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    • 专利摘要:
    rolled steel sheet, part, sheet steel and one-piece fabrication methods, and one-piece use. the invention relates to a laminated steel sheet, for hardening by pressing, for which the chemical composition comprises, with contents expressed by weight: 0.24% = c = 0.38%, 0.40% = mn = 3%, 0.10% = si = 0.70%, 0.015% = al = 0.070%, 0% = cr = 2%, 0.25% = ni = 2%, 0.015% = ti = 0.10% , 0% = nb = 0.060%, 0.0005% = b = 0.0040%, 0.003% = n = 0.010%, 0.0001% = s = 0.005%, 0.0001% = p = 0.025%, being understood that the contents of nitrogen and titanium satisfy: ti/n >3.42, and that the contents of carbon, manganese, chromium and silicon satisfy: 2.6c + mn/5.3 + cr/13 + si/15 = 1.1%, where the chemical composition optionally comprises one or more of the following elements: 0.05% = mo = 0.65%, 0.001% = w = 0.30%, 0.0005% = ca = 0.005 %, where the remainder is composed of iron and unavoidable impurities arising from the preparation, where the plate contains a nickel content ni surf at any point in the steel near the surface of said plate at a depth ?, so that ni surf > ni nom, where ni no m indicates the nominal nickel content of the steel, and so that ni max indicates the maximum nickel content within ?: (ni max + ni nom)/ 2 x (?) = 0.6 and so that: (ni max - ni nom)/ ? = 0.01, with the depth ? expressed in microns and the contents of ni max and ni nom expressed in percentages by weight.
    公开号:BR112017007999B1
    申请号:R112017007999-2
    申请日:2015-07-29
    公开日:2021-06-01
    发明作者:Sebastian Cobo；Juan David Puerta Velasquez；Martin Beauvais；Catherine Vinci
    申请人:Arcelormittal；
    IPC主号:
    专利说明:

    FIELD OF THE INVENTION
    [001] The invention relates to a manufacturing method for steel sheets intended to produce mechanical parts of very high strength after hardening by pressing. BACKGROUND OF THE INVENTION
    [002] As is known, quench hardening in pressing (or press hardening) consists of heating raw steel blocks to a temperature high enough to obtain an austenitic transformation and then hot stamping the raw blocks while maintaining them. the same inside the pressing tool in order to obtain sharply cooled microstructures. According to a variant of the method, a cold pre-stamping can be done on the raw blocks in advance before heating and hardening by pressing. These raw blocks can be pre-coated, for example, with a zinc or aluminum alloy. In that case, during heating in an oven, precoat the alloy with the steel substrate by diffusion so as to create a composite that provides surface protection of the part against decarburization and scale formation. This compound is suitable for hot forming.
    [003] The resulting parts are, in particular, used as structural elements in automotive vehicles to provide energy-absorbing or anti-intrusion functions. Thus, as examples of implantation, the following can be cited: bumper beams, reinforcements of the central pillar or door or frame rails. Such press-hardened parts can also be used, for example, to make tools or parts for agricultural machinery.
    [004] Depending on the composition of the steel and the cooling speed obtained in pressing, the mechanical strength can reach a lower or higher level. Thus, EP publication 2,137,327 discloses a steel composition containing: 0.040%<C<0.100%, 0.80%<Mn<2.00%,Si<0.30%, S<0.005%, P <0.030%, 0.010% < AI < 0.070%, 0.015%<Nb<0.100%, 0.030% < Ti < 0.080%, N<0.009%, Cu, Ni, Mo<0.100%, Ca<0.006%, with which a tensile strength Rm above 500 MPa can be obtained after press hardening.
    [005] The FR publication 2780.984 reveals a higher strength level that is obtained: a steel sheet containing 0.15%<C<0.5%, 0.5% <Mn<3%, 0.1 %< Si<0.5%, 0.01%<Cr<1%, Ti<0.2%, Al and P<0.1%, S<0.05%, 0.0005%<B<0 .08% allows a resistance Rm above 1,000 above 1,500 MPa to be achieved.
    [006] Such resistances are satisfactory for many applications. However, demands to reduce vehicle energy consumption drive the search for even lighter weight vehicles through the use of parts whose mechanical strength would be even higher, meaning that the Rm resistance would be above 1800 MPa. Since some parts are painted and subjected to a paint baking cycle, this value must be reached with or without heat treatment by baking.
    [007] Now, such a level of resistance is usually associated with a complete or very predominantly martensitic microstructure. It is known that this type of microstructure has a lower resistance to delayed cracking: after hardening by pressing, the manufactured parts can, in fact, be susceptible to cracking or rupture after a certain time, through a set of three factors:- a microstructure predominantly martensitic; - a sufficient amount of diffusible hydrogen. This can be introduced during furnace heating of the raw blocks before the hot stamping and press hardening step: in fact, the water vapor present in the furnace can decompose and be absorbed on the surface of the raw block; - the presence sufficient level of residual or applied stress.
    [008] In order to solve the delayed cracking problem, the strict control of the atmosphere of the reheating furnaces and the cutting conditions of the raw blocks was proposed in order to minimize the level of stresses. The performance of thermal post-treatments on hot stamped parts was also proposed in order to allow the degassing of hydrogen. These operations are, however, limiting for the industry that wants a material that allows avoiding this risk and overcoming these additional costs and restrictions.
    [009] The deposit of specific coatings on the surface of the steel sheet that reduces the absorption of hydrogen has also been proposed. However, a simpler process that offers resistance to equivalent delayed cracking is being sought.
    [010] Therefore, a method of manufacturing parts that simultaneously offers a very high mechanical strength Rm and a high resistance to delayed cracking after hardening by pressing is sought; where these goals are previously difficult to reconcile.
    [011] In addition, it is known that steel compositions richer in elements that promote sudden cooling and/or hardening (C, Mn, Cr, Mo, etc.) lead to obtaining hot-rolled sheets with greater hardness . Thus, this increased hardness is detrimental to obtaining cold-rolled sheets in a wide range of thicknesses, considering the limited rolling capacity of some cold-rolling mills. A very high level of strength in the hot-rolled sheet stage therefore does not allow very thin cold-rolled sheets to be obtained. A method that provides a wide range of cold rolled sheet thicknesses is therefore pursued.
    [012] Additionally, the presence of elements promoting sudden cooling and/or hardening in larger quantities can have consequences during the thermomechanical treatment for manufacturing due to the fact that a variation of some parameters (end of rolling temperature, coiling temperature, cooling speed variation through the length of the laminated tape) can lead to a variation of the mechanical properties within the sheet. A steel composition less sensitive to a variation of certain manufacturing parameters is therefore sought in order to manufacture a sheet that has good mechanical property homogeneity.
    [013] It is also sought a steel composition that can be easily coated, in particular, through hot immersion, so that the sheet can be available in different forms: uncoated, or coated with aluminum alloy or aluminum alloy. zinc, depending on end-user specifications.
