sheets according to the invention.
  • This table also specifies the reference steels which are designated in table as C and D .
  • Table 2 also shows tabulation of Ac1 and Ac3.
  • the table 2 is as follows :
  • Table 3 exemplifies the results of the tests conducted in accordance with the standards on different microscopes such as Scanning Electron Microscope for determining the microstructures of both the inventive and reference steels.
  • Table 4 exemplifies the mechanical properties of both the inventive steel and reference steels.
  • tensile tests are conducted in accordance of JIS Z2241 standards.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Claims (20)

  1. Kaltgewalztes Stahlblech, das eine Zusammensetzung aufweist, die die folgenden Elemente umfasst, ausgedrückt in Gewichtsprozent:
    0,13 % ≤ Carbon ≤0,18 %
    1,1 % ≤ Mangan ≤ 1,8%
    0,5 % ≤ Silicon ≤ 0,9 %
    0,6 % ≤ Aluminium ≤ 1%
    0,002 % ≤ Phosphor ≤ 0,02 %
    0 % ≤ Schwefel ≤ 0,003 %,
    0 % ≤ Stickstoff ≤ 0,007%
    und die eines oder mehrere der folgenden optionalen Elemente enthalten kann
    0,05% ≤ Chrom ≤ 1 %
    0,001% ≤ Molybdän ≤ 0, 5 %
    0,001% ≤ Niobium ≤ 0,1 %
    0,001 % ≤ Titan ≤ 0,1 %
    0,01 % ≤ Kupfer ≤ 2 %
    0,01% ≤ Nickel ≤3 %
    0,0001% ≤ Calcium ≤ 0,005 %
    0 % ≤ Vanadium ≤ 0,1 %
    0 % ≤ Bor ≤ 0,003 %
    0 % ≤ Cerium ≤ 0,1 %
    0 % ≤ Magnesium ≤ 0,010 %
    0 % ≤ Zirkon ≤ 0,010 %
    wobei die restliche Zusammensetzung aus Eisen und unvermeidlichen, durch die Verarbeitung verursachten Verunreinigungen besteht, die Mikrostruktur des Stahlblechs umfassend in Flächenfraktion 60 bis 75 % Ferrit, 20 bis 30 % Bainit, 10 bis 15 % Restaustenit und 0 bis 5 % Martensit, wobei die kumulierten Mengen an Restaustenit und Ferrit zwischen 70 und 80 % sind.
  2. Kaltgewalztes Stahlblech nach Anspruch 1, wobei die Zusammensetzung 0,6 bis 0,8 % Silizium beinhaltet.
  3. Kaltgewalztes Stahlblech nach Anspruch 1 oder 2, wobei die Zusammensetzung 0,14 % bis 0,18 % Kohlenstoff beinhaltet.
  4. Kaltgewalztes Stahlblech nach Anspruch 3, wobei die Zusammensetzung 0,6 % bis 0,8 % Aluminium beinhaltet.
  5. Kaltgewalztes Stahlblech nach einem von Anspruch 1 bis 4, wobei die Zusammensetzung 1,2 % bis 1,8 % Mangan beinhaltet.
  6. Kaltgewalztes Stahlblech nach Anspruch 5, wobei die Zusammensetzung 1,3 bis 1,7 % Mangan beinhaltet.
  7. Kaltgewalztes Stahlblech nach einem der Ansprüche 1 bis 6, wobei die kumulierten Mengen an Ferrit und Restaustenit zwischen 73 % und 80 % sind und der Prozentsatz an Restaustenit weniger als 13% ist.
  8. Kaltgewalztes Stahlblech nach einem der Ansprüche 1 bis 7, wobei die Menge an Martensit zwischen 0 % und 3% ist.
  9. Kaltgewalztes Stahlblech nach einem von Anspruch 1 bis 8, wobei der Kohlenstoffgehalt von Restaustenit zwischen 0,9 bis 1,1 % ist.
  10. Kaltgewalztes Stahlblech nach einem der Ansprüche 1 bis 9, wobei das Stahlblech eine Zugfestigkeit von 600 MPa oder mehr und eine Gesamtdehnung von 31 % oder mehr aufweist.
  11. Kaltgewalztes Blech nach Anspruch 10, wobei das Stahlblech eine Streckgrenze von 320 MPa oder mehr und eine Gesamtdehnung von 33 % oder mehr aufweist.
  12. Kaltgewalztes Stahlblech nach einem der Ansprüche 1 bis 11, wobei das Stahlblech beschichtet ist.
  13. Verfahren zur Herstellung eines kaltgewalzten Stahlblechs, umfassend die folgenden aufeinanderfolgenden Schritte:
    - Bereitstellen einer Zusammensetzung nach einem der Ansprüche 1 bis 6;
    - Wiedererhitzen des Halbfertigprodukts auf eine Temperatur zwischen 1150 °C und 1280 °C;
    - Walzen des besagten Halbfertigprodukts in dem austenitischen Bereich, wobei die Warmwalzabschlusstemperatur zwischen Ac1+50 °C und Ac1+250 °C sein muss, um ein warmgewalztes Stahlblech zu erlangen;
    - Abkühlen des Blechs mit einer Abkühlungsgeschwindigkeit von über 30 °C/s auf eine Aufspultemperatur von unter 625 °C; und Aufspulen des warmgewalzten Blechs;
