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    • 专利摘要:
    steel sheet, method for producing a cold rolled and hot dip coated steel sheet and use of a steel sheet. the invention deals with a sheet of cold-rolled steel and of hot immersion, with a tensile strength of at least 980 mpa, with resistance to deformation above or equal to 500 mpa, with total elongation above or equal to 8% , the composition consisting of weight percent: 0.05 <c <0.15%, 2 <mn = 3%, al <0.1%, 0.3 <si <1.5%, 0.01% < nb <0.05%, n <0.02%, 0.1 <cr + mo <1%, 0.0001 <b <0.0025, ti <0.5%, v <0.01%, s <0.01%, p <0.05% the rest of the composition being iron and unavoidable impurities that result from melting and the microstructure contains, in surface fraction: between 50 and 95% of martensite and between 5 and 50% of the sum of ferrite and bainite, where the ferrite grain size is below 10 µm, and where the aspect ratio of the ferrite grain size is between 1 and 3. the steel according to the invention is oxidized and subsequently reduced during the heating, soaking and cooling annealing steps.
    公开号:BR112016027681B1
    申请号:R112016027681-7
    申请日:2015-06-03
    公开日:2021-04-27
    发明作者:Dongwei Fan；Hyun Jo Jun；John A. Rotole
    申请人:Arcelormittal；
    IPC主号:
    专利说明:

    FIELD OF THE INVENTION
    [001] The present invention relates to high strength multiphase steels, for use in motor vehicles, which have high malleability properties and exhibit high levels of resistance, and are intended to be used as structural members and reinforcement materials mainly for motor vehicles. It also deals with the method of producing highly malleable multiphase steel. BACKGROUND OF THE INVENTION
    [002] As the use of high strength steels increases in automotive applications, there is an increasing demand for steels of increased strength without sacrificing malleability. Increasing demands for weight savings and safety requirements motivate intensive elaborations of new automotive steel concepts that can achieve higher ductility simultaneously with higher strength compared to existing Advanced High Strength Steels (AHSS).
    [003] Thus, several steel families such as those mentioned below that offer various levels of resistance have been proposed.
    [004] Among those concepts, steels with microalloying elements whose hardening is obtained simultaneously by precipitation and by refining the grain size were developed. The development of such high strength and low alloy steels (HSLA) was followed by those of higher strength called Advanced High Strength Steels which maintain good strength levels together with good cold malleability. However, the levels of traction achieved by these degrees are generally low.
    [005] In order to respond to the demand for steels with high strength and at the same time high malleability, many developments have taken place. However, it is well known that for high strength steels, trying to increase the ultimate tensile strength in general leads to lower ductility levels. Nevertheless, car manufacturers continue to develop more and more complex parts that require more ductility without sacrificing strength requirements. In addition, an improvement in resistance to deformation and hole expansion performance in relation to steels currently in production is necessary, for example, for hot-dip coated steel sheets.
    [006] The invention is directed to a method of making high-strength steel coated by hot dip, the method of producing it and the use of said high-strength steel to produce a part of a vehicle.
    [007] US order US2013008570 is known, such an order deals with an ultra-high strength steel plate with at least 1,100 MPa of tensile strength that has both an excellent stretch-strength balance and excellent bending operability and a method for produce the same. The metal structure of the steel plate has martensite, and the soft phases of bainitic ferrite and polygonal ferrite. The area of the aforementioned martensite constitutes 50% or more, the area of the aforementioned bainitic ferrite constitutes 15% or more, and the area of the aforementioned polygonal ferrite constitutes 5% or less (including 0%). When the diameter equivalent to the circle of the aforementioned soft phase is measured, the coefficient of variation (standard deviation / average value) is less than or equal to 1.0. The ultra-high strength steel plate has at least 1,100 MPa of tensile strength. This request is omitted with regard to different malleability issues such as hole expansion and resistance to deformation which have an important impact on the properties of use.
    [008] It is also known the application WO2012153016, which deals with cold rolled steel whose tensile strength is above 1000 MPa and uniform elongation above 12%, as well as V-bending capacity above 90 °. The chemical composition of this application comprises, in percentage by weight: 0.15% <C <0.25%, 1.8% <Mn <3.0%, 1.2% <Si <2%, 0% <Al <0.10%, 0% <Cr <0.50%, 0% <Cu <1%, 0% <Ni <1%, 0% <S <0.005%, 0% <P <0.020%, Nb < 0.015%, Ti <0.020%, V <0.015%, Co <1%, N <0.008%, B <0.001% while Mn + Ni + Cu <3%, the remainder being Fe and unavoidable impurities from the mold. The steel microstructure contains, in percentage of surface, 5 to 20% of polygonal ferrite, between 10 and 15% of residual austenite, of 5 to 15% of martensite, the balance being of clapboard bainite. This order requires that austenite be stabilized through the process of continuous annealing. DESCRIPTION OF THE INVENTION
    [009] The objective of the invention is to solve the problems mentioned above, that is, to bring a high-strength steel coated by hot immersion simultaneously:
    [010] A tensile strength above or equal to 980 MPa, or even 1,180 MPa.
    [011] A total elongation above or equal to 8%.
    [012] A hole expansion value greater than or equal to 20%, or even 40%.
    [013] A deformation resistance value above 500 MPa, or even 780 MPa.
    [014] Another objective of the invention is to provide a process for making such hot dip coated multiphase steel, while being compatible with normal continuous annealing galvanizing lines.
    [015] To do this, the main objective of the invention is a hot-dip coated steel sheet with a tensile strength of at least 980 MPa, with resistance to deformation above or equal to 500 MPa, with total elongation above or equal to 8%, whose composition consists, in percentage by weight, of: 0.05 <C <0.15% 2 <Mn <3% Al <0.1% 0.3 <Si <1.5% 0, 01% <Nb <0.05% N <0.02% 0.1 <Cr + Mo <1% 0.0001 <B <0.0025% Ti <0.5% V <0.01% S <0 , 01% P <0.05% the rest of the composition being iron and unavoidable impurities that result from melting and the microstructure consists, in surface fraction, of: between 50 and 95% of martensite and between 5 and 50% of the sum of ferrite and bainite, where the ferrite grain size is below 10 μm, and where the aspect ratio of the ferrite grain size is between 1 and 3.
    [016] In a preferred embodiment, the chemical composition of steel has a carbon content such that 0.09 <C <0.14%.
    [017] In another preferred embodiment, steel has a manganese content such that 2.2 <Mn <2.7%.