    [014] A process is also sought that provides a plate that has good suitability for the mechanical cutting step in order to obtain raw blocks intended for hardening by pressing, that is, whose mechanical strength would not be very high at that stage in order to prevent breakage of drilling or cutting tools. DESCRIPTION OF THE INVENTION
    [015] The purpose of the present invention is to solve all the problems discussed above through an economical manufacturing method.
    [016] Surprisingly, the inventors showed that these problems were solved by providing a plate with the composition detailed below, where this plate furthermore had the feature of having a specific enrichment with nickel in its surface area.
    [017] For this purpose, the present invention is a laminated steel sheet, for hardening by pressing, for which the chemical composition comprises, with contents expressed by weight: 0.24% < C < 0.38%, 0, 40% < Mn < 3%, 0.10% < Si < 0.70%, 0.015% < Al < 0.070%, 0% < Cr < 2%, 0.25% < Ni < 2%, 0.015% < Ti < 0.10%, 0% < Nb < 0.060%, 0.0005% < B < 0.0040%, 0.003% < N < 0.010%, 0.0001% < S < 0.005%, 0.0001% < P < 0.025%, it being understood that the nitrogen and titanium contents satisfy: Ti/N >3.42, and that the carbon, manganese, chromium and silicon contents satisfy:
    wherein the chemical composition optionally comprises one or more of the following elements: 0.05% < Mo < 0.65%, 0.001% < W < 0.30%, 0.0005% < Ca < 0.005%, where the remainder it is composed of iron and unavoidable impurities arising from the preparation, where the plate contains a Nisurf nickel content at any point in the steel near the surface of said plate at a depth Δ, so that Nisurf > Ninom, where Ninom indicates the nominal nickel content of the steel, and so that Nimax indicates the
    Δ > 0.01, with depth Δ expressed in microns and Nimax and Ninom contents expressed in percentages by weight.
    [018] According to a first mode, the composition of the sheet comprises, by weight: 0.32% < C < 0.36%, 0.40% < Mn < 0.80%, 0.05% < Cr < 1.20%.
    [019] According to a second mode, the composition of the sheet comprises, by weight: 0.24% < C < 0.28%, 1.50% < Mn < 3%.
    [020] The silicon content of the sheet is preferably such that: 0.50% < Si < 0.60%.
    [021] According to in specific mode, the composition comprises, by weight: 0.30% < Cr < 0.50%.
    [022] Preferably, the composition of the sheet comprises, by weight: 0.30% < Ni < 1.20%, and most preferably: 0.30% < Ni < 0.50%.
    [023] The titanium content is preferably such that: 0.020% < Ti.
    [024] The composition of the sheet advantageously comprises: 0.020% < Ti < 0.040%.
    [025] According to a preferred mode, the composition comprises, by weight: 0.15% < Mo < 0.25%.
    [026] The composition preferably comprises by weight: 0.010% < Nb < 0.060%, and most preferably: 0.030% < Nb < 0.050%.
    [027] According to specifically, the composition comprises, by weight: 0.50% < Mn < 0.70%.
    [028] Advantageously, the microstructure of the steel sheet is ferritic-pearlitic.
    [029] According to a preferred mode, the steel sheet is a hot rolled sheet.
    [030] Preferably, the sheet is a hot rolled and annealed sheet.
    [031] According to a specific mode, the steel sheet is precoated with a layer of aluminum or aluminum alloy metal or aluminum-based alloy.
    [032] According to a specific mode, the steel sheet is precoated with a layer of zinc metal or zinc alloy or zinc based alloy.
    [033] According to another mode, the steel sheet is precoated with a coating or several coatings of intermetallic alloys that contain aluminum and iron and possibly silicon, in which the precoat does not contain free aluminum, from the T phase 5 of the Fe3Sí2Al2 type, and T 6 of the Fe2Sí2Al9 type.
    [034] The present invention is also a part obtained by the press hardening of a composite steel sheet according to any of the above modes with martensitic or martensitic-bainitic structure.
    [035] Preferably, the press-hardened part contains a nominal Ninom nickel content, where the Nisurf nickel content in the steel near the surface is greater than Ninom at a depth Δ, and where, Nimax designating the content maximum nickel in
    [036]
    0.01, where the depth Δ is expressed in microns and the Nimax and Ninom contents are expressed as a percentage by weight.
    [037] Advantageously, the piece hardened by pressing has a mechanical strength Rm greater than or equal to 1800 MPa.
    [038] According to a preferred way, the press-hardened part is coated with an aluminum or aluminum-based alloy, or a zinc or zinc-based alloy, which results from diffusion between the steel substrate and the pre- coating during press hardening heat treatment.
    [039] Another object of the invention is a manufacturing method for a hot rolled steel sheet comprising successive steps according to which an intermediate product with chemical composition according to any of the ways presented above is melted, and , then reheated to a temperature between 1,250 °C and 1,300 °C for a retention time at that temperature between 20 and 45 minutes. The intermediate product is hot rolled above one end of the rolling temperature, ERT, between 825°C and 950 °C to obtain a hot rolled sheet, and then the hot rolled sheet is spirally wound into a temperature between 500 °C and 750 °C in order to obtain a rolled sheet and hot spirally wound, and then the oxide layer formed during the previous steps is removed by pickling.
    [040] The purpose of the invention is also a manufacturing method for annealed and cold-rolled sheet, distinguished by comprising the successive steps according to which a hot-rolled sheet is supplied, spirally wound and pickled, manufactured by the method described above and then this hot rolled, spiral wound, pickled sheet is cold rolled to get a cold rolled sheet. This cold rolled sheet is annealed at a temperature between 740 °C and 820 °C to obtain an annealed and cold rolled sheet.
    [041] According to an advantageous mode, a sheet fabricated laminated according to any of the above methods is provided and then a continuous precoat is performed by hot dipping, wherein the precoat is aluminum or a aluminum or aluminum based alloy, or zinc or a zinc or zinc based alloy.
    [042] Advantageously, an object of the invention is also a manufacturing method for a pre-coated and prefabricated sheet with alloys according to which a sheet laminated according to any of the above methods is provided and then a Continuous hot-dip precoat is carried out with an aluminum or aluminum-based alloy and then a heat pretreatment of the precoated sheet is done at a temperature θ1 between 620 and 680 °C for a retention time t1 between 6 and 15 hours, so that the precoat no longer contains free aluminum of the T5 phase of the Fe3Sí2Al2 type, and T 6 of the Fe2Sí2Al9 type, and so that an austenitic transformation is not caused in the steel substrate, where the pretreatment is done in an oven under an atmosphere of hydrogen and nitrogen.
