 HOT STAMPED STEEL AND METHOD FOR PRODUCING THE SAME
专利摘要:
patent summary: "hot stamped steel and method for producing the same". in a hot-stamped steel article, where [c] represents a carbon content (mass%), [s] represents a silicon content (mass%), and [mn] represents a manganese content (% mass) by mass), a ratio of 5 x [si] + [mn]) / [c]> 10 is satisfied, and if the metallographic structure contains 80% or more martensite per area fraction and also contains one or more pearlite 10% or less per area fraction, austenite retained at 5% or less by volume ratio, 20% or less ferrite per area fraction, and less than 20% bainite per area fraction, ts x?, which is the product of tensile strength (ts) and orifice expansion ratio (?), is at least 50000 mpa.% and the hardness of martensite as measured by a nanoindentator satisfies h2 / h1 <1.10 and shm <20. 21776723v1 公开号:BR112014017113B1 申请号:R112014017113-0 申请日:2013-01-11 公开日:2019-03-26 发明作者:Toshiki Nonaka；Satoshi Kato；Kaoru Kawasaki；Toshimasa Tomokiyo 申请人:Nippon Steel & Sumitomo Metal Corporation； IPC主号:
专利说明:
[001] The present invention relates to a hot stamped steel having excellent formability for which a cold rolled steel sheet for hot stamping is used, and a method for producing the same. The cold-rolled steel sheet of the present invention includes a cold-rolled steel sheet, a hot-dip galvanized cold-rolled steel sheet, a galvanized and galvanized cold-rolled steel sheet, a sheet electrogalvanized cold-rolled steel and aluminum-coated cold-rolled steel sheet. Priority is claimed in Japanese Patent Application No. 2012-004552, filed on January 13, 2012, the content of which is incorporated herein by reference. RELATED TECHNIQUE [002] Currently, a steel sheet for a vehicle needs to be improved in terms of collision safety and have a reduced weight. Currently, there is a demand for a sheet of high strength steel in addition to a sheet of steel of class 980 MPa (980 MPa or higher) and a sheet of steel of class 1180 MPa (1180 MPa or higher) in terms of strength traction. For example, there is a demand for a sheet of steel having a tensile strength of more than 1.5 GPa. In the circumstance described above, hot stamping (also called hot pressing, cooling in cold dies, cooling in the press or others) is drawing attention as a method to obtain high resistance. Hot stamping refers to a forming method in which a steel sheet is heated to a temperature of 750 ° C or more, formed hot Petition 870190003384, of 11/01/2019, p. 4/59 2/46 (machined) to improve the formability of a high strength steel sheet, and then cooled to thereby extinguish the steel sheet, thereby obtaining desired qualities. [003] A steel sheet having a ferrite and martensite, a steel sheet having a ferrite and bainite, a steel sheet containing austenite retained in the structure or others is known as a steel sheet having a press workability and a high strength . Among the steel sheets described above, a multi-stage steel sheet having a martensite dispersed on a ferrite base (a steel sheet including a ferrite and martensite, that is, a so-called DP steel sheet) has a low yield ratio and high tensile strength, and in addition, it has excellent elongation characteristics. However, the multi-stage steel sheet has poor orifice expandability since the stress is concentrated at an interface between ferrite and martensite, and cracking is likely to originate from the interface. In addition, a sheet of steel having the multiple phases described above is not capable of exhibiting a tensile strength of the class of GPa 1.5. [004] For example, Patent Documents 1 to 3 disclose the multi-stage steel sheets described above. In addition, Patent Documents 4 to 6 describe a relationship between a hardness and the formability of the high strength steel sheet. [005] However, even with the techniques described above of the related technique, it is difficult to satisfy the current requirements for a vehicle such as an additional reduction in weight, an additional increase in strength and a more complicated component shape and a operating performance such as orifice expandability after hot stamping. PREVIOUS TECHNICAL DOCUMENT PATENT DOCUMENT Petition 870190003384, of 11/01/2019, p. 5/59 3/46 [006] [Patent Document 1] Unexamined Japanese Patent Application, First Publication No. H6-128688 [007] [Patent Document 2] Unexamined Japanese Patent Application, First Publication No. 2000-319756 [ 008] [Patent Document 3] Unexamined Japanese Patent Application, First Publication No. 2005-120436 [009] [Patent Document 4] Unexamined Japanese Patent Application, First Publication No. 2005-256141 [0010] [Document Patent 5] Unexamined Japanese Patent Application, First Publication No. 2001-355044 [0011] [Patent Document 6] Unexamined Japanese Patent Application, First Publication No. H11-189842 DISCLOSURE OF THE INVENTION PROBLEMS TO BE SOLVED BY THE INVENTION [0012] The present invention was made in view of the problem described above. That is, an objective of the present invention is to provide a hot-stamped steel for which a cold-rolled steel sheet for hot stamping (including a galvanized steel sheet or an aluminized steel sheet as described below) is used and which it ensures a resistance of 1.5 GPa or more, preferably 1.8 GPa or more, and more preferably 2.0 GPa or more and has a more favorable orifice expandability, and a method for producing the same. Here, hot stamped steel refers to a molded article obtained using the cold-rolled steel sheet described above for hot stamping as a material and forming the material through hot stamping. MEANS TO SOLVE THE PROBLEM [0013] The present inventors first carried out intensive studies in relation to a cold rolled steel sheet for hot stamping used for a hot stamped steel that guarantees Petition 870190003384, of 11/01/2019, p. 6/59 4/46 a resistance of 1.5 GPa or more, preferably 1.8 GPa or more, and more preferably 2.0 GPa or more and has excellent formability (orifice expandability), and hot stamping conditions. As a result, it has been found that, in cold rolled steel sheet for hot stamping (the cold rolled steel sheet before hot stamping), a more favorable formability since then, that is, a product of a strength ratio to TS traction and an orifice expansion À (TS x À) of 50000 MPa% or more can be ensured (i), with respect to a steel composition, establishing an appropriate relationship between an amount of Si, an amount of Mn and an amount of C, (ii) adjusting a fraction (area fraction) of a ferrite and a fraction (area fraction) of a martensite for predetermined fractions, and (iii) adjusting a cold rolling mill