    [018] In another preferred embodiment, steel has an aluminum content such that Al <0.05%.
    [019] In another preferred embodiment, steel has a silicon content such that 0.6 <Si <1.3%.
    [020] In another preferred embodiment, the chemical composition of steel has a niobium content such that Nb <0.03%.
    [021] In another preferred embodiment, the chemical composition of steel has a sum of chromium and molybdenum such that 0.1 <Cr + Mo <0.7%.
    [022] In another preferred embodiment, the chemical composition of steel has a boron content such that 0.001 <B <0.0022%.
    [023] In another preferred embodiment, the chemical composition of steel has a titanium content such that: 0.02% <Ti <0.05%.
    [024] In another preferred embodiment, the steel sheet has an internally oxidized depth of at least 200 nm and less than 100 μm, comprising one or more of oxides containing Si, Mn, Al, Ti, present under the dip coating the hot.
    [025] In a preferred embodiment, the surface fraction of the sum of ferrite and bainite is between 20 and 40%, with the average ferrite grain size below 3 μm.
    [026] Preferably, the hot-dip coated steel of the invention has a tensile strength of at least 980 MPa, deformation resistance is at least 500 MPa, the total elongation is at least 8% and the expansion of bore is at least 20%.
    [027] Preferably, the hot dip coated steel of the invention has a tensile strength of at least 1,180 MPa, a deformation resistance of at least 780 MPa, a total elongation of at least 8% and a bore expansion of at least minus 20%.
    [028] Preferably, the steel according to the invention is galvanized or annealed after galvanizing.
    [029] The invention also has, as a second objective, a method for producing a hot-dip coated sheet of high strength steel comprising the following successive steps: - shaping a steel whose composition is according to the invention as defined above in order to obtain a rebar, - reheat the rebar to a Treheat temperature above 1,180 ° C, - hot-laminate the rebar reheated to a temperature above 800 ° C to obtain a hot-rolled steel, - cool the cold-rolled steel hot at a conventional cooling rate to a Tcoiling winding temperature between 500 and 800 ° C, then - wind the Tcoiling-cooled hot-rolled steel, - peel the hot-rolled steel - Optionally, the hot-rolled steel is annealed to a TIA temperature above 300 ° C for more than 20 minutes. - Optionally, the temperature of the hot rolled steel before entering the cover must be above 400 ° C. The cooling rate of hot rolled steel should be lower than or equal to 1 ° C / min and higher than or equal to 0.01 ° C / min. - cold-rolling the steel in order to obtain a cold-rolled steel sheet, - annealing the cold-rolled steel sheet comprising the steps of: - heating said cold-rolled steel sheet in an oven with direct fire having an atmosphere with a percentage by volume of excess oxygen between 0.2% and 4%, in which an oxidation stage takes place between 500 ° C and 750 ° C, - increase the heating from the said oven temperature with direct fire until an annealing temperature in a radiation tube oven, the heating rate being between 0.5 and 2.5 ° C / s, the dew point of the atmosphere in said radiation tube oven being below or equal to 25 ° C, - said Tanneal annealing temperature being between 750 to 950 ° C. - keep the steel at said annealing temperature Tanneal for a duration of at least 30 seconds and less than or equal to 300 seconds, - cool the cold rolled steel to a TOA temperature between 440 ° C and 470 ° C, - hold the cold rolled steel to TOA for more than 30 seconds and less than 180 seconds, - and during said heating, remaining in Tanneal and in the cooling stages, the surface of the cold rolled steel is oxidized and subsequently reduced in order to obtain an internally oxidized depth of at least 200 nm and less than 100 μm, comprising one or more of oxides containing Si, Mn, Al, Ti, - Hot-dip cold-rolled steel to obtain coated cold-rolled steel , - optionally, cold-rolled hot-dip coated steel is annealed after galvanizing to achieve an iron content between 7% and 15% in the cold-rolled steel coating. - cold-rolled hot-dip coated steel is cooled to room temperature at a cooling rate of at least 1 ° C / s.
    [030] Preferably, the winding temperature is such that: 500 ° C <Tcoiling <750 ° C.
    [031] In a preferred embodiment, the optional annealing temperature TIA is such that 500 ° C <TIA <650 ° C for a time between 30 hours and 100 hours.
    [032] Preferably, the reduction ratio of cold rolling is comprised between 40 and 60%.
    [033] In a preferred embodiment, the surface of the cold rolled steel is reduced within said radiant tube furnace having a mixed gas atmosphere having a dew point below 0 ° C.
    [034] Preferably, the hot-dip coating is done in a bath of liquid Zn alloy in order to obtain a hot-dip galvanized or hot-rolled high-strength steel after galvanizing.
    [035] The steel according to the invention can be used to produce a part for a motor vehicle. BRIEF DESCRIPTION OF THE DRAWINGS
    [036] The main aspects of the invention will now be described: Figure 1 illustrates a microstructure of the steel according to the invention with martensite in white, ferrite and bainite in black. DESCRIPTION OF ACCOMPLISHMENTS OF THE INVENTION
    [037] In order to obtain the steel of the invention, the chemical composition is very important as well as the production parameters in order to achieve all objectives. The elements of chemical composition are given in percentage by weight.
    [038] Carbon is an element used to increase the resistance of martensite, if the carbon content is below 0.05%, the tensile strength of a minimum of 980 MPa is not achieved in the present invention. If the carbon is higher than 0.15%, the martensite will be hard and the total elongation of 8% will not be achieved in the steel of the present invention. In addition, carbon is a strong austenite-forming element. Lowering the carbon content, from 0.15% to lower, makes it possible to have, for a given annealing temperature, less austenite and ferrite enough to improve the malleability and reach the target total elongation. In addition, low annealing temperatures for the steel according to the invention considerably limit the growth of ferrite grain; as a consequence, the final ferritic grain size is below 10 microns. This combination contributes to the great compromise of mechanical properties obtained in the steel according to the invention.
    [039] Preferably, the carbon content is such that 0.09 <C <0.14%.
    [040] Manganese is a hardening element. If the Mn content is below 2%, the tensile strength will be lower than 980 MPa. If the Mn content is above 3%, the central Mn segregation is expected to be half thick and this will be detrimental to the Properties in Use. Preferably, the manganese content is such that 2.2 <Mn <2.7% .