    [043] An object of the invention is also a manufacturing method for a press-hardened part comprising successive steps according to which a sheet manufactured by a method according to any of the above modes is supplied and then a said sheet is cut to obtain a blank block and then an optional cold stamping step is performed on the blank block. The raw block is heated to a temperature between 810 °C and 950 °C in order to generate a completely austenitic structure in the steel and then the raw block is transferred into a press. The raw block is hot stamped in order to obtain a part and then it is kept inside the press in order to obtain a hardening by the martensitic transformation of the austenitic structure.
    [044] An object of the invention is also the use of a press-hardened part comprising the characteristics presented above or manufactured according to the method presented above for the manufacture of reinforcement parts or structural parts for vehicles. BRIEF DESCRIPTION OF THE DRAWINGS
    [045] Other features and advantages of the invention will appear during the description below given as an example and with reference made to the attached figures below.
    [046] Figure 1 schematically shows the variation of nickel content near the surface of plates or pieces hardened by pressing and illustrates certain parameters that define the invention: Nimax, Nisurf, Ninom and Δ.
    [047] Figure 2 shows the mechanical strength of hot stamped and press-hardened parts as a function of a parameter that combines the contents of C, Mn, Cr and Si of the plates.
    [048] Figure 3 shows the diffusible hydrogen content measured in hot stamped and press hardened parts as a function of a parameter that expresses the total nickel content near the surface of the plates.
    [049] Figure 4 shows the diffusible hydrogen content measured in hot stamped and press hardened parts as a function of a parameter that expresses the amount of enrichment with nickel in the surface layer of the plates.
    [050] Figure 5 shows the variation in nickel content close to the surface of plates that have different compositions.
    [051] Figure 6 shows the variation in nickel content close to the surface of plates of identical composition that were subjected to two modes of surface preparation before pressing hardening.
    [052] Figure 7 shows the variation in diffusible hydrogen content as a function of the amount of nickel enrichment in the surface layer, for sheets that were subjected to two modes of surface preparation before pressing hardening.
    [053] Figures 8 and 9 show the structures of hot rolled sheets according to the invention. DESCRIPTION OF ACHIEVEMENTS OF THE INVENTION
    [054] The thickness of the sheet metal implanted in the method according to the invention is preferably comprised between 0.5 mm and 4 mm, in which a range of thickness is notably used in the manufacture of reinforcement parts or structural parts for the automotive industry. This can be achieved by hot rolling or being a matter of a subsequent cold rolling and annealing. This thickness range is suitable for industrial press hardening tools, in particular hot stamping presses.
    [055] Advantageously, steel contains the following elements, with the composition expressed by weight:- a carbon content comprising between 0.24% and 0.38%. This element plays a major role in the sudden cooling capacity and the mechanical strength obtained after cooling following the austenitization treatment. Below a content of 0.24% by weight, the mechanical strength level of 1800 MPa cannot be reached after hardening by pressing hardening, without additional addition of costly elements. Above a content of 0.38% by weight, the risk of delayed cracking is increased, and the ductile/brittle transition temperature, measured with Charpy type notched bending tests, becomes greater than -40°C, the which is seen as a very significant reduction in tenacity.
    [056] With a carbon content comprised between 0.32% and 0.36% by weight, the bleached properties can be obtained stably, while maintaining the weldability at a satisfactory level and limiting production costs.
    [057] The suitability for spot welding is particularly good when the carbon content is between 0.24% and 0.28%.
    [058] As will be seen later, the carbon content must also be defined in conjunction with the contents of manganese, chromium and silicon; - in addition to its role as a deoxidizer, manganese plays a role in the cooling capacity: the content of the same must be greater than 0.40% by weight to obtain a sufficiently low starting temperature of the transformation Ms (austenite → martensite) during the cooling in the pressing, which makes it possible to increase the strength Rm. Increased resistance to delayed cracking can be achieved by limiting the manganese content to 3%. In fact, manganese segregates to the austenitic grain boundaries and increases the risk of irregular breakage in the presence of hydrogen. On the other hand, as will be explained later, the resistance to delayed cracking arises, in particular, from the presence of a surface layer enriched with nickel. Without wishing to be bound by theory, it is believed that when the manganese content is excessive, a thick oxide layer is created during the reheating of the plates, since the nickel that does not have time to diffuse sufficiently is located under this layer of iron oxide and manganese.
    [059] The manganese content is preferably defined together with the carbon content and possibly chromium:- when the carbon content comprises between 0.32% and 0.36% by weight, with a manganese content comprises between 0.40% and 0.80% and where the chromium content comprises between 0.05% and 1.20%, an excellent resistance to delayed cracking due to the fact that the presence of a surface layer enriched with nickel is particularly effective and at the same time a very good suitability for mechanical cutting of sheets can be obtained. The manganese content ideally comprises between 0.50% and 0.70% to reconcile the achievement of high mechanical strength and resistance to delayed cracking; - when the carbon content comprises between 0.24% and 0.28%, combined with a content of manganese comprising between 1.50% and 3%, the suitability for spot welding is particularly good.
    [060] These ranges of composition make it possible to obtain a starting temperature of cooling transformation (austenite→martensite) Ms comprised between about 320 °C and 370 °C and in this way, it can be guaranteed that the heat-hardened parts have a sufficiently high strength; - the silicon content of the steel must comprise between 0.10% and 0.70% by weight: with a silicon content above 0.10%, an additional hardening can be obtained and the silicon contributes to the deoxidation of the liquid steel. The content of the same should, however, be limited to 0.70% in order to avoid excessive formation of surface oxides during the reheating and/or annealing steps and not to impair the hot-dip coating capability.
    [061] The silicon content is preferably above 0.50% in order to avoid a softening of the fresh martensite, which can occur when the part is retained in the pressing tool after the martensitic transformation. The silicon content is preferably below 0.60% so that the heating transformation temperature Ac3 (ferrite + perlite → austenite) is not too high. Otherwise, this requires reheating the raw blocks to a higher temperature before hot stamping, which reduces the productivity of the method; - in quantities greater than or equal to 0.015%, aluminum is an element that allows deoxidation in the liquid metal during elaboration, and the precipitation of nitrogen. When its content is above 0.070%, it can form coarse aluminates during steelmaking which tends to reduce ductility. Ideally, its content is comprised between 0.020% and 0.060%; chromium increases the sudden cooling capacity and contributes to obtaining the desired level of Rm after hardening by pressing. Above a content equal to 2% by weight, the effect of chromium on the homogeneity of mechanical properties in the press-hardened part is saturated. In an amount preferably comprised between 0.05% and 1.20%, this element contributes to the increase in strength. Preferably, the desired effects on mechanical strength and delayed cracking can be obtained by adding chromium in the range of 0.30% to 0.50% while limiting the additional cost. When the manganese content is sufficient, that is, comprised between 1.50% and 3% of manganese, the addition of chromium is considered ideal due to the fact that the sudden cooling capacity obtained through manganese is considered sufficient.