    - Abkühlen des warmgewalzten Blechs auf Raumtemperatur;
    - optional Ausführen von Zunderentfernungsverfahren an dem warmgewalzten Stahlblech;
    - optional Glühen des warmgewalzten Stahlblechs bei einer Temperatur zwischen 400 °C und 750 °C;
    - optional Ausführen von Zunderentfernungsverfahren an dem warmgewalzten Stahlblech;
    - Kaltwalzen des warmgewalzten Stahlblechs mit einem Reduktionsgrad zwischen 35 und 90 %, um ein kaltgewalztes Stahlblech zu erlangen,
    - dann Ausführen eines Glühens bei einer Durchwärmtemperatur zwischen Ac1 +30 °C und Ac3 über eine Dauer zwischen 10 und 500 Sekunden durch Erhitzen des kaltgewalzten Stahlblechs in einem zweistufigen Erhitzen, wobei:
    ∘ in Schritt eins des Erhitzens das kaltgewalzte Stahlblech mit einer Erhitzungsgeschwindigkeit zwischen 10 °C/s und 40 °C/s auf einen Temperaturbereich zwischen 550 °C und 650 °C erhitzt wird;
    ∘ in Schritt zwei das kaltgewalzte Stahlblech mit einer Erhitzungsgeschwindigkeit zwischen 1 °C/s und 5 °C/s von einem Temperaturbereich zwischen 550 °C und 650 °C auf die Glühtemperatur erwärmt wird, bei der es gehalten wird,
    - anschließend Abkühlen des kaltgewalzten Stahlblechs in einem zweistufigen Abkühlen, wobei:
    ∘ in Schritt eins des Abkühlens das kaltgewalzte Stahlblech mit einer Abkühlungsgeschwindigkeit von weniger als 5 °C/s auf eine Temperatur zwischen 600 °C und 720 °C abgekühlt wird
    ∘ dann in Schritt zwei das Blech mit einer Abkühlungsgeschwindigkeit zwischen 10 °C/s und 100 °C/s von einem Temperaturbereich zwischen 600 °C und 720 °C auf eine Überalterungstemperatur abgekühlt wird
    - dann das kaltgewalzte Stahlblech bei einer Temperatur zwischen 250 °C und 470 °C über 5 bis 500 Sekunden überhitzt wird, und
    - dann auf Raumtemperatur abgekühlt wird, um ein kaltgewalztes Stahlblech zu erlangen.
  14. Verfahren nach Anspruch 13, wobei die Abkühltemperatur unter 600 °C ist.
  15. Verfahren nach Anspruch 13 oder 14, wobei die Abschlusswalztemperatur zwischen Ac1 +50 °C and Ac1 +200 °C ist.
  16. Verfahren nach einem der Ansprüche 13 bis 15, wobei die Abkühlgeschwindigkeit nach Glühen in dem Temperaturbereich zwischen 625 °C und 720 °C weniger als 3 °C/s ist.
  17. Verfahren zur Herstellung eines kaltgewalzten Stahlblechs nach einem der Ansprüche 13 bis 16, wobei das kaltgewalzte Stahlblech zwischen Ac1 +30 °C und Ac3 geglüht wird und die Glühtemperatur gewählt ist, um das Vorhandensein von mindestens 30 % Austenit am Ende des Durchwärmens sicherzustellen.
  18. Verfahren zur Herstellung eines kaltgewalzten Stahlblechs nach einem der Ansprüche 13 bis 17, wobei das kaltgewalzte Stahlblech in einem Temperaturbereich zwischen 400 °C und 480 °C beschichtet werden kann.
  19. Verwendung eines Stahlblechs nach einem der Ansprüche 1 bis 12 oder eines Stahlblechs, das gemäß dem Verfahren der Ansprüche 13 bis 18 erzeugt wird, zur Herstellung von Struktur- oder Sicherheitsteilen eines Fahrzeugs.
  20. Fahrzeug, umfassend ein Teil, das gemäß Anspruch 19 erlangt wird.
EP19772880.1A 2018-09-20 2019-09-17 Kaltgewalztes und beschichtetes stahlblech und verfahren zu seiner herstellung Active EP3853387B1 (de)

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BR112023024874A2 (pt) * 2021-06-16 2024-02-15 Arcelormittal Método para produzir uma peça de aço e peça de aço
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WO2018115935A1 (en) * 2016-12-21 2018-06-28 Arcelormittal Tempered and coated steel sheet having excellent formability and a method of manufacturing the same

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CN112689684A (zh) 2021-04-20
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UA126725C2 (uk) 2023-01-11
WO2020058748A1 (en) 2020-03-26
KR20210061382A (ko) 2021-05-27
MX2021003290A (es) 2021-05-13
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