    [041] Silicon has an effect of increasing the strength, it improves the total elongation and the bore expansion ratio as well as resistance to delayed fracture. If the Si content is below 0.3%, the total elongation will be below 8% and the aforementioned properties will be impaired. If the Si content is above 1.5%, the rolling loads increase too much and the cold rolling process becomes difficult. In addition, the soaking temperature will be very high, this will lead to manufacturing capacity issues. In addition, the ability to coat with hot dip coating can be impaired due to the formation of silicon oxide on the surface of the sheet. Preferably, the Si content is such that 0.6 <Si <1.3 for the reasons given above.
    [042] Aluminum, like titanium, can form AlN to protect boron. However, its content is limited to 0.1% because higher Al levels will lead to higher annealing temperatures having the same microstructural balance, all other parameters being the same. As a consequence, for cost and energy saving purposes, its content is limited to 0.1%. Preferably, the content of Al is such that Al <0.05%.
    [043] Niobium can form precipitates, which have a grain-refining effect, known to increase tensile strength. In addition, it improves the bore expansion ratio as well as the delayed fracture resistance. If the Nb content is above 0.05%, ductility will be reduced and the total elongation will drop below 8%. The Nb content must be above 0.01% to obtain sufficient grain refinement and tensile strength. Preferably, the Nb content is such that Nb <0.03%.
    [044] Mo and Cr will improve hardenability and tensile strength. If the sum of these elements is below 0.1%, a large fraction of ferrite will form in addition to the growth of the proeutetoid ferrite grain formed during annealing and this will decrease the strength. If the sum of these elements is above 1% in the steel of the invention, this will make the hot strip hard and difficult to cold-roll. Preferably the sum of these elements is such that 0.1 <Cr + Mo <0.7%.
    [045] Titanium is added to combine with nitrogen to form TiN and as a consequence protect B in solid solution, if neither Ti nor Al are present, boron nitride can form. In this case, boron would not be in a solid solution nor would it perform its role defined below. In addition, the formation of TiN improves malleability and weldability, as well as delayed fracture resistance in the steel of the invention. Above 0.5%, Ti will lead to higher annealing temperatures having the same microstructural balance, all other parameters being the same. As a consequence, for cost and energy saving purposes, its content is preferably limited to 0.05%. Preferably, the Ti content is such that 0.02 <Ti <0.05%. In a preferred embodiment, the Ti content is at least 3.4 times the nitrogen content, in order to ensure its combination with nitrogen and obtain efficient grain refinement.
    [046] Boron can suppress the formation of ferrite during the cooling step of the cold rolled strip annealing. As a result, this prevents a drop in strength below 980 MPa. If the boron content is above or equal to 0.0025% (25 ppm), excess boron will precipitate as boron nitride within austenitic grain limits and these will serve as nucleation sites for the formation of ferrite with the same effect of falling traction on mechanical properties. Below 0.0001% (1 ppm) higher grades in terms of tensile strength are more difficult to achieve. Ideally, boron needs to be 0.001 <B <0.0022% to obtain mechanical properties above 1,180 MPa with a minimum of 8% total elongation.
    [047] As for vanadium, if the content is above 0.01%, vanadium will consume carbon forming carbides and / or nitrocarbons and this will soften the martensite. In addition, the ductility of the steel according to the invention will be impaired and will fall below 8%.
    [048] As for nitrogen, if the nitrogen content is above 0.02%, boron nitrides will form and reduce the hardenability of the steel since low free boron content will be available. It will also form a large fraction of AlN, which is detrimental to total elongation and bore ratio expansion. As a consequence, the nitrogen content is limited to 0.02% so as not to fall below 8% elongation and / or 20% bore ratio expansion.
    [049] As for phosphorus, at levels above 0.050 weight percent, phosphorus segregates along steel boundaries and causes deterioration of delayed fracture resistance and weldability of the steel sheet. The phosphorus content should therefore be limited to 0.050 weight percent.
    [050] As for sulfur, levels above 0.01 percent by weight lead to a large amount of non-metallic inclusions (MnS), and this causes deterioration of delayed fracture resistance and ductility of the steel sheet. Consequently, the sulfur content should be limited to 0.01 weight percent.
    [051] The steel balance according to the invention is made of iron and unavoidable impurities.
    [052] The method for producing steel according to the invention involves shaping steel with the chemical composition of the invention.
    [053] Molded steel is reheated to above 1,180 ° C. When the rebar reheat temperature is below 1,180 ° C, the steel will not be homogeneous and the precipitates will not be completely dissolved.
    [054] Then the rebar is hot rolled, the last hot rolling mill going at a Tlp temperature of at least 800 ° C. If the Tlp is below 800 ° C, hot operability is reduced and cracks will appear and the rolling forces will increase, - cool the steel at a typical cooling rate known to you by a person skilled in the art to the temperature of winding Tcoiling, - Tcoiling must be lower than the temperature of the last pass Tlp ° C. This temperature is preferably below 800 ° C. Preferably, the winding temperature is such that 500 ° C ≤ Tcoiling ≤ 750 ° C, - after winding, the hot rolled steel is peeled, - then, optionally, the hot rolled steel is annealed at a temperature above 300 ° C for more than 20 minutes. If the heat treatment is carried out below 300 ° C, the forces for cold rolling will be very high and in less than 20 minutes the same result will be obtained, the material will be too hard to be easily cold rolled. In addition, the inventors have found that this intermediate heat treatment greatly improves sheet thickness homogeneity in a surprising way. Preferably, the heat treatment is carried out between 500 ° C and 650 ° C for 30 hours up to 100 hours, - optionally, the hot rolled steel is placed under a cover, insulated if necessary, to cover one or more windings to facilitate uniform cooling of the hot rolled product. In addition, the inventors have found that this coating treatment can also improve the homogeneity of sheet thickness, - in a preferred embodiment, the temperature of the hot-rolled steel before entering the layer must be above 400 ° C. The cooling rate of the steel must be lower than or equal to 1 ° C / min and higher than or equal to 0.01 ° C / min. If the cooling rate is higher than 1 ° C / min, the hot strip will be too hard to follow cold rolling. A cooling rate lower than 0.01 ° C / min would be detrimental to productivity, - cold-rolling the steel with a cold-rolling ratio that will depend on the final target thickness. The cold rolling ratio is defined by: (thickness before cold rolling) - (thickness after cold rolling) / (thickness before cold rolling). Preferably the cold reduction ratio is between 40 and 60%. Thus, the stored stress energy is adequate to ensure additional recrystallization during annealing, - heat the steel to the Tanneal annealing temperature which needs to be between 750 ° C and 950 ° C.