    [062] In addition to the conditions in each of the elements C, Mn, Cr and Si defined above, the inventors showed that these elements must be specified together: in fact, Figure 2 shows the mechanical strength of the press-hardened raw blocks for different steel compositions with variable contents of carbon (between 0.22% and 0.36%), manganese (between 0.4% and 2.6%), chromium (between 0% and 1.3%) and silicon (between 0. 1% and 0.72%) as a

    [063] The data shown in Figure 2 refer to the raw blocks heated in the austenitic domain at a temperature of 850 °C or 900 °C held at this temperature for 150 seconds and then hot stamped and cooled abruptly holding in the tool. In all cases, the structure of the parts that result after hot stamping is completely martensitic. Straight line 1 designates the lower envelope of mechanical strength results. Despite the dispersion due to the variety of compositions studied, it seems that a minimum value of 1,800 MPa is obtained when the P1 parameter is greater than 1.1%. When this condition is satisfied, the transformation temperature Ms during pressure cooling is below 365 °C. Under these conditions, the fraction of self-hardened martensite, under the effect of retention in the pressing tool, is extremely limited, so that the very high amount of unhardened martensite allows a high value of mechanical strength to be obtained.
    [064] Titanium has a high affinity for nitrogen. Considering the nitrogen content of the steels of the invention, the titanium content must be greater than or equal to 0.015% in order to obtain an effective precipitation. In amounts above 0.020% by weight, titanium protects the boron so that this element is found in a free form to play its full effect on the quenching capability. Its content must be greater than 3.42 N, where this amount is defined by the stoichiometry of TiN precipitation in order to avoid the presence of free nitrogen. Beyond 0.10%, there is, however, a risk of forming coarse titanium nitrates in the liquid steel which plays a detrimental role in toughness. The titanium content is preferably comprised between 0.020% and 0.040% in order to create fine nitrides which limit the growth of austenitic grains during reheating of the raw blocks prior to hot stamping.
    [065] In amounts above 0.010% by weight, niobium forms niobium carbonitrides which can also limit the growth of austenitic grains during reheating of the raw blocks. The content of the same should, however, be limited to 0.060% due to the fact that its ability to limit recrystallization during hot rolling which increases rolling forces and manufacturing difficulty. Optimal effects are obtained when the niobium content is between 0.030% and 0.050%.
    [066] In amounts above 0.0005% by weight, boron increases the quenching capacity very strongly. By diffusing the austenitic grain boundary joints, it exerts a favorable influence by preventing intergranular phosphorus segregation. Up to 0.0040%, this effect is saturated.
    [067] A nitrogen content above 0.003% makes it possible to obtain the precipitation of TiN, Nb(CN) or (Ti, Nb)(CN) mentioned above in order to limit the growth of the austenitic grain. The content should, however, be limited to 0.010% in order to avoid the formation of coarse precipitates.
    [068] Optionally, the sheet can contain molybdenum in an amount between 0.05% and 0.65% by weight: this element forms a coprecipitate with niobium and titanium. These precipitates are very thermally stable, reinforcing the limitation of austenitic grain growth on heating. An ideal effect is obtained for a molybdenum content between 0.15% and 0.25%.
    [069] As an option, the steel may also comprise tungsten in an amount comprised between 0.001% and 0.30% by weight. In the indicated quantities, this element increases the sudden cooling capacity and the hardenability due to the formation of carbides.
    [070] Optionally, steel can also contain calcium in an amount between 0.0005% and 0.005%: combining with oxygen and sulfur, calcium makes it possible to avoid the formation of large size inclusions that negatively affect the ductility of the sheets or parts made that way.
    [071] In excessive amounts, sulfur and phosphorus lead to increased brittleness. This is due to the fact that the sulfur content by weight is limited to 0.005% in order to avoid excessive sulphide formation. However, obtaining an extremely low sulfur content, ie, below 0.001%, is unnecessarily expensive, in the sense that it does not provide an additional benefit.
    [072] For similar reasons, the phosphorus content is comprised between 0.001% and 0.025% by weight. At an excessive content, this element segregates into the austenitic grain joints and increases the risk of delayed cracking due to irregular breakage.
    [073] Nickel is an important element of the invention: in fact, the inventors have shown that this element, in an amount comprised between 0.25% and 2% by weight, very substantially reduces the sensitivity to delayed fracture when it is located concentrated on the surface of the sheet or parts in a specific shape.
    [074] For this, reference is made to Figure 1 which schematically shows some characteristic parameters of the invention: the variation of the nickel content of a steel close to the surface of the plate, for which a surface enrichment was noted, is presented. For the sake of convenience, only one of the surfaces of the sheet has been shown, it is understood that the following description applies to other surfaces of that sheet as well. The steel has a nominal Ninom nickel content. Due to the fabrication method that will be described later, the steel sheet is enriched with nickel in its surface area, up to a maximum Nimax. This maximum Nimax can be found on the surface of the sheet, as shown in Figure 1, or slightly under that surface, a few tens or hundreds of nanometers below it, without changing the description below and the results of the invention. Similarly, the variation in nickel content cannot be linear, as shown schematically in Figure 1, but adopts a characteristic profile that results from the diffusion phenomenon. In this sense, the following definition of characteristic parameters is also valid for this type of profile. The nickel-enriched surface zone is therefore distinguished by the fact that at any point, the local Nisurf nickel content of the steel is such that: Nisurf > Ninom. This enriched zone has a depth of Δ.
    [075] Surprisingly, the inventors showed that a resistance to delayed cracking is obtained considering two parameters P2 and P3 characteristic of the enriched surface area, which must satisfy some critical conditions. First, one defines:

    [076] This first parameter describes the total nickel content in the enriched layer Δ and corresponds to the dashed area shown in Figure 1.
    [077] The second parameter P3 is defined by:

    [078] This second parameter describes the average nickel content gradient, that is, the amount of enrichment within the Δ layer.
    [079] The inventors are looking for conditions that prevent the delayed cracking of press-hardened parts with very high mechanical strength. This method is known to provide raw steel blocks, if exposed or pre-coated with a metal coating (aluminum or aluminum alloy, or zinc or zinc alloy) that are heated and then transferred in a press. hot stamping. During the heating step, water vapor possibly present in the furnace in a more or less significant amount is absorbed on the surface of the raw block. Hydrogen arising from the dissociation of water can be dissolved in the austenitic steel substrate at high temperatures. The introduction of hydrogen is therefore facilitated by an oven atmosphere with a high dew point, a significant austenitizing temperature and a long retention time. During cooling, the solubility of hydrogen drops abruptly. After returning to room temperature, the coating formed by making a metallic alloy between the possible metal precoat and the steel substrate forms a virtually sealed barrier to hydrogen desorption. A significant diffusible hydrogen content will therefore increase the risks of delayed cracking for a steel substrate with a martensitic structure. The inventors therefore looked for means by which to lower the diffusible hydrogen content on a hot stamped part to a very low level, ie less than or equal to 0.16 ppm. This level is to ensure that a part tensioned in flexion under a stress equal to that of the material yield stress for 150 hours does not exhibit cracking.