reduction to fit a hardness ratio (a difference of a hardness) of the martensite between a superficial portion of a sheet thickness (surface part) and a central portion of the sheet thickness (central part) of the steel sheet and a hardness distribution of the martensite in the central part in a specific range. The cold-rolled steel sheet before hot stamping refers to a cold-rolled steel sheet in a state in which a heating in a hot stamping process in which the steel sheet is heated to 750 ° C to 1000 ° C, worked and cooled is yet to come. In addition, it was discovered that when hot stamping is performed on cold rolled steel sheet for hot stamping under the hot stamping conditions described below, the hardness ratio of martensite between the surface portion of the sheet thickness and the central part of the steel sheet and the hardness distribution of the martensite in the central part is almost maintained even after hot stamping, and a hot stamped steel having a high strength and excellent formability in which TS χ À reaches Petition 870190003384, of 11/01/2019, p. 7/59 5/46 50000 MPa% or more can be obtained. In addition, it was also clarified that it is also effective to suppress a segregation of MnS in the central part of the sheet thickness of the cold rolled steel sheet for hot stamping to improve the formability (orifice expandability) of the hot stamped steel. [0014] In addition, it has also been found that, in cold rolling, it is also effective to adjust a fraction of a cold rolling reduction at each point from an upper point to a third point in a total cold rolling reduction ( cumulative lamination reduction) for a specific range to control the martensite hardness. Based on the discovery described above, the inventors have discovered a variety of aspects of the present invention described below. In addition, it has been found that the effects are not impaired even when hot dip galvanizing, galvanizing and galvanizing, electroplating and aluminum treatment are carried out on cold rolled steel sheet for hot stamping. [0015] (1) That is, according to a first aspect of the present invention, a hot stamped steel is provided including,% by mass, C: more than 0.150% to 0.300%, Si: 0.010% to 1,000%, Mn: 1.50% to 2.70%, P: 0.001% to 0.060%, S: 0.001% to 0.010%, N: 0.0005% to 0.0100%, Al: 0.010% to 0.050%, and optionally one or more of B: 0.0005% to 0.0020%, Mo: 0.01% to 0.50%, Cr: 0.01% to 0.50%, V: 0.001% to 0.100%, Ti: 0.001% to 0.100%, Nb: 0.001% to 0.050%, Ni: 0.01% to 1.00%, Cu: 0.01% to 1.00%, Ca: 0.0005% to 0.0050%, REM: 0.0005% to 0.0050%, and a balance including Fe and unavoidable impurities in which, when [C] represents an amount of C% by mass, [Si] represents an amount of Si% by mass, and [ Mn] represents an amount of Mn% by mass, an expression the following is satisfied, a metallographic structure includes 80% Petition 870190003384, of 11/01/2019, p. 8/59 6/46 or more than one martensite in a fraction of area, and optionally also includes one or more than 10% or less of a pearlite in a fraction of area, 5% or less of an austenite retained in a volume ratio, 20% or less of a ferrite in a fraction of an area, and less than 20% of a bainite in a fraction of an area, TS x λ which is a product of TS, that is, a tensile strength and À, that is, an orifice expansion ratio is 50000MPa% or more, and a martensite hardness measured with a nanoindentator satisfies a next b expression and a next c expression. 5x [Si] + [Mn]) / [C]> 10 H2 / H1 <1.10 oHM <20 (a) (b) (c) [0016] Here, H1 represents an average hardness of martensite in a superficial portion, ο H2 represents the average hardness of martensite in a central part of a sheet thickness which is an area having a width of ± 100 pm in a direction of the thickness of a center of the sheet thickness, and ο σΗΜ represents a variance of the martensite hardness that exists in the central part of the sheet thickness. [0017] (2) In hot stamped steel according to (1) above, a fraction of an MnS area existing in the metallographic structure and having an equivalent diameter of 0.1 pm to 10 pm can be 0.01% or less, and an expression d following can be satisfied. n2 / n1 <1.5 (d) [0018] Here, n1 represents an average density in number per 10,000 pm 2 of MnS in a 1/4 part of the thickness of the leaf, and n2 represents an average density in number per 10,000 pm 2 of MnS in the central part of the sheet thickness. [0019] (3) In hot stamped steel according to (1) or (2) above, a hot dip galvanization can be formed on a surface of the same. Petition 870190003384, of 11/01/2019, p. 9/59 7/46 [0020] (4) In hot-stamped steel according to (3) above, the hot-dip galvanized layer may include galvanized and annealed coating. [0021] (5) In hot stamped steel according to (1) or (2) above, an electroplating can be additionally formed on a surface thereof. [0022] (6) In hot stamped steel according to (1) or (2) above, an aluminization can be additionally formed on a surface thereof. [0023] (7) In accordance with another aspect of the present invention, there is provided a method for producing a hot stamped steel including melting a molten steel having a chemical composition according to (1) above and obtaining a steel; heat the steel; hot rolling steel with a hot rolling instrument having a plurality of points; muddy steel after hot rolling; stripping the steel after winding; cold laminating the steel after pickling with a cold rolling mill having a plurality of points under one condition that satisfies one expression and the next; annealing, in which the steel is heated under 700 ° C to 850 ° C and cooled after cold rolling; to harden the steel after annealing; and hot stamping, where the steel is heated to a temperature range of 750 ° C or more at a temperature rise rate of 5 o C / second or more, formed within the temperature range, and cooled to 20 ° C to 300 ° C at a cooling rate of 10 ° C / second or more after hardening lamination. 1.5 x r1 / r + 1.2 x r2 / r + r3 / r> 1 (e) [0024] Here, ri represents a reduction of individual cold rolling (%) at a. ° point based on a upper point between a plurality of points in the cold rolling process where i is 1, 2 or 3, er represents a reduction of total cold rolling (%) in laPetição 870190003384, of 11/01/2019, pg. 10/59 8/46 cold mining. [0025] (8) In the method for producing hot stamped steel according to (7) above, when CT (° C) represents a winding temperature in the winding; [C] represents an amount of C% by mass, [Si] represents an amount of Si% by mass, [Mn] represents an amount of Mn% by mass in steel; and [Mo] represents an amount of Mo% by mass in the steel, an expression f following can be satisfied. 