    [055] The cold rolled steel sheet is additionally annealed continuously in order to obtain recrystallization and to obtain the desired microstructure by transformation. Annealing comprises the following steps:
    [056] The cold-rolled sheet is heated in an oven with direct fire (or "DFF") within an atmosphere having an excess volume percentage of oxygen between 0.2% and 4%. The excess oxygen volume refers to the oxygen that is present in addition to the amount of oxygen needed to combine with the fuel used to heat the oven, ie: percentage of excess oxygen volume = (total oxygen volume - oxygen volume required for combustion) / (total oxygen volume) so, when excess oxygen is present in the combustion atmosphere within the proportion of the invention, it is available to react with the steel strip. In the range between 500 and 750 ° C, oxidation occurs, that is, an iron oxide layer is formed on the surface of the steel sheet while an internal oxidation occurs under this iron oxide: internal oxides within a depth of 100 μm, which may contain one or more of Si, Mn, Al, Ti, are thus created. If the oxidation depth is above 100 μm, the steel surface will be heavily oxidized, which will be difficult to reduce, and the coating quality will be deteriorated, - the steel sheet is further heated from that temperature range. oxidation to a Tanneal annealing temperature, in a radiation tube oven, the heating rate being between 0.5 and 2.5 ° C / s. If the heating rate is below 0.5 ° C / s, excessive grain growth will reduce the resistance to final deformation. If the heating rate is above 2.5 ° C / s, a lot of energy will be consumed.
    [057] The atmosphere in the radiant tube oven is a mixed gas atmosphere having a dew point below 25 ° C. Higher than 25 ° C will cause excessive oxidation of the steel surface, which can impact the coating quality.
    [058] In a preferred embodiment, the dew point is below 0 ° C to obtain a very good surface quality, - the steel is additionally annealed continuously in the radiation tube furnace, under the same atmospheric conditions , at Tanneal temperature between 750 ° C and 950 ° C and maintained at that temperature for 30 to 300 seconds. Controlling the annealing temperature is an important feature of the process since it enables to control the initial fractions of austenite and ferrite as well as their chemical composition. Below 750 ° C, the ferrite will not be fully recrystallized and the elongation will be below 8%, while it is useless to go above 950 ° C for reasons of energy and cost savings. Preferably, the annealing is done at a temperature between 775 and 860 ° C.
    [059] The steel sheet is then further cooled to a TOA temperature, - during these heating, annealing and cooling steps, the steel is oxidized and then reduced, that is, so that the iron oxide layer on the sheet surface of steel, mentioned above, is totally reduced, while an internal oxidized zone, with a depth between 200 nm and 100 μm, comprising one or more among oxides containing Si, Mn, Al, Ti, is present. This oxidation followed by a reduction step is necessary so that the steel surface is suitable for hot dip coating, - after cooling, the steel is kept at a temperature between 440 ° C to 470 ° C for more than 30 seconds. less than 180 seconds. Below 440 ° C, a large fraction of bainite or martensite will be formed and either the tensile strength or the total elongation will be below the expectations of the present invention: 980 MPa and 8% respectively. Above 470 ° C, hot-dip issues will appear with vaporization of the melt and the reaction between melt and strip will be uncontrolled, - then the steel is hot-dip coated to obtain a cold-rolled coated steel, preferably the hot-dip coating. hot dipping is done in a bath of Zn or Zn alloy in order to obtain a cold-rolled galvanized high-strength steel, - optionally, cold-rolled hot-dip coated steel is bonded to the substrate in order to obtain a high-strength steel cold rolled annealed after galvanizing, the Zn or Zn alloy coating containing between 7 to 15% iron.
    [060] The internal oxidized zone is present under the coating of Zn or Zn alloy, - then cold-rolled hot-dip coated steel is cooled to room temperature at a cooling rate of at least 1 ° Cs.
    [061] Ferrite in the framework of the present invention is defined by a cubic center structure with a grain size lower than 10 microns (μm). The sum of the ferrite and bainite content, within the framework of the invention, needs to be between 5 and 50% in order to have at least 8% of total elongation; when the sum of ferrite and bainite is below 5%, such an elongation level will not be reached. Above 50% of the sum of ferrite and bainite, the target tensile strength of 980 MPa will not be achieved. Preferably, the sum of ferrite and bainite content is between 5 and 30%. In another embodiment, the sum of ferrite and bainite content is between 20 and 40%.
    [062] In a preferred embodiment, the ferrite grain size is below 10 μm, preferably it is below 5 μm and even more preferably it is below 3 μm. The low grain size ferrite, that is, below 10 μm, improves the resistance to deformation. This range of ferrite content with limited size is obtained thanks to the combination of low annealing temperatures, elements of chemical composition such as Nb and Ti which fix ferritic grain sizes and limit their growth as well as the presence of Cr and Mo which limit the formation of ferrite upon cooling after annealing. Above 10 μm, the resistance to deformation will be very low and below the target of 500 MPa.
    [063] In a still preferred embodiment, the aspect ratio of the ferrite grain size, that is, the average values of the length to height ratios of each ferrite grain is between 1 and 3. Such measurements are taken at least 3 populations of ferrite grains, the analyzed samples being observed with an optical electron microscope or a scanning one in the third material thickness for the purpose of homogeneity. This aspect ratio of ferrite grain size improves the homogeneity of properties, if the ferrite grain size are needle types, that is, above 3 or below 1, the difference in properties between longitudinal and transverse direction will be very high and the material properties will be heterogeneous and very dependent on the stress direction.
    [064] Martensite is the structure formed during cooling after soaking from the unstable austenite formed during annealing. Its content needs to be within the range of 50 to 95%. No less than 50% of the target tensile strength of 980 MPa or above 95% is achieved, the total elongation will be below 8%.
    [065] The good results of bore expansion in this invention are due to the phase fraction balance and the small difference in phase hardness (ferrite and martensite). ABBREVIATIONS
    [066] UTS (MPa) refers to the ultimate tensile strength measured by tensile testing in the transverse direction relative to the rolling direction.
    [067] YS (MPa) refers to the resistance to deformation measured by tensile test in the transverse direction relative to the rolling direction, TEl (%) refers to the total elongation.
    [068] UTS, YS and Tel can be measured after several tests. The tests used for the examples are done according to the JIS-T standard.