    [080] They showed that this result is achieved when the surface of the hot stamped part or that of the sheet or blank before hot stamping has the following specific properties: - Figure 3, established for parts hardened by pressing with Rm resistance that comprises between 1800 MPa and 2140 MPa shows that the diffusible hydrogen content depends on the P2 parameter above. A diffusible hydrogen content below 0.16 ppm is obtained when
    where the depth Δ is expressed in microns and the Nimax and Ninom contents are expressed as a percentage by weight.- in Figure 4, referring to the same press-hardened parts, the inventors also showed that the diffusible hydrogen content below 0.16 ppm was reached when the nickel enrichment in the Δ layer reached a critical value compared to the nominal Ninom content, that is, when the
    parameter P3 satisfied: A > 0.01, the units being the same as for parameter P2. In Figure 4, curve 2, corresponding to the bottom envelope of the results, is shown.
    [081] Without wishing to be bound by theory, it is believed that these features create a barrier effect against the penetration of hydrogen into the sheet at high temperature, in particular, by an enrichment of nickel in the previous austenitic grain joints, which limits the diffusion of hydrogen.
    [082] The rest of the steel composition is produced from iron and unavoidable impurities that result from the elaboration.
    [083] The method according to the invention will now be described: an intermediate product of the composition indicated above is melted. This intermediate product may be in slab format of thickness typically comprising between 200 mm and 250 mm, or thin slab formats whose typical thickness is on the order of a few tens of millimeters, or any other suitable format. It is conducted at a temperature comprised between 1,250 °C and 1,300 °C and held in this temperature range for a time comprised between 20 and 45 minutes. For the steel composition of the invention, an oxide layer essentially rich in iron and manganese forms by reaction with oxygen from the furnace atmosphere; in that layer, nickel solubility is very low and nickel remains in metallic form. In parallel with the growth of this oxide layer, nickel diffuses to the interface between the oxide and the steel substrate, thus causing the appearance of a nickel-enriched layer within the steel. At this stage, the thickness of this layer depends, in particular, on the nominal nickel content of the steel and the temperature that retains the conditions previously defined. During the subsequent manufacturing cycle, this initial enriched layer is simultaneously subjected to: - a thinning, due to the rate of reduction conferred by successive lamination steps; - a thickening, due to the plate that is kept at high temperatures during successive manufacturing steps . However, this thickening occurs in smaller proportions than during the step of reheating the plates.
    [084] The manufacturing cycle of a hot rolled sheet typically comprises: - hot rolling steps (eg rough rolling, finishing) in a temperature range extending from 1,250 °C to 825 °C; - winding over a temperature range extending from 500 °C to 750 °C.
    [085] The inventors showed that a variation of the parameters of coiling and hot rolling, in the ranges defined by the invention, do not substantially modify the mechanical properties, as the process also tolerated some variation within these ranges, without noticeable impact on the resulting products .
    [086] At this stage, the hot-rolled sheet, whose thickness can typically be 1.5 mm to 4.5 mm, is pickled by a process known per se, which eliminates the oxide layer, so that the enriched layer of nickel is located close to the surface of the sheet.
    [087] When it is desired to obtain a thinner sheet, cold rolling is done with an adequate reduction rate, for example, comprised between 30% and 70% and then annealing at a temperature typically comprised between 740 °C and 820 °C in order to obtain a recrystallization of the work hardened metal. After this heat treatment, the sheet can be cooled to obtain an uncoated sheet, or continuously coated by hot immersion in a bath, using methods known to you, and finally cooled.
    [088] The inventors showed that, among the manufacturing steps detailed above, the step of reheating the plates in a specific temperature range and retention time was the step that had the predominant influence on the characteristics of the nickel-enriched layer on the plate Final. In particular, they showed that the annealing cycle of the cold rolled sheet, whether it comprises a coating step or not, has only a minor influence on the characteristics of the nickel-enriched surface layer. In other words, except for the cold rolling reduction ratio, which thins the nickel-enriched layer by a proportional amount, the nickel enrichment characteristics of this layer are virtually identical in a hot-rolled sheet and in a sheet that is additionally subjected to cold rolling and annealing, whether it comprises a pre-coating step with hot dip or not.
    [089] This precoat can be aluminum, an aluminum alloy (which comprises above 50% aluminum) or an aluminum-based alloy (where aluminum is the majority of the constituent). Advantageously, this precoat is an aluminum-silicon alloy comprising by weight 7% to 15% silicon, 2% to 4% iron and optionally between 15 ppm and 30 ppm calcium, the remainder being aluminum and impurities that result from the elaboration.
    [090] The precoat can also be an aluminum alloy that contains 40% to 45% Zn, 3% to 10% Fe, 1% to 3% Si, where the balance is aluminum and unavoidable impurities that result of the elaboration.
    [091] According to an embodiment, the precoat can be an aluminum alloy, being in the intermetallic form that contains iron. This type of pre-coating is achieved by a heat pre-treatment of pre-coated sheet with aluminum or aluminum alloy. This heat pretreatment is done at a temperature θ1 for a retention time t1, so that the precoat no longer contains free aluminum from the T5 phase of the Fe3Sí2Ali2 type and T6 of the Fe2Si2Al9 type and so as not to cause austenitic transformation in the steel substrate. Preferably, the temperature θ1 is comprised between 620°C and 680°C, and the retention time t1 is comprised between 6 and 15 hours. In this way, the diffusion of iron from the steel sheet to the aluminum or aluminum alloy is obtained. This type of pre-coating then makes it possible to heat the blank blocks, prior to the hot stamping step, at a clearly higher rate, which allows the high temperature retention time during reheating of the blank blocks to be minimized, which it means reducing the amount of hydrogen absorbed during the heating step of the raw blocks.
    [092] Alternatively, the precoat can be galvanized or alloyed by galvanizing, that is, it has an amount of iron comprised between 7% to 12% after heat treatment with alloys carried out in the queue process immediately after the galvanizing bath.
    [093] The pre-coating can also be composed of a superposition of layers deposited in successive steps, in which at least one of the layers can be aluminum or an aluminum alloy.
    [094] After the manufacture described above, the plates are cut or perforated by methods known per se in order to obtain raw blocks whose geometry is related to the final geometry of the piece hardened by pressing and stamping. As explained above, cutting sheets comprising in particular between 0.32% and 0.36% C, between 0.40% and 0.80% Mn and between 0.05% and 1.20% Cr is particularly easy because to the fact that the relatively low mechanical strength at this stage, associated with a ferritic-pearlite microstructure.