560 - 474 x [C] - 90 x [Mn] - 20 x [Cr] - 20 x [Mo] <CT <830 - 270 x [C] -90 x [Mn] - 70 x [Cr] - 80 x [Mo] (f) [0026] (9) In the method for producing hot stamped steel according to (7) or (8) above, when T (° C) represents a heating temperature in the heating; t (minutes) represents a time in the oven; and [Mn] represents an amount of Mn% by mass, and [S] represents an amount of S% by mass in steel, a following g expression can be satisfied. T x ln (t) / (1.7 x [Mn] + [S])> 1500 (g) [0027] (10) The method for producing hot stamped steel according to any of (7) to (9) above can additionally include galvanizing between annealing and hardening lamination. [0028] (11) The method for producing hot stamped steel according to (10) above may additionally include alloying between hot dip galvanizing and hardening lamination. [0029] (12) The method for producing the hot stamped steel according to any one of (7) to (9) above may additionally include electroplating between the hardening lamination and the hot stamping. [0030] (13) The method for producing hot stamped steel according to any one of (7) to (9) above may additionally include Petition 870190003384, of 11/01/2019, p. 11/59 9/46 go aluminization between annealing and hardening lamination. EFFECTS OF THE INVENTION [0031] According to the present invention, once an appropriate relationship is established between the amount of C, the amount of Mn and the amount of Si, and the hardness of the martensite measured with a nanoindentator is adjusted to a appropriate value in the molded article after hot stamping, it is possible to obtain a hot stamped steel having a favorable orifice expandability. BRIEF DESCRIPTION OF THE DRAWING [0032] FIG. 1 is a graph that illustrates a relationship between (5 x [Si] + [Mn]) / [C] and TS x À. [0033] FIG. 2A is a graph that illustrates a foundation of an expression b and an expression c, and is a graph that illustrates a relationship between H2 / H1 and the HM of a hot stamped steel. [0034] FIG. 2B is a graph that illustrates a foundation of the expression c, and is a graph that illustrates a relationship between oHM and TS x À. [0035] FIG. 3 is a graph that illustrates a relationship between n2 / n1 and TS x À before and after hot stamping, and illustrating a foundation of the expression d. [0036] FIG. 4 is a graph that illustrates a relationship between 1.5 x r1 / r + 1.2 x r2 / r + r3 / r, and H2 / H1, and illustrating a foundation of an expression e. [0037] FIG. 5A is a graph that illustrates a relationship between an expression f and a fraction of a martensite. [0038] FIG. 5B is a graph that illustrates a relationship between the expression f and a fraction of a pearlite. [0039] FIG. 6 is a graph that illustrates a relationship between T x ln (t) / (1.7 x [Mn] + [S]) and TS x À, and illustrating a foundation of expression g. [0040] FIG. 7 is a perspective view of a hot stamped steel used in an example. Petition 870190003384, of 11/01/2019, p. 12/59 10/46 [0041] FIG. 8 is a flow chart illustrating a method for producing hot stamped steel according to an embodiment of the present invention. MODALITIES OF THE INVENTION [0042] As described above, it is important to establish an appropriate relationship between an amount of Si, an amount of Mn and an amount of C, and furthermore, adjust an appropriate hardness of a martensite in a predetermined position to improve a formability (orifice expansion) of hot-stamped steel. So far, there has been no study regarding a relationship between the formability of hot stamped steel and the hardness of martensite. [0043] Hereinafter, an embodiment of the present invention will be described in detail. [0044] First, the reasons for limiting a chemical composition of a cold-rolled steel sheet for hot stamping (including a hot-dip galvanized cold-rolled steel sheet or a cold-rolled steel sheet coated with aluminum and , in some cases, referred to as a cold rolled steel sheet according to the modality or simply as a cold rolled steel sheet for hot stamping) used for a hot stamped steel according to a modality of the present invention ( hot stamped steel according to the present modality or, in some cases, simply referred to as hot stamped steel) will be described. Henceforth,% which is a unit of an amount of an individual component indicates% by mass. Considering that a quantity of component of a chemical composition of the steel sheet does not change in the hot stamping, the chemical composition is identical both in the cold-rolled steel sheet and in the hot-stamped steel for which the cold-rolled steel sheet is used. Petition 870190003384, of 11/01/2019, p. 13/59 11/46 [0045] C: more than 0.150% to 0.300% [0046] C is an important element to strengthen a ferrite and martensite and to increase the strength of a steel. However, when an amount of C is 0.150% or less, a sufficient amount of a martensite cannot be obtained, and it is not possible to increase the strength sufficiently. On the other hand, when the amount of C exceeds 0.300%, elongation and orifice expansion are significantly degraded. Therefore, a range of the amount of C is adjusted by more than 0.150% and 0.300% or less. [0047] Si: 0.010% to 1,000% [0048] Si is an important element to suppress a generation of a harmful carbide and to obtain multiple phases mainly including ferrite and martensite. However, when an amount of Si exceeds 1,000%, the elongation or expandability of the orifice degrades, and a chemical conversion property also degrades. Therefore, the amount of Si is adjusted to 1,000% or less. In addition, Si is added for deoxidation, but a deoxidation effect is not sufficient in the Si amount of less than 0.010%. Therefore, the amount of Si is adjusted to 0.010% or more. [0049] Al: 0.010% to 0.050% [0050] Al is an important element as a deoxidizing agent. To obtain the deoxidation effect, an amount of Al is adjusted to 0.010% or more. On the other hand, even when Al is added excessively, the effect described above is saturated, and conversely, the steel becomes brittle, and TS x À is decreased. Therefore, the amount of Al is fixed in a range of 0.010% to 0.050%. [0051] Mn: 1.50% to 2.70% [0052] Mn is an important element to improve stiffness and strengthen steel. However, when the amount of Mn is less than 1.50%, it is not possible to increase the resistance sufficiently. By or Petition 870190003384, of 11/01/2019, p. 14/59 12/46 on the other hand, when the amount of Mn exceeds 2.70%, the stiffness becomes excessive, and the elongation or expandability of the orifice is degraded. Therefore, the amount of Mn