    [069] HE (%) refers to hole expansion. Such a test can be performed with the help of a conical punch made from a cylindrical piece whose diameter is 45 mm, topped by a conical piece. Such a punch is being positioned under the steel sheet for testing and which was previously provided with a hole with an initial diameter of 10 mm. The conical punch is then being moved up and into such a hole and effectively increases it until a first transverse crack appears. The final diameter D of the hole is then being measured and the hole expansion is calculated using the following relationship:

    [070] Microstructures were observed using a SEM in the fourth part thickness location, using 2% Nital stripper and quantified by image analysis.
    [071] The steels according to the invention will be better understood by reading the examples below which are given not for the purpose of limiting the scope, but as illustrations.
    [072] Semi-finished products were produced from steel molding. The chemical compositions of the semi-finished products, expressed as a percentage by weight, are shown in Table 1 below.
    TABLE 1: CHEMICAL COMPOSITION OF STEELS (PERCENTAGE BY WEIGHT) 19/27 Underlined values: out of the invention
    [073] The rest of the steel composition in Table 1 consists of iron and unavoidable impurities that result from smelting, the level of impurity being lower than 0.0005 but higher than 0.0001 mill.%.
    [074] Ingots of composition 1 to 14 were initially reheated and hot rolled. The hot-rolled steel plates were then cold-rolled and annealed. The tested process parameters are shown below: Reheat temperature (HR reheat), ° C Finishing laminate temperature (HRFT): ° C Winding temperature (CT): ° C Intermediate annealing temperature (IA T): ° C and time (IA t): hr Hot band delaying cooling, entering temperature (° C) on the cover, and cooling rate (° C / min) Cold rolling applied (CR): Oxidation temperature in the fire furnace. direction (DFF temperature): ° C percentage by volume of excess oxygen in DFF, the heating rate before reaching the annealing temperature (° C / s) The dew point in the annealing furnace (° C) Soak temperature during annealing (AT): ° C Soak time during annealing (At): s Over-aging temperature range OAT Over-aging time OAt
    [075] Type of coating: GI for galvanized at 465 ° C and GA for annealing after galvanizing with varying temperature.
    [076] Steels 1 to 14 experimented with the process parameters described in Table 2.
    TABLE 2 PARAMETERS OF REHEATING PROCESS TO COLD LAMINATION
    [077] The effects of intermediate annealing and cover treatment TIA were evaluated on the final product, that is, after cold rolling, annealing and final coating. Comparing to the example DD that did not undergo intermediate annealing, the example EE was intermediate annealed; its microstructure was homogenized during this process. After cold rolling and the final coating process, the thickness variation along the winding length was below 5%, while the thickness variation along the winding length in the DD example was significantly higher.
    [078] The GG example was treated inside a cover device that made the hot-rolled steel cool much more slowly, which also improved the microstructure homogeneity within the steel. As a consequence, its variation in the thickness of the final product was also below 5%.
    [079] In Table 3 below, all steels experienced an oxidation during heating using a furnace with direct fire followed by a reduction in a radiant tube furnace according to the present invention. As a consequence, the steel sheets are suitable to receive a GI or GA coating, since their surfaces do not include an iron oxide layer, but an internal oxidized zone, with a depth between 200 nm and 100 μm, comprising one or more of the oxides containing Si, Mn, Al, Ti, which corresponds to the bonding of the coating to the substrate. Cooling from GA temperature to room temperature after annealing after galvanizing was carried out at 5 ° C / s.


    TABLE 3: ANIMAL PARAMETERS TO PRODUCE VERY HIGH RESISTANCE STEEL COATED BY HOT IMMERSION nm: not measured. Underline: outside the scope of the invention
    [080] With respect to the microstructure, the average values for Table 3 with selected examples have the following microstructural resources:

    TABLE 4: MICRO-STRUCTURAL RESOURCES Underlined values: out of the invention
    [081] As for the mechanical properties, Table 4 above shows the results for deformation resistance, tensile strength, total elongation and bore expansion. BOG represents broken meter, the value has not been obtained.

    TABLE 5: MECHANICAL PROPERTIES nm: not measured. Underline: out of invention
    [082] The steels according to the invention have a good ability to be coated. In addition, many examples show tensile strength above 980 MPa and even above 1,180 MPa (see example W). In addition, ductility levels are also above 8% in all cases that correspond to the invention, the resistance to deformation is above 500 MPa and even above 780 MPa in some examples (see example W) and bore expansion values they are clearly above 20% and in the best cases above 40% (see example W).
    [083] Example XA was processed with a dew point at 28 ° C which was higher than 25 ° C. The tensile strength of the steel was below 980MPa due to excessive decarbonization caused by a very high dew point in the furnace.
    [084] The steel of example XB has 1.8% Mn, which is lower than 2%. The coated sheet obtained at the end of the process contains 65% ferrite plus bainite, which consequently results in a tensile strength much lower than 980 MPa.
    [085] The steel in example XC has more than 0.15% C, more than 1.5% Si and more than 0.1% Al, which made martensite very hard on steel. Consequently, the total elongation was much lower than 8% and the bore expansion ratio was much lower than 20%.
    [086] The steel according to the invention can be used for automotive body in white parts for motor vehicles.
    权利要求:
    Claims (23)
    [0001]
    1. COLD LAMINATED STEEL SHEET AND HOT IMMERSION COVERED, characterized by having a tensile strength of at least 980 MPa, with resistance to deformation above or equal to 500 MPa, with a total elongation above or equal to 8%, the composition of the steel sheet consisting, in percentage by weight, of: 0.05 <C <0.15%; 2 <Mn <3%; Al <0.1%; 0.3 <Si <1.5%; 0.01% <Nb <0.05%; N <0.02%; 0.1 <Cr + Mo <1%; 0.0001 <B <0.0025%; Ti <0.5%; V <0.01%; S <0.01%; P <0.05%; the rest of the composition being iron and unavoidable impurities that result from melting, having a microstructure consisting, in surface fraction, of: between 50 and 95% of martensite and between 5 and 50% of the sum of ferrite and bainite, in which the size ferrite grain is below 10 μm, where the ferrite grain size has an aspect ratio between 1 and 3 and where an internally oxidized depth of at least 200 nm and less than 100 μm, comprising one or more among oxides containing Si, Mn, Al, Ti, it is present under the coating by hot immersion.
    [0002]
    2. COLD LAMINATED STEEL SHEET AND HOT IMMERSION COVER, according to claim 1, characterized by 0.09 <C <0.14%.
    [0003]
    3. COLD LAMINATED STEEL SHEET AND HOT IMMERSION COVER, according to any one of claims 1 to 2, characterized by 2.2 <Mn <2.7%.