    [095] These raw blocks are heated to a temperature between 810 °C and 950 °C in order to completely austenitize the steel substrate, hot stamped, and then retained in the pressing tool in order to obtain a martensitic transformation . The deformation ratio applied during the hot stamping step can be smaller or larger according to the possibility that a cold deformation (stamping) step was done before the austenitization treatment. The inventors have shown that press-hardening thermal heating cycles, which consist of heating the raw blocks close to the Ac3 transformation temperature, and then retaining them at this temperature for several minutes, do not cause noticeable change in the nickel-enriched layer .
    [096] In other words, the characteristics of the surface layer enriched with nickel are similar in the sheet before the press hardening and in the part obtained from the sheet after the press hardening.
    [097] Due to the compositions of the invention having a transformation temperature of Ac3 lower than conventional steel components, it is possible to austenitize the raw blocks with reduced temperature retention times, which serve to reduce the possible absorption of hydrogen in the heating furnaces .
    [098] As the non-limiting examples, the following embodiments illustrate the advantages conferred by the invention.EXAMPLE 1
    [099] The intermediate steel products were supplied with the composition shown in Table 1 below.
    TABLE 1: STEEL COMPOSITIONS (% BY WEIGHT) THE UNDERLINED VALUES DO NOT SATISFY THE INVENTION
    [0100] These intermediate products were brought to 1,275°C and held at that temperature for 45 minutes, then hot rolled with an ERT rolling temperature tip of 950 °C, and a winding temperature of 650 °C. The hot rolled sheets were then blasted in an acid bath with inhibitor to remove only the oxide layer created during the previous manufacturing steps and then cold rolled to a thickness of 1.5 mm. The resulting sheets were cut into the form of raw blocks. Suitability for mechanical cutting was assessed through the force required to perform this operation. This property is, in particular, related to the mechanical strength and hardness of the sheet at this stage. The raw blocks were then brought to the temperature indicated in Table 2 and held at that temperature for 150 seconds before being hot stamped and cooled by retention in the press. The cooling speed, measured between 750 °C and 400 °C, is comprised between 180 °C/s and 210 °C/s. The mechanical tensile strength Rm of the resulting parts, whose structure is martensitic, was measured using 12.5x50 ISO tensile test samples.
    [0101] Additionally, some raw blocks were heated to a temperature between 850 °C and 950 °C for five minutes in an oven under an atmosphere with a dew point of -5 °C. These raw blocks are then hot stamped under conditions identical to those given above. The diffusible hydrogen values in the resulting parts were then measured with a thermal desorption analysis (TDA) method known to you: in this method, a sample to be tested is heated to 900 °C in an infrared heating oven under a nitrogen flow. The hydrogen content arising from desorption is measured as a function of temperature. Diffusible hydrogen is quantified by the total hydrogen desorbed between room temperature and 360 °C. The variation in nickel content in steel near the surface was also measured on the plates implanted by hot stamping using glow discharge optical emission spectroscopy (GDOES, “Glow Discharge Optical Emission Spectrometry”, a technique known to itself). The values of parameters Nimax, Nisurf, Ninom and Δ can be set in this way.
    [0102] The results of these tests are reported in Table 2.

    TABLE 2: HEATING CONDITIONS OF THE RAW BLOCKS AND PROPERTIES RESULTING AFTER PRESSING HARDENING THE UNDERLINED VALUES DO NOT SATISFIED WITH THE INVENTION o= plate more specifically suited for cutting.
    [0103] Sheets A to D are particularly well suited for cutting due to their ferritic-pearlite structure. The press-hardened sheets and parts A to F have characteristics in terms of composition and surface layer enriched with nickel which correspond to the invention.
    [0104] Examples A to D show that a composition containing, in particular, a C content comprised between 0.32% and 0.36%, the Mn content comprised between 0.40% and 0.80%, a chromium content of between 0.05% and 1.20% in combination with a nominal nickel content of 0.30% to 1.20% and a specific layer enriched in this element serves to result in an Rm strength over 1950 MPa and a diffusible hydrogen content at a value less than or equal to 0.16 ppm.
    [0105] The example of test A shows that the nickel content can be decreased between 0.30% and 0.50% which serves to obtain satisfactory results in terms of mechanical strength and resistance to delayed cracking under economical manufacturing conditions.
    [0106] Examples E to F show that satisfactory results can be obtained with a composition containing in particular a carbon content comprising between 0.24% and 0.28% and a manganese content comprising between 1.50% and 3%. The high value of the parameter
    it is associated with a particularly low diffusible hydrogen content.
    [0107] On the other hand, the parts of examples G to K have a diffusible hydrogen content above 0.25 ppm due to the fact that the steels do not have a surface layer enriched with nickel. Furthermore, examples J to K correspond to steel compositions for which the parameter P1 is below 1.1% so that a strength Rm of 1800 MPa is not obtained after hardening by pressing.
    [0108]For steel compositions A to D and H, that is, those for which the carbon content is between 0.32% and 0.35%, Figure 5 shows the nickel content as a function of measured depth compared to the sheet surface as measured by the GDOES technique. The reference letters appearing beside the curve in this figure correspond to the steel reference. Unlike a plate that does not contain nickel (reference H), it can be noted that the plates according to the invention have an enrichment in the surface layer. At a given nominal nickel content (0.79%), it is noted from examples B and C that a range of chromium content from 0.51% to 1.05% serves to preserve the enrichment in the surface layer , which satisfies the conditions of the invention.EXAMPLE 2
    [0109] Hot-rolled steel sheets with a composition corresponding to those of E and F steels above, that is, containing nickel contents of 1% and 1.49% respectively and manufactured under the conditions mentioned above, were supplied .
    [0110] After lamination, the sheets subjected to two types of preparation:- X: pickling acid with inhibitor in order to remove only the oxide layer; - Y: 100 μm grinding.
    [0111] Figure 6, which shows the nickel content measured by glow discharge optical emission spectroscopy of the surface of the plate F, shows that in preparation mode X, a surface layer enriched with nickel is present (curve labeled X) , while grinding eliminated the oxide layer and the nickel-enriched undercoat (curve labeled Y).
    [0112] After cold rolling to a thickness of 1.5 mm, the then prepared raw blocks were then heated to 850 °C in an oven at a speed of 10 °C/s, held at that temperature for five minutes and then hot stamped. In both modes of preparation, the following element is the diffusible hydrogen content measured on the stamped parts:

    [0113] Figure 7 shows the diffusible hydrogen content as a function of the steel composition and the mode of preparation. For example, reference EX refers to sheet and hot stamped part made of composite steel E with preparation mode X.
    [0114] These results show that a nickel-enriched surface layer, ie, one that shows a sufficient nickel content gradient, is necessary to obtain a low diffusible hydrogen content.
    [0115] Plates, 235 mm thick, were prepared with the following composition:
    TABLE 3: STEEL COMPOSITION (% BY WEIGHT)
    [0116] These plates were brought to 1,290 °C and held at that temperature for 30 minutes.