is adjusted from 1.50% to 2.70%. In a case where higher elongation is required, the amount of Mn is desirably adjusted to 2.00% or less. [0053] P: 0.001% to 0.060% [0054] In a large quantity, P secretes at the grain limits, and deteriorates local elongation and weldability. Therefore, an amount of P is adjusted to 0.060% or less. The amount of P is desirably lower, but an extreme decrease in the amount of P leads to an increase in cost for refinement, and therefore the amount of P is desirably adjusted to 0.001% or more. [0055] S: 0.001% to 0.010% [0056] S is an element that forms MnS and significantly deteriorates local elongation or weldability. Therefore, an upper limit for an amount of S is set to 0.010%. In addition, the amount of S is desirably less; however, due to a refinement cost problem, a lower limit on the amount of S is desirably adjusted to 0.001%. [0057] N: 0.0005% to 0.0100% [0058] N is an important element to precipitate AIN and others and miniaturizes the crystal grains. However, when an amount of N exceeds 0.0100%, a solid nitrogen solution remains and elongation or expandability of the orifice is degraded. Therefore, an amount of N is adjusted to 0.0100% or less. The amount of N is desirably less; however, due to a refinement cost problem, a lower limit on the amount of N is desirably adjusted to 0.0005%. [0059] The cold rolled steel sheet according to the modality has a basic composition including the elements described above and Petition 870190003384, of 11/01/2019, p. 15/59 13/46 a balance including iron and unavoidable impurities, however, in some cases, it includes at least one element of Nb, Ti, V, Mo, Cr, Ca, REM (rare earth metal), Cu, Ni and B as elements which have so far been used in an amount that is equal to or less than an upper limit described below to improve strength, to control a form of a sulfide or an oxide, and others. The chemical elements described above are not necessarily added to the steel sheet, and therefore, their lower limit is 0%. [0060] Nb, Ti and V are elements that precipitate a fine carbonitride and strengthen the steel. In addition, Mo and Cr are elements that increase rigidity and strengthen steel. To obtain the effects described above, it is desirable to include Nb: 0.001% or more, Ti: 0.001% or more, V: 0.001% or more, Mo: 0.01% or more and Cr: 0.01% or more. However, even when Nb: more than 0.050%, Ti: more than 0.100%, V: more than 0.100%, Mo: more than 0.50%, and Cr: more than 0.50% are contained, an effect of increased strength is saturated, and degradation of the elongation or orifice expansion is caused. Therefore, upper limits of Nb, Ti, V, Mo and Cr are adjusted to 0.050%, 0.100%, 0.100%, 0.50% and 0.50%, respectively. [0061] Ca controls the shape of the sulfide or oxide and improves local elongation or orifice expandability. To obtain the effect described above, it is desirable to contain 0.0005% or more of Ca. However, since an excessive addition deteriorates a workability, an upper limit of an amount of Ca is adjusted to 0.0050%. [0062] Similar to Ca, rare earth metal (REM) controls the shape of sulfide and oxide and improves local elongation or orifice expandability. To obtain the effect described above, it is desirable to contain 0.0005% or more of REM. However, since an excessive addition deteriorates workability, an upper limit for an amount of REM is set to 0.0050%. Petition 870190003384, of 11/01/2019, p. 16/59 14/46 [0063] Steel may also include Cu: 0.01% to 1.00%, Ni: 0.01% to 1.00% and B: 0.0005% to 0.0020%. The elements described above can also improve stiffness and can increase the strength of steel. However, to obtain the effect described above, it is desirable to contain Cu: 0.01% or more, Ni: 0.01% or more and B: 0.0005% or more. In quantities that are equal to or less than the quantities described above, the effect that strengthens the steel is small. On the other hand, even when Cu: more than 1.00%, Ni: more than 1.00% and B: more than 0.0020% are added, the strength increase effect is saturated, and the elongation or orifice expandability degrade. Therefore, an upper limit for an amount of Cu is set to 1.00%, an upper limit for an amount of Ni is set to 1.00%, and an upper limit for an amount of B is set to 0.0020% . [0064] In a case where B, Mo, Cr, V, Ti, Nb, Ni, Cu, Ca and REM, at least one element is included. The steel balance includes Fe and unavoidable impurities. As unavoidable impurities, elements other than the elements described above (for example, Sn, As and others) can still be included as long as the characteristics are not impaired. When B, Mo, Cr, V, Ti, Nb, Ni, Cu, Ca and REM are included in quantities that are less than the lower limits described above, the elements are treated as the inevitable impurities. [0065] In addition, in hot stamped steel according to the modality, when [C] represents the amount of C (% by mass), [Si] represents the amount of Si (% by mass) and [Mn] represents the amount of Mn (mass%), it is important to satisfy the following expression to obtain sufficient orifice expandability as illustrated in FIG. 1. (5 x [Si] + [Mn]) / [C]> 10 (a) Petition 870190003384, of 11/01/2019, p. 17/59 15/46 [0066] When a value of (5 x [Si] + [Mn]) / [C] is 10 or less, TS x λ becomes less than 50000 MPa%, and it is not possible to obtain the orifice expandability enough. This is because, when the amount of C is high, a hard phase hardness becomes very high and a difference between a hard phase hardness and a soft phase hardness becomes large, and thus a value of λ deteriorates. if, and, when the amount of Si or the amount of Mn is small, TS is low. Therefore, it is necessary to adjust each element in the ranges described above, and, in addition, to control a balance between their quantities. Since the value of (5 x [Si] + [Mn]) / [C] does not change even after hot stamping as described above, the value is preferably satisfied to produce the cold rolled steel sheet. However, even when (5 x [Si] + [Mn]) / [C]> 10 is satisfied, in a case where H2 / H1 or σΗΜ described below does not satisfy the conditions, sufficient orifice expandability cannot be obtained. In FIG. 1, a reference sign for which the hot stamping indicates the hot stamped steel, and a reference sign for before the hot stamping indicates the cold rolled steel sheet for hot stamping. [0067] In general, it is martensite instead of ferrite to dominate formability (orifice expandability) in cold rolled steel sheet having the metallographic structure mainly including ferrite and martensite. The inventors carried out intensive studies regarding a relationship between