    [0004]
    4. COLD LAMINATED STEEL SHEET AND HOT IMMERSION COVER, according to any one of claims 1 to 3, characterized by Al <0.05%.
    [0005]
    5. COLD LAMINATED STEEL SHEET AND HOT IMMERSION COVER, according to any one of claims 1 to 4, characterized by 0.6 <Si <1.3%.
    [0006]
    6. COLD LAMINATED STEEL SHEET AND HOT IMMERSION COVER, according to any one of claims 1 to 5, characterized by Nb <0.03%.
    [0007]
    7. COLD LAMINATED STEEL SHEET AND HOT IMMERSION COVER, according to any one of claims 1 to 6, characterized by 0.1 <Cr + Mo <0.7%.
    [0008]
    8. COLD-LAMINATED STEEL SHEET AND HOT IMMERSION COVER, according to any one of claims 1 to 7, characterized by 0.001 <B <0.0022%.
    [0009]
    9. COLD LAMINATED STEEL SHEET AND HOT IMMERSION COVER, according to any one of claims 1 to 8, characterized by 0.02% <Ti <0.05%.
    [0010]
    10. COLD LAMINATED STEEL SHEET AND HOT IMMERSION COVER, according to any one of claims 1 to 9, characterized in that the surface fraction of the sum of ferrite and bainite is between 20 and 40%, with the average grain size of ferrite being below 3 μm.
    [0011]
    11. COLD LAMINATED STEEL SHEET AND HOT IMMERSION COVER, according to any one of claims 1 to 10, characterized in that the tensile strength is at least 980 MPa, the resistance to deformation is at least 500 MPa, the total elongation is at least 8% and the cold-rolled and hot-dip coated steel sheet has a hole expansion of at least 20%.
    [0012]
    12. COLD LAMINATED STEEL SHEET AND HOT IMMERSION COVER, according to claim 11, characterized in that the tensile strength is at least 1180 MPa, the resistance to deformation is at least 780 MPa, the total elongation is at least 8% and the hole expansion is at least 20%.
    [0013]
    13. COLD LAMINATED STEEL SHEET AND HOT DIP COATING, according to any one of claims 1 to 12, characterized in that the steel is galvanized or annealed after galvanizing.
    [0014]
    14. METHOD TO PRODUCE A COLD LAMINATED STEEL SHEET AND HOT IMMERSION COVER, as defined in any one of claims 1 to 13, characterized by comprising the following successive steps: - molding a steel whose composition is as defined in any one from claims 1 to 9 in order to obtain a rebar, - reheat the rebar to a Treheat temperature above 1180 ° C, - hot-laminate the rebar reheated to a temperature above 800 ° C to obtain a hot-rolled steel, - cool the hot rolled steel at a conventional cooling rate to a Tcoiling winding temperature between 500 ° C and 800 ° C, then - wind the Tcoiling-cooled hot rolled steel, - peel the hot rolled steel, - laminate the hot rolled steel in order to obtain a cold rolled steel sheet, with a cold rolling reduction ratio of between 40 and 60%, - annealing the cold rolled steel sheet, comprising the steps of: - Warm the cold rolled steel sheet at a direct fire oven temperature in a direct fire oven having an atmosphere with an excess oxygen volume percentage between 0.2% and 4%, in which an oxidation step takes place between 500 ° C and 750 ° C, a layer of iron oxide being formed on the surface of the cold-rolled steel sheet while internal oxidation occurs under that iron oxide; - increase the heating of the furnace with direct fire temperature to a Tanneal annealing temperature in a radiation tube oven, with a heating rate between 0.5 and 2.5 ° C / s, the radiation tube oven having an atmosphere with a dew point below or equal to 25 ° C, - the Tanneal annealing temperature being between 750 to 950 ° C, - keeping the steel at the Tanneal annealing temperature for a duration of at least 30 seconds and less than or equal to 300 seconds, - cool the cold rolled steel sheet to a TOA temperature between 440 ° C and 470 ° C, - hold the cold rolled steel sheet to TOA temperature for more than 30 seconds and less than 180 seconds, - and during heating, keeping in Tanneal and cooling steps, the surface of the cold rolled steel sheet is oxidized and subsequently reduced, in order to obtain an internally oxidized depth of at least 200 nm and less than 100 μm , comprising one or more oxides containing Si, Mn, Al, Ti, - hot-dip cold-rolled steel sheet to obtain cold-rolled steel sheet and hot-dip coated steel, - cool the cold-rolled steel sheet and dip-coated hot to room temperature at a cooling rate of at least 1 ° C / s.
    [0015]
    15. METHOD TO PRODUCE A COLD LAMINATED STEEL SHEET AND HOT DIP COATING, according to claim 14, characterized in that, after hot dip coating, the cold-rolled steel sheet and coated by hot immersion are annealed after galvanizing to achieve an iron content between 7% and 15% in the coating.
    [0016]
    16. METHOD FOR PRODUCING A COLD LAMINATED STEEL SHEET AND HOT DIP COATING, according to any one of claims 14 to 15, characterized by 500 ° C <Tcoiling <750 ° C.
    [0017]
    17. METHOD TO PRODUCE A COLD LAMINATED STEEL SHEET AND HOT IMMERSION COVER, according to any one of claims 14 to 16, characterized in that, after peeling and before cold rolling, the hot rolled steel is annealed at a TIA temperature above 300 ° C for more than twenty minutes.
    [0018]
    18. METHOD FOR PRODUCING A COLD LAMINATED STEEL SHEET AND HOT DIP COATING, according to claim 17, characterized in that the hot rolled steel is annealed at TIA temperature so that 500 ° C <TIA <650 ° C per a time between 30 hours and 100 hours.
    [0019]
    19. METHOD TO PRODUCE A COLD LAMINATED STEEL SHEET AND HOT IMMERSION COVER, according to any one of claims 17 to 18, characterized in that, after annealing at TlA temperature and before cold rolling, the steel has a temperature before entering the roof above 400 ° C, hot rolled steel being cooled under the roof with a cooling rate less than or equal to 1 ° C / min and higher than or equal to 0.01 ° C / min.
    [0020]
    20. METHOD TO PRODUCE A COLD LAMINATED STEEL SHEET AND HOT IMMERSION COVER, according to any one of claims 14 to 19, characterized in that the radiant tube oven has a mixed gas atmosphere having a dew point below 0 ° C, the surface of the cold rolled steel sheet being reduced within the radiant tube furnace.