    [0117] They were then hot rolled to a thickness of 3.2 mm according to various winding or rolling end temperatures. The mechanical tensile properties (yield stress Re, tensile strength Rm, total elongation Et) of these hot rolled sheets are reported in Table 4.
    TABLE 4: IMPLEMENTATION CONDITIONS OF HOT ROLLED SHEETS AND RESULTING MECHANICAL PROPERTIES
    [0118] At almost identical winding temperature (T and U tests), it is observed that an edge of rolling temperature variation of 70 °C has only a very small influence on the mechanical properties. At the neighboring end of the rolling temperature (U and V tests), it is observed that a reduction in the winding temperature from 650 °C to 580 °C has only a very small influence, in particular on the resistance which varies by less than 5% . Thus, it is shown that steel sheet manufactured under the conditions of the invention is not sensitive to manufacturing variations, which result in rolled strips having good homogeneity.
    [0119] Figures 8 and 9 show hot rolled sheets from the T and V tests respectively. It can be seen that the ferritic-pearlite microstructures are very similar for the two conditions.
    [0120] The hot rolled sheets were continuously blasted so as to remove only the oxide layer formed in the previous steps while leaving the nickel-enriched layer in place. The sheets were then rolled to a target thickness of 1.4mm. Whatever the hot rolling condition, the desired thickness was able to be achieved; where the rolling forces are similar for the various conditions.
    [0121] The sheets were then annealed at a temperature of 760 °C, which is just above the transformation temperature of Ac1, and then cooled and continuously aluminated by quenching in a bath containing 9% silicon by weight 3% iron by weight and the remainder aluminum and unavoidable impurities. The result is then plates with a coating in the order of 80 g/m2 per surface; this coating has a very regular defect-free thickness.
    [0122] The blanks resulting from the T test conditions in Table 4 above were then cut, heated under various conditions and hot stamped. In all cases, the resulting rapid cooling achieved the steel substrate and a martensitic structure. Some parts additionally undergo a thermal paint baking cycle.

    TABLE 4: IMPLEMENTATION CONDITIONS OF HOT ROLLED SHEETS AND RESULTING MECHANICAL PROPERTIES
    [0123] It is observed that the resulting strength exceeds 1800 MPa, whatever the temperature and retention time of the raw block in the oven, with or without subsequent paint baking treatment.EXAMPLE 4
    [0124] Cold-rolled and annealed steel sheets 1.4 mm thick with compositions corresponding to those of steels A and J above, ie, containing a nickel content of 0.39% and 0%, respectively , and manufactured under the conditions indicated in Example 1, were provided. Next, a coating was applied by hot immersion in a bath whose composition is described in Example 3. This resulted in sheets with a 30 µm thick aluminum alloy precoat from which the raw blocks were cut.
    [0125] These raw blocks were austenitized in an oven at a maximum temperature of 900 °C in an atmosphere with a controlled dew point of -10 °C and the total retention time of the raw blocks in the furnace was 5 or 15 minutes. After austenitization, the raw blocks were quickly transferred from the furnace to a hot stamping press and abruptly cooled by retention in the tool. The test conditions reported in Table 5 are representative of an industrial thin plate hot stamping method.
    TABLE 5: CONDITIONS FOR PERFORMING HOT STAMPING TESTS ON RAW BLOCKS WITH ALUMINUM ALLOY PRECOATING
    [0126] Mechanical tensile properties (strength Rm and total elongation Et) and diffusible hydrogen content were measured in the press-hardened parts and reported in Table 6.
    TABLE 6: MECHANICAL PROPERTIES AND DIFFUSABLE HYDROGEN CONTENT OBTAINED IN PARTS HARDENED BY PRESSING WITH ALUMINUM ALLOY PRECOATING
    [0127] It is observed that the resulting strength of parts A5 to A6 exceeds 1800 MPa and that the diffusible hydrogen content is below 0.16 ppm, while for parts J5 to J6, the strength is below 1800 MPa and the diffusible hydrogen content is above 0.16 ppm. Under the conditions of the invention, the strength characteristics and hydrogen content of the parts are very small as a function of the retention time in the furnace, which ensures very stable production.
    [0128] Thereby, simultaneously press-hardened parts that have a very high mechanical strength and a resistance to delayed cracking can be manufactured with the invention. These parts will be advantageously used as reinforcing parts or structural parts in the field of automotive manufacturing.
    权利要求:
    Claims (29)
    [0001]
    1. LAMINATED STEEL SHEET, for hardening by pressing, for which the chemical composition (A, B, C, D, E, F) is characterized by comprising, with contents expressed in weight: 0.24% < C < 0, 38%0.40% < Mn < 3%0.10% < Si < 0.70% 0.015% < Al < 0.070% 0% < Cr < 2% 0.25% < Ni < 2% 0.015% < Ti < 0.10% 0% < Nb < 0.060% 0.0005% < B < 0.0040% 0.003% < N < 0.010%0.0001% < S < 0.005% 0.0001% < P < 0.025% being understood that the titanium and nitrogen contents satisfy: Ti/N > 3.42, and the carbon, manganese, chromium and silicon contents satisfy:
    [0002]
    2. STEEL SHEET, according to claim 1, characterized by the composition (A, B, C, D) thereof comprising, by weight: 0.32% < C < 0.36% 0.40% < Mn < 0.80% 0.05% < Cr < 1.20%.
    [0003]
    3. STEEL SHEET according to claim 1, characterized in that the composition (E, F) thereof comprises, by weight: 0.24% < C < 0.28% 1.50% < Mn < 3%.
    [0004]
    4. STEEL SHEET, according to any one of claims 1 to 3, characterized in that its composition comprises, by weight: 0.50% < Si < 0.60%.
    [0005]
    5. STEEL SHEET, according to any one of claims 1 to 4, characterized in that its composition comprises, by weight: 0.30% < Cr < 0.50%.
    [0006]
    6. STEEL SHEET, according to any one of claims 1 to 5, characterized in that the composition (A, B, C, D, E) thereof comprises, by weight: 0.30% < Ni < 1.20%.
    [0007]
    7. STEEL SHEET, according to any one of claims 1 to 6, characterized in that the composition (A) thereof comprises, by weight: 0.30% < Ni < 0.50%.
    [0008]
    8. STEEL SHEET, according to any one of claims 1 to 7, characterized in that the composition (A, B, C, D, E, F) thereof comprises, by weight: 0.020% < Ti.
    [0009]
    9. STEEL SHEET, according to any one of claims 1 to 8, characterized in that the composition (A, B, C, D, E, F) thereof comprises, by weight: 0.020% < Ti < 0.040%.
    [0010]
    10. STEEL SHEET, according to any one of claims 1 to 9, characterized in that the composition (A, B, C, D) thereof comprises, by weight: 0.15% < Mo < 0.25%.