hardness and formability such as martensite elongation or orifice expansion. As a result, it was found that when a hardness ratio (a difference in hardness) of the martensite between a superficial portion of a sheet thickness and a central part of the sheet thickness, and a hardness distribution of the martensite in the central part of the thickness sheet is in a predetermined state with respect to a formability of Petition 870190003384, of 11/01/2019, p. 18/59 16/46 hot stamping according to the embodiment as illustrated in FIGS. 2A and 2B, formability such as elongation or orifice expansion is favorable. In addition, it was clarified that when the hardness ratio and the hardness distribution are within a predetermined range on the cold-rolled steel sheet for hot stamping used for the hot stamping formability according to the modality, the hardness and hardness distribution in hot stamped steel are almost maintained as well, and formability such as elongation or orifice expansion is favorable. This is because the hardness distribution of the martensite formed in the cold-rolled steel sheet for hot stamping also has a significant effect on hot stamped steel after hot stamping. Specifically, this is considered to be because the alloying elements condensed in the central part of the sheet thickness still retain a state of being condensed in the central part even after the hot stamping is carried out. That is, in cold-rolled steel sheet for hot stamping, in a case where the difference in martensite hardness between the superficial portion of the sheet thickness and the central part of the sheet thickness is large or a case in which a the variance of the martensite hardness is large in the central part of the sheet thickness, the similar hardness ratio and the similar variance are obtained in hot stamped steel as well. In FIGS. 2A and 2B, a reference sign for after hot stamping indicates hot stamped steel, and a reference sign for before hot stamping indicates cold rolled steel sheet for hot stamping. [0068] The inventors also found that, with respect to a measurement of martensite hardness measured with a nanoindentator manufactured by Hysitron Corporation 1000 times, when the next b expression and the next c expression are satisfied, a Petition 870190003384, of 11/01/2019, p. 19/59 17/46 the stamping of hot-pressed steel improves. Here, a Ή1 is the hardness of the martensite in the superficial portion of the sheet thickness that is within an area having a width of 200 pm in a direction of the thickness of an outermost layer of the hot-stamped steel. A Ή2 is the hardness of the martensite in the central part of the sheet thickness of hot-stamped steel that is found in an area having a width of ± 100 pm in the direction of the thickness of the central part of the sheet thickness. An oHM is the variance of martensite hardness that exists in an area having a width of 200 pm in the direction of thickness in the central part of the thickness of the hot-stamped steel sheet. OH1, oH2eooHM are each obtained from measurements of 300 points. The area having a width of 200 pm in the direction of thickness in the central part of the thickness of the sheet refers to an area having a center in a center of the thickness of the sheet and having a dimension of 200 pm in the direction of the thickness. H2 / H1 <1.10 (b) oHM <20 (c) [Expression 1] [0069] In addition, here, the variance is a value obtained using the expression h below and indicating a distribution of martensite hardness. οΜ = 1ν (ΐιι _ χ .) í-1 (h) [0070] A Xave represents an average value of the measured hardness of the martensite, and X represents the hardness of an i ° martensite. [0071] FIG. 2A illustrates the ratios between the hardness of the martensite in the superficial portion and the hardness of the martensite in the central part of the thickness of the hot-stamped steel sheet and of the cold-rolled steel sheet for hot stamping. In addition, FIG. 2B collectively illustrates the variance of martensite hardness that exists in the width of Petition 870190003384, of 11/01/2019, p. 20/59 18/46 ± 100 μηι in the direction of the sheet thickness from the center of the sheet thickness of the hot stamped steel and the cold rolled steel sheet for hot stamping. As illustrated in FIGS. 2A and 2B, the hardness ratio of the cold rolled steel sheet before hot stamping and the hardness ratio of the cold rolled steel sheet after hot stamping are almost the same. Furthermore, the variances in the hardness of the martensite in the central part of the sheet thickness are also almost as much in the cold-rolled steel sheet before hot stamping as in the cold-rolled steel sheet after hot stamping. [0072] In hot stamped steel, an H2 / H1 value of 1.10 or more represents that the hardness of the martensite in the central part of the sheet thickness is 1.10 or more the hardness of the martensite in the superficial portion of the thickness of the leaf. That is, it indicates that the hardness in the central part of the sheet thickness is very high. As illustrated in FIG. 2A, when ο H2 / H1 is 1.10 or more, oHM reaches 20 or more. In this case, TS x À is less than 50000MPa%, and sufficient formability cannot be achieved after extinguishing, that is, in hot stamped steel. Theoretically, there is a case where a lower limit of H2 / H1 becomes equal in the central part of the sheet thickness and in the superficial portion of the sheet thickness unless a special heat treatment is carried out; however, in a current production process with a view to productivity, the lower limit is, for example, up to about 1.005. [0073] The oHM variance of hot stamped steel being 20 or more indicates that the variation in martensite hardness is large, and there are parts where the hardness is very high locally. In this case, TS x À becomes less than 50000MPa%. That is, sufficient formability cannot be achieved in hot stamped steel. [0074] Next, the metallographic structure of the stamped steel Petition 870190003384, of 11/01/2019, p. 21/59 19/46 hot according to the mode will be described. A fraction of the martensite's area is 80% or more in hot stamped steel according to the modality. When the area fraction of the martensite is less than 80%, sufficient strength that has recently been required for hot stamped steel (eg 1.5 GPA) cannot be achieved. Therefore, the area fraction of the martensite is adjusted to 80% or more. All or the main parts of the metallographic structure of hot stamped steel are occupied by martensite, and may also include one or more from 0% to 10% of a pearlite in a fraction of area, 0% to 5% of an austenite retained