    [0021]
    21. METHOD FOR PRODUCING A COLD LAMINATED STEEL SHEET AND HOT DIP COATING, according to any one of claims 14 to 20, characterized by 775 ° C <Tanneal <860 ° C.
    [0022]
    22. METHOD TO PRODUCE A COLD LAMINATED STEEL SHEET AND HOT IMMERSION COVER, according to any one of claims 14 to 21, characterized by the hot dip coating being done in a liquid Zn bath in order to obtain a cold rolled steel sheet and hot dip galvanized or annealed after galvanizing.
    [0023]
    23. USE OF A COLD LAMINATED STEEL SHEET AND HOT DIP COVERED, as defined in any one of claims 1 to 13, characterized in that it is to produce a part for a motor vehicle.
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    同族专利:
    公开号 | 公开日
    CN106471147A|2017-03-01|
    EP3152336A1|2017-04-12|
    KR20170015303A|2017-02-08|
    WO2015185956A1|2015-12-10|
    US10612107B2|2020-04-07|
    ES2729870T3|2019-11-06|
    MA39954A|2017-04-12|
    US11047020B2|2021-06-29|
    PL3152336T3|2019-08-30|
    RU2016147787A3|2018-10-26|
    WO2015185975A1|2015-12-10|
    JP2017520681A|2017-07-27|
    CN106471147B|2018-07-10|
    TR201907448T4|2019-06-21|
    UA117865C2|2018-10-10|
    JP6599902B2|2019-10-30|
    RU2675025C2|2018-12-14|
    RU2016147787A|2018-06-06|
    US20170137906A1|2017-05-18|
    CA2951215A1|2015-12-10|
    US20190256942A1|2019-08-22|
    MX2016016129A|2017-03-28|
    MA39954B1|2019-05-31|
    HUE044866T2|2019-11-28|
    EP3152336B1|2019-02-20|
    引用文献:
    公开号 | 申请日 | 公开日 | 申请人 | 专利标题
    JP3646538B2|1998-10-02|2005-05-11|Ｊｆｅスチール株式会社|Manufacturing method of hot-dip galvanized high-tensile steel sheet with excellent workability|
    JP3882679B2|2002-05-23|2007-02-21|Ｊｆｅスチール株式会社|Manufacturing method of high-strength hot-dip galvanized cold-rolled steel sheet with excellent deep-drawability with good plating appearance|
    US6811624B2|2002-11-26|2004-11-02|United States Steel Corporation|Method for production of dual phase sheet steel|
    DE60333400D1|2003-05-27|2010-08-26|Nippon Steel Corp|METHOD OF MANUFACTURING HIGHLY RESISTANT THIN STEEL PLATE WITH EXCELLENT RESISTANCE TO DELAYED BREAK AFTER FORMING|
    US7883769B2|2003-06-18|2011-02-08|3M Innovative Properties Company|Integrally foamed microstructured article|
    JP4486336B2|2003-09-30|2010-06-23|新日本製鐵株式会社|High yield ratio high strength cold-rolled steel sheet and high yield ratio high strength hot-dip galvanized steel sheet excellent in weldability and ductility, high yield ratio high-strength galvannealed steel sheet, and manufacturing method thereof|
    KR101094594B1|2003-09-30|2011-12-15|신닛뽄세이테쯔 카부시키카이샤|High-yield-ratio high-strength cold rolled steel sheet excelling in weldability and ductility|
    JP5162836B2|2006-03-01|2013-03-13|新日鐵住金株式会社|High-strength cold-rolled steel sheet excellent in hydrogen embrittlement resistance of welds and method for producing the same|
    US9067260B2|2006-09-06|2015-06-30|Arcelormittal France|Steel plate for producing light structures and method for producing said plate|
    EP1897963A1|2006-09-06|2008-03-12|ARCELOR France|Steel sheet for the manufacture of light structures and manufacturing process of this sheet|
    JP5194878B2|2007-04-13|2013-05-08|Ｊｆｅスチール株式会社|High-strength hot-dip galvanized steel sheet excellent in workability and weldability and method for producing the same|
    EP2009127A1|2007-06-29|2008-12-31|ArcelorMittal France|Process for manufacturing a galvanized or a galvannealed steel sheet by DFF regulation|
    ES2387040T3|2007-08-15|2012-09-12|Thyssenkrupp Steel Europe Ag|Double phase steel, flat product of a double phase steel of this type and process for manufacturing a flat product|
    EP2256224B1|2008-03-27|2016-05-04|Nippon Steel & Sumitomo Metal Corporation|High-strength cold-rolled steel sheet, high-strengthgalvanized steel sheet, and high-strength alloyed hot-dip galvanized steel sheet having excellent formability andweldability, and methods for manufacturing the same|
    JP5251208B2|2008-03-28|2013-07-31|Ｊｆｅスチール株式会社|High-strength steel sheet and its manufacturing method|
    JP5504643B2|2008-08-19|2014-05-28|Ｊｆｅスチール株式会社|High-strength hot-dip galvanized steel sheet excellent in workability and manufacturing method thereof|
    JP5394709B2|2008-11-28|2014-01-22|株式会社神戸製鋼所|Super high strength steel plate with excellent hydrogen embrittlement resistance and workability|
    JP5564784B2|2008-12-05|2014-08-06|Ｊｆｅスチール株式会社|Manufacturing method of high-strength hot-dip galvanized steel sheet and high-strength galvannealed steel sheet|
    JP4924730B2|2009-04-28|2012-04-25|Ｊｆｅスチール株式会社|High-strength hot-dip galvanized steel sheet excellent in workability, weldability and fatigue characteristics and method for producing the same|
    EP2436797B1|2009-05-27|2017-01-04|Nippon Steel & Sumitomo Metal Corporation|High-strength steel sheet, hot-dipped steel sheet, and alloy hot-dipped steel sheet that have excellent fatigue, elongation, and collision characteristics, and manufacturing method for said steel sheets|
    PL2290133T3|2009-08-25|2012-09-28|Thyssenkrupp Steel Europe Ag|Method for producing a steel component with an anti-corrosive metal coating and steel component|
    JP5771034B2|2010-03-29|2015-08-26|株式会社神戸製鋼所|Ultra-high strength steel plate with excellent workability and manufacturing method thereof|
    GB2493302A|2010-03-29|2013-01-30|Kobe Steel Ltd|Ultra high strength steel plate having excellent workability, and protection method for same|