    [0011]
    11. STEEL SHEET according to any one of claims 1 to 10, characterized in that the composition (A, B, C, D, E) thereof comprises, by weight: 0.010% < Nb < 0.060%.
    [0012]
    12. STEEL SHEET according to any one of claims 1 to 11, characterized in that the composition (A, B, C, D) thereof comprises, by weight: 0.030% < Nb < 0.050%.
    [0013]
    13. STEEL SHEET according to claim 2, characterized in that the composition (A, B, C, D) thereof comprises, by weight: 0.50% < Mn < 0.70%.
    [0014]
    14. STEEL SHEET, according to claim 2, characterized by the microstructure of the same being ferritic-pearlite.
    [0015]
    15. STEEL SHEET, according to any one of claims 1 to 14, characterized in that the sheet is a hot-rolled sheet.
    [0016]
    16. STEEL SHEET, according to any one of claims 1 to 14, characterized in that the sheet is an annealed and cold-rolled sheet.
    [0017]
    17. STEEL SHEET, according to any one of claims 1 to 16, characterized in that it is pre-coated with a layer of aluminum or aluminum alloy metal or aluminum-based alloy.
    [0018]
    18. STEEL SHEET according to any one of claims 1 to 16, characterized in that it is pre-coated with a layer of zinc metal or zinc alloy or zinc-based alloy.
    [0019]
    19. STEEL SHEET according to any one of claims 1 to 16, characterized in that it is pre-coated with a coating or several coatings of intermetallic alloys containing aluminum and iron and possibly silicon, in which the pre-coating no longer contain free aluminum, of phase T5 of the Fe3Si2Al2 type, and T6 of the Fe2Si2Al9 type.
    [0020]
    20. PART, obtained by hardening by pressing a steel plate of composition (A, B, C, D, E, F), as defined in any one of claims 1 to 13, characterized by having a martensitic or martensitic-bainitic structure .
    [0021]
    21. PART, hardened by pressing, according to claim 20, which contains a nominal nickel content of Ninom, characterized in that the Nisurf nickel content in the steel near the surface is greater than Ninom at a depth Δ, and where, Nimax indicates the maximum nickel content within Δ:
    [0022]
    22. PART, hardened by pressing, according to any one of claims 20 to 21, characterized in that its mechanical strength Rm is greater than or equal to 1800 MPa.
    [0023]
    23. PIECE, hardened by pressing, according to any one of claims 20 to 22, characterized in that it is coated with an aluminum or aluminum-based alloy, or a zinc or zinc-based alloy that results from diffusion between the substrate steel and pre-coating during the press hardening heat treatment.
    [0024]
    24. METHOD OF MANUFACTURING A hot-rolled steel SHEET characterized by comprising successive steps according to which: - an intermediate product with chemical composition (A, B, C, D, E, F), as defined in any one of claims 1 to 13, is melted, and then - the intermediate product is reheated to a temperature comprised between 1.250°C and 1300°C for a retention time at that temperature comprised between 20 and 45 minutes, and then - the intermediate product is hot rolled up to an extremity of rolling temperature, ERT, comprised between 825°C and 950°C in order to obtain a hot rolled plate, and then - the hot rolled plate is spirally wound at a temperature comprised between 500°C and 750°C in order to obtain a hot rolled and spiral laminated sheet, and then the oxide layer formed during the previous steps is pickled (X).
    [0025]
    25. METHOD OF MANUFACTURING A cold-rolled, ringed SHEET characterized by comprising the following successive steps: - a hot-rolled sheet is supplied, spirally wound and pickled (X), manufactured by the method as defined in claim 24 and then - the laminated, spiral-wound and hot pickled (X) sheet is cold rolled to obtain a cold rolled sheet, and then - the cold rolled sheet is annealed at a temperature between 740°C and 820° C in order to obtain an annealed and cold rolled sheet.
    [0026]
    26. METHOD OF MANUFACTURING A PRECOATED SHEET, characterized in that a sheet fabricated laminated according to the method as defined in any one of claims 24 to 25 is provided and then a continuous hot-dip precoat be carried out, wherein the precoat is aluminum or an aluminum or aluminum-based alloy, or zinc or a zinc or zinc-based alloy.
    [0027]
    27. METHOD OF MANUFACTURING A SHEET pre-coated and pre-fabricated with alloys, characterized in that: - a laminated sheet obtained by the method, as defined in any one of claims 24 to 25, is provided and then a pre-coat Continuous hot-dip is carried out with an aluminum or aluminum-based alloy, and then a heat pretreatment of the precoated sheet is carried out at a temperature θ1 between 620°C and 680°C for a retention time t1 between 6 and 15 hours, so that the precoat no longer contains free aluminum of the T5 phase of the Fe3Sí2Ali2 type, and T6 of the Fe2Si2Al9 type, and so that an austenitic transformation no longer occurs in the steel substrate, in that the pretreatment is done in an oven under an atmosphere of hydrogen and nitrogen.
    [0028]
    28. METHOD OF MANUFACTURING A PART hardened by pressing, as defined in any one of claims 20 to 23, characterized in that it comprises successive steps according to which: - a plate manufactured by a method, as defined in any one of the claims 24 to 27, is provided, and then - the plate is cut to obtain a blank block, and then - an optional cold stamping deformation step is done on the blank block, and then - the blank is heated in a temperature between 810°C and 950°C in order to generate a completely austenitic structure in the steel, and then - the blank is transferred to the interior of a press, and then - the blank is hot stamped to obtain a part , and then - the part is kept inside the press to obtain a hardening by martensitic transformation of the austenitic structure.
    [0029]
    29. USE OF A press-hardened PART, as defined in any one of claims 20 to 23, or manufactured according to the method defined in claim 28, characterized in that it is for the manufacture of reinforcement parts or structural parts for automotive vehicles.
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    法律状态:
    2019-08-27| B06U| Preliminary requirement: requests with searches performed by other patent offices: procedure suspended [chapter 6.21 patent gazette]|
    2021-04-27| B09A| Decision: intention to grant [chapter 9.1 patent gazette]|
    2021-06-01| B16A| Patent or certificate of addition of invention granted|Free format text: PRAZO DE VALIDADE: 20 (VINTE) ANOS CONTADOS A PARTIR DE 29/07/2015, OBSERVADAS AS CONDICOES LEGAIS. |
    优先权:
    申请号 | 申请日 | 专利标题
    PCT/IB2014/001428|WO2016016676A1|2014-07-30|2014-07-30|Process for manufacturing steel sheets, for press hardening, and parts obtained by means of this process|
    IBPCT/IB2014/001428|2014-07-30|
    PCT/IB2015/001273|WO2016016707A1|2014-07-30|2015-07-29|Process for manufacturing steel sheets for press hardening, and parts obtained by means of this process|
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