in a volume ratio, 0% to 20% of ferrite in a fraction of area, and 0% less than 20% of a bainite in a fraction of area. Although there was a case where 0% to 20% of the ferrite exists, depending on a hot stamping condition, there was no problem with the strength after the hot stamping within the range described above. When the retained austenite remained in the metallographic structure, a secondary functioning fragility and a delayed fracture characteristic are likely to degrade. Therefore, it is preferable that residual austenite is not substantially included; however, inevitably, 5% or less of residual austenite in a volume ratio can be included. Considering that pearlite is a hard and fragile structure, it is preferable not to include pearlite; however, inevitably, up to 10% of the pearlite in a fraction of an area can be included. Bainite, which is a structure that can be formed as a residual structure, and is an intermediate structure in terms of strength or formability, can be included. Bainite can be included up to less than 20% in terms of a fraction of the area. In the modality, the metallographic structures of ferrite, bainite and pearlite were observed through cauterization of Nital, and the metallographic structure of martensite was observed through cauterization Petition 870190003384, of 11/01/2019, p. 22/59 20/46 of Le pera. All metallographic structures were observed in 1/4 of a part of the thickness of the sheet with an optical microscope 1000 times. The volume ratio of the retained austenite was measured with an X-ray diffraction apparatus after polishing the steel sheet to 1/4 of the part of the sheet thickness. [0075] Next, the desirable metallographic structure of the cold rolled steel sheet for hot stamping for which the hot stamped steel according to the modality is used will be described. The metallographic structure of hot stamped steel is affected by the metallographic structure of cold rolled steel sheet for hot stamping. Therefore, when the metallographic structure of the cold-rolled steel sheet for hot stamping is controlled, it is easy to obtain the metallographic structure described above in hot stamped steel. In the cold-rolled steel sheet according to the modality, the area fraction of the ferrite is desirably 40% to 90%. When the ferrite area fraction is less than 40%, the resistance is very high even before hot stamping and there is a case where the shape of the hot stamped steel deteriorates or cuts is difficult. Therefore, the area fraction of the ferrite before hot stamping is desirably adjusted to 40% or more. In addition, in cold rolled steel sheet according to the modality, since a large number of alloying elements, it is difficult to adjust the ferrite area fraction to more than 90%. In the metallographic structure, in addition to ferrite, martensite is included, and the fraction of its area is desirably 10% to 60%. A total of the area fraction of the ferrite and the area fraction of the martensite is desirably 60% or more before hot stamping. The metallographic structure may also include one or more of the pearlite, bainite and austenite retained. However, when the retained austenite remains in the metallographic structure, the fragility of secondary functioning and the delayed fracture characteristics Petition 870190003384, of 11/01/2019, p. 23/59 21/46 are likely to degrade, and therefore it is preferable that the retained austenite is not included substantially. However, inevitably, 5% or less of the retained austenite can be included in a volume ratio. Considering that pearlite is a hard and fragile structure, pearlite is preferably not included; however, inevitably, up to 10% of the pearlite can be included in a fraction of the area. Up to 20% or less of bainite as the residual structure can be included in a fraction of the area for the same reason as described above. Similar to the cold-rolled steel sheet before hot stamping, the metallographic structures of ferrite, bainite and pearlite were observed through Nital etching, and the martensite metallographic structure was observed through etching of Le pera All structures metallographic measurements were observed in 1/4 of a part of the sheet thickness with an optical microscope 1000 times. The volume ratio of the retained austenite was measured with an X-ray diffraction apparatus after polishing the steel sheet to 1/4 of the part of the sheet thickness. [0076] In addition, in hot stamped steel according to the modality, the martensite hardness measured with a nanoindentator 1000 times (indentation hardness (GPa or N / mm 2 ) or a value obtained by converting the indentation hardness to a Vickers hardness (Hv) is specified. In a usual Vickers hardness test, an indent formed is larger than the martensite. Therefore, a macroscopic hardness of the martensite and its peripheral structures (ferrite and others) can be obtained, but it is not possible to obtain the hardness of the martensite itself. Considering that the formability as well as the orifice expandability is significantly affected by the hardness of the martensite itself, it is difficult to evaluate the formability sufficiently only with Vickers hardness. On the contrary, in hot stamped steel according to the modality, since the hardness ratio Petition 870190003384, of 11/01/2019, p. 24/59 22/46 of the martensite hardness measured with the nanoindentator and a dispersion state are controlled in an appropriate range, it is possible to obtain an extremely favorable formability. [0077] The MnS was observed at a location of 1/4 the thickness of the sheet (a location that is 1/4 of the thickness of the sheet below the surface) and the central part of the sheet thickness of hot-stamped steel. As a result, it was observed that a fraction of the MnS area that has an equivalent circular diameter from 0.1 pm to 10 pm is 0.01% or less and, as illustrated in FIG. 3, the following d expression being satisfied are favorably preferable and steadily obtaining TS x À> 50000 MPa%. n2 / n1 <1.5 (d) [0078] Here, n1 represents a density in number (average density in number) (grains / 10000 pm 2 ) of MnS having the equivalent circular diameter of 0.1 pm to 10 pm per unit area in 1/4 part of the sheet thickness of hot stamped steel, and n2 represents a density in number (average density in number) (grains / 10000 pm 2 ) of MnS having an equivalent circular diameter of 0, 1 pm to 10 pm per unit area in the central part of the hot stamped steel sheet thickness. [0079] A reason for improving formability in a case where the MnS area fraction from 0.1 pm to 10 pm is 0.01% or less is considered that when an orifice