    JP5434960B2|2010-05-31|2014-03-05|Ｊｆｅスチール株式会社|High-strength hot-dip galvanized steel sheet excellent in bendability and weldability and method for producing the same|
    KR20120075260A|2010-12-28|2012-07-06|주식회사 포스코|Hot dip plated steel sheet excellent in plating adhesiveness and method for manufacturing the hot dip plated steel sheet|
    KR101453240B1|2011-05-10|2014-10-22|아르셀러미탈 인베스티가시온 와이 데살롤로 에스엘|Steel sheet with high mechanical strength, ductility and formability properties, production method and use of such sheets|
    DE102011051731B4|2011-07-11|2013-01-24|Thyssenkrupp Steel Europe Ag|Process for the preparation of a flat steel product provided by hot dip coating with a metallic protective layer|
    CN103827335B|2011-09-30|2015-10-21|新日铁住金株式会社|Steel plate galvanized and manufacture method thereof|
    MX2014003716A|2011-09-30|2014-06-23|Nippon Steel & Sumitomo Metal Corp|Hot-dip galvanized steel sheet and process for producing same.|
    EP2684975B1|2012-07-10|2016-11-09|ThyssenKrupp Steel Europe AG|Cold rolled steel flat product and method for its production|JP6131919B2|2014-07-07|2017-05-24|Ｊｆｅスチール株式会社|Method for producing galvannealed steel sheet|
    ES2674133T3|2014-12-01|2018-06-27|Voestalpine Stahl Gmbh|Procedure for heat treatment of a manganese-steel product|
    JP6020605B2|2015-01-08|2016-11-02|Ｊｆｅスチール株式会社|Method for producing galvannealed steel sheet|
    WO2016198906A1|2015-06-10|2016-12-15|Arcelormittal|High-strength steel and method for producing same|
    EP3415653B1|2016-02-10|2020-03-04|JFE Steel Corporation|High-strength galvanized steel sheet and method for producing same|
    EP3421633B1|2016-03-31|2020-05-13|JFE Steel Corporation|Thin steel sheet, plated steel sheet, method for producing hot-rolled steel sheet, method for producing cold-rolled full-hard steel sheet, method for producing thin steel sheet, and method for producing plated steel sheet|
    CN109072375B|2016-03-31|2020-11-03|杰富意钢铁株式会社|Thin steel sheet and plated steel sheet, and method for producing hot-rolled steel sheet, method for producing cold-rolled all-hard steel sheet, method for producing thin steel sheet, and method for producing plated steel sheet|
    CN105908089B|2016-06-28|2019-11-22|宝山钢铁股份有限公司|A kind of hot-dip low density steel and its manufacturing method|
    US11136643B2|2016-08-10|2021-10-05|Jfe Steel Corporation|High-strength steel sheet and method for producing same|
    US11091817B2|2016-08-30|2021-08-17|Jfe Steel Corporation|High-strength steel sheet and method for manufacturing the same|
    WO2018062342A1|2016-09-30|2018-04-05|Ｊｆｅスチール株式会社|High-strength plated steel sheet and production method therefor|
    KR101889181B1|2016-12-19|2018-08-16|주식회사 포스코|High-strength steel having excellent bendability and stretch-flangeability and method for manufacturing same|
    CN107164624B|2017-04-10|2020-02-21|首钢集团有限公司|Method for controlling pockmark defects on surface of phosphorus-containing cold-rolled high-strength steel|
    CN107254572B|2017-06-01|2019-07-02|首钢集团有限公司|A kind of cold-reduced silicon manganese dual-phase steel surface point defects controlling method|
    CN109207841B|2017-06-30|2021-06-15|宝山钢铁股份有限公司|Low-cost high-formability 1180 MPa-grade cold-rolled annealed dual-phase steel plate and manufacturing method thereof|
    DE102017123236A1|2017-10-06|2019-04-11|Salzgitter Flachstahl Gmbh|Highest strength multi-phase steel and process for producing a steel strip from this multi-phase steel|
    EP3653745A4|2017-10-20|2020-07-15|JFE Steel Corporation|High-strength steel sheet and manufacturing method thereof|
    JP6443594B1|2017-10-20|2018-12-26|Ｊｆｅスチール株式会社|High strength steel plate and manufacturing method thereof|
    CN107761007A|2017-10-23|2018-03-06|攀钢集团攀枝花钢铁研究院有限公司|Strong dual phase steel of low-carbon cold rolling superelevation and preparation method thereof|
    WO2020136989A1|2018-12-26|2020-07-02|Ｊｆｅスチール株式会社|High-strength hot-dip zinc-coated steel sheet and method for manufacturing same|
    BE1026986B1|2019-01-23|2020-08-25|Drever Int S A|Method and furnace for the heat treatment of a strip of high strength steel comprising a temperature homogenization chamber|
    CN113366126A|2019-01-29|2021-09-07|杰富意钢铁株式会社|High-strength steel sheet and method for producing same|
    CN111411295B|2020-03-24|2021-06-15|首钢集团有限公司|Multiphase steel member and preparation method and application thereof|
    CN113737108A|2020-05-27|2021-12-03|宝山钢铁股份有限公司|Delay cracking resistant electro-galvanized super-strong dual-phase steel and manufacturing method thereof|
    WO2022042730A1|2020-08-31|2022-03-03|宝山钢铁股份有限公司|High-strength low-carbon martensitic high hole expansion steel and manufacturing method therefor|
    法律状态:
    2019-08-20| B06U| Preliminary requirement: requests with searches performed by other patent offices: procedure suspended [chapter 6.21 patent gazette]|
    2021-03-02| B09A| Decision: intention to grant [chapter 9.1 patent gazette]|
    2021-04-27| B16A| Patent or certificate of addition of invention granted|Free format text: PRAZO DE VALIDADE: 20 (VINTE) ANOS CONTADOS A PARTIR DE 03/06/2015, OBSERVADAS AS CONDICOES LEGAIS. |
    优先权:
    申请号 | 申请日 | 专利标题
    PCT/IB2014/000991|WO2015185956A1|2014-06-06|2014-06-06|High strength multiphase galvanized steel sheet, production method and use|
    IBPCT/IB2014/000991|2014-06-06|
    PCT/IB2015/000819|WO2015185975A1|2014-06-06|2015-06-03|High strength multiphase steel, production method and use|
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