expansion test is performed, if there are MnS having an equivalent circular diameter of 0.1 pm or more, since stress is concentrated in an immediate vicinity, cracking is likely to occur. One reason for not having MnS having an equivalent circular diameter of less than 0.1 pm is that an effect on the stress concentration is small, and one reason for not having MnS having an equivalent circular diameter of more than 10 pm is that the MnS having the equivalent circular diameter of Petition 870190003384, of 11/01/2019, p. 25/59 23/46 more than 10 μπι is not originally suitable for being worked. In addition, when the fraction of the MnS area having the equivalent circular diameter from 0.1 pm to 10 pm exceeds 0.01%, since it is easy for the fine cracks generated due to the stress concentration to propagate. Therefore, there is a case where the orifice expandability degrades. In addition, a lower limit of the fraction of the MnS area is not particularly specified, but it is reasonable to adjust the lower limit to 0.0001% or again by setting the lower limit to less than 0.0001% in view of a method of measurement described below, limitations of an enlargement and a visual field, the amount of Mn or S, and a desulfurization treatment capacity have an effect on productivity and cost. [0080] When the fraction of MnS area having the equivalent circular diameter from 0.1 pm to 10 pm in hot stamped steel is more than 0.01%, as described above, formability is likely to degrade due to stress concentration. A value of n2 / n1 being 1.5 or more in hot stamped steel indicates that the density in number of MnS in the central part of the sheet thickness of hot stamped steel is 1.5 or more times the density in number of MnS 1/4 of the part of the sheet thickness of the hot-stamped steel. In this case, formability is likely to degrade due to a segregation of MnS in the central part of the sheet thickness. In the modality, the equivalent circular diameter and density in number of the MnS is measured with a field emission scanning electron microscope (Fe-SEM) manufactured by JEOL Ltd. The magnification was 1000 times, and a measurement area of the visual field was adjusted to 0.12x0.09 mm 2 (= 10800 pm 2 ~ 10000 pm 2 ). 10 visual fields were observed at the location of 1/4 of the leaf thickness of the surface (1/4 of the part of the leaf thickness), and 10 visual fields were observed at the central part of the leaf thickness. The fraction of the MnS area was Petition 870190003384, of 11/01/2019, p. 26/59 24/46 with particle analysis software. In this modality, MnS was observed in cold rolled steel sheet for hot stamping in addition to hot stamped steel. As a result, it was observed that a shape of the MnS formed before hot stamping (on cold rolled steel sheet for hot stamping) does not even change the hot stamped steel (after hot stamping). FIG. 3 is a view that illustrates a relationship between the n2 / n1 and TS x À of hot stamped steel, and also illustrates an evaluation of the density measurement results in number of MnS in 1/4 of the part of the sheet thickness and in central part of the sheet thickness of the cold rolled steel sheet for hot stamping using the same index as for hot stamped steel. In FIG. 3, a reference sign after hot stamping indicates the hot stamped steel, and a reference sign before the hot stamping indicates the cold rolled steel sheet for hot stamping. As illustrated in FIG. 3, the n2 / n1 (a ratio of MnS between 1/4 of the part of the sheet thickness and the central part of the sheet thickness) of the cold-rolled steel sheet for hot stamping and the hot-stamped steel is almost equal . This is because the shape of the MnS does not change at a hot stamping heating temperature. [0081] Hot stamped steel according to the modality is obtained, for example, by heating the cold rolled steel sheet according to the modality to 750 ° C to 1000 ° C at a temperature increase rate of 5 o C / second at 500 ° C / second, forming (working) the steel sheet for 1 second at 120 seconds, and cooling the steel sheet to a temperature range of 20 ° C to 300 ° C at a cooling rate of 10 ° C / second at 1000 ° C / second. A hot-stamped steel obtained has a tensile strength of 1500 MPa to 2200 MPa, and can achieve a significant formability improvement effect, particularly on a steel sheet having a Petition 870190003384, of 11/01/2019, p. 27/59 25/46 high resistance of about 1800 MPa to 2000 MPa. [0082] It is preferable to form a galvanization, for example, a hot-dip galvanization, a galvanized and annealed coating, an electro-galvanization, or an aluminization in the hot stamped steel according to the modality in terms of rust prevention. In a case where a metallic coating is formed on the hot-stamped steel, a plated layer does not change under the hot-stamping condition described above, and therefore a metallic coating can be formed on the cold-rolled steel sheet for hot stamping. hot. Even when the metallic coating described above is formed on hot-stamped steel, the effects of the modality are not affected. The metallic coatings described above can be formed with a well-known method. [0083] Hereinafter, a method for producing the cold rolled steel sheet according to the modality and the hot stamped steel according to the modality obtained by hot stamping the cold rolled steel sheet will be described. [0084] When producing the cold-rolled steel sheet according to the modality, as a usual condition, a molten steel melted to have the chemical composition described above is melted continuously after a converter, thus producing a plate. In continuous casting, when a casting rate is fast, a precipitate of Ti and others becomes very fine. On the other hand, when the smelting rate is slow, productivity deteriorates, and therefore the precipitate described above thickens to decrease the number of particles, and there is a case where other characteristics cannot be contaminated such as a fracture. late appears. Therefore, the casting rate is desirably 1.0 m / min at 2.5 m / min. [0085] The plate after melting and casting can be subjected Petition 870190003384, of 11/01/2019, p. 28/59 26/46 used for hot rolling as a foundry. Alternatively, in a case where the plate is cooled to below 1100 ° C, it is possible to reheat the plate to 1100 ° C to 1300 ° C in a tunnel or other oven and subject the plate to hot rolling. When a plate temperature during hot rolling is less than 1100 ° C, it is difficult to ensure a finishing temperature in hot rolling, causing elongation degradation. In addition, in the steel sheet to which Ti or Nb are added, a dissolution of the precipitate becomes insufficient during heating causing a decrease in resistance. On the other hand, when the plate temperature is higher than 1300 ° C, a generation of fouling becomes large, and there is a concern that it may be impossible to make the surface quality of the steel sheet favorable. [0086] In addition, to decrease the fraction of area of MnS, when [Mn] represents the amount of Mn (% by mass) and [S] represents the amount of S (% by mass) in steel, it is preferable that a temperature T (° C) of a heating oven before carrying out the hot rolling, a time within t (minutes), [Mn] and [S] satisfy the following g expression as illustrated in FIG. 6. T x ln (t) / (1.7 x [Mn] + [S])> 1500 (g) [0087] When a value of T x ln (t) / (1.7 x [Mn] + [S ]) is equal to or less than 1500, the fraction of the MnS area becomes large, and there is a case where a difference between the number of MnS in 1/4 part of the leaf thickness and the number of MnS in the central part the thickness of the sheet becomes large. The temperature of the heating oven before carrying out the hot lamination refers to an extraction temperature at a side outlet of the heating oven, and the time inside the oven refers to a time elapsed from a plate insertion. in the hot heating oven to extract the plate from the heating oven. Since the MnS does not change with the bladePetition 870190003384, from 11/01/2019, pg. 29/59 27/46 hot stamping or hot stamping as described above, it is preferable to satisfy the expression g during heating of the plate. The In described above represents a natural logarithm. [0088] Then, the hot rolling is carried out according to a conventional method. At this point, it is desirable to adjust the finishing temperature (a final hot rolling temperature) to an Ar3 temperature at 970 ° C and to perform hot rolling on the plate. When the finishing temperature is lower than the Ar3 temperature, there is a concern that the lamination may become a two-phase lamination (a) and austenite (À), and the elongation may degrade. On the other hand, when the finishing temperature is higher than 970 ° C, a grain size of the austenite thickens, a fraction of the ferrite becomes small, and there is a concern that the elongation may degrade. [0089] The temperature of Ar3 can be estimated from an inflection point after performing a dilatometer test and measuring a change in the length of a test specimen in response to a change in temperature. [0090] After hot rolling, the steel is cooled to an average cooling rate of 20 ° C / second to 500 ° C / second, and is wound at the predetermined winding temperature CT 0 C. In a case where the refrigeration rate is less than 20 ° C / second, pearlite that causes elongation degradation is likely to be formed, which is not preferable. [0091] On the other hand, an upper limit of the cooling rate is not particularly specified, but the upper limit of the cooling rate is desirably set at about 500 ° C / second from the point of view of an instrument specification, but is not limited to this. [0092] After winding, stripping is carried out, and the blade Petition 870190003384, of 11/01/2019, p. 30/59 Cold 28/46 is performed. At this point, as illustrated in FIG. 4, cold lamination is carried out under a condition in which the expression e next is satisfied to obtain a range that satisfies the expression b described above. When the lamination described above is carried out, and then annealing, cooling and others are carried out under the conditions described below, TS x À> 50000 MPa% can be obtained on the cold rolled steel sheet before hot stamping, and furthermore, it is possible to ensure TS x À> 50000 MPa% in hot stamped steel for which cold rolled steel sheet is used. Meanwhile, cold rolling is desirably carried out with a tandem rolling mill in which a plurality of rolling mills are arranged linearly, and the steel sheet is rolled continuously in a single direction, thus obtaining a predetermined thickness. 1.5 x r1 / r + 1.2 x r2 / r + r3 / r> 1.0 (e) [0093] Here, the ri (i = 1, 2 or 3) represents a reduction in target cold rolling individual (%) at a. ° point (i = 1, 2, 3) based on an upper point in cold rolling, and r represents a total target cold rolling reduction (%) in cold rolling. [0094] The reduction of total cold rolling is a so-called cumulative reduction, and is based on the thickness of the sheet at a first point entrance, and is a percentage of the cumulative reduction (a difference between the thickness of the sheet at the entrance of a first pass and the thickness of the sheet at an exit after a final pass) with respect to the base described above. [0095] When cold rolling is carried out under a condition where the expression described above is satisfied, it is possible to sufficiently divide the pearlite into the cold rolling even when large pearlite exists before the cold rolling. As a result, it is possible to burn the pearlite or suppress the fraction of the pearlite area in the extension Petition 870190003384, of 11/01/2019, p. 31/59 29/46 minimum through annealing performed after cold rolling. Therefore, it is easy to obtain a structure that satisfies expression b and expression c. On the other hand, in a case where the expression e is not satisfied, the cold rolling reductions at the upper flow points are not sufficient, and the large pearlite is likely to remain. As a result, it is not possible to form the martensite having a desired shape in an annealing process. [0096] Furthermore, the inventors found that, in the cold-rolled steel sheet that had been subjected to a rolling process satisfying the expression, it was possible to maintain the shape of the martensite structure obtained even after annealing in almost the same state when hot stamping is then carried out, and elongation or orifice expansion becomes advantageous. In a case where the cold-rolled steel sheet for hot stamping according to the modality is heated to a region of austenite through hot stamping, the hard phase including martensite becomes an austenite that has a high C concentration , and the ferrite phase becomes austenite which has a low concentration of C. When austenite is cooled later, austenite forms a hard phase including martensite. That is, when the hot stamping is performed on the steel sheet for hot stamping having the martensite hardness to satisfy the expression and (to make ο H2 / H1 described above in a predetermined range), ο H2 / H1 described above reaches in a predetermined range even after hot stamping, and formability after hot stamping is excellent. [0097] In mode, r, r1, r2 and r3 are the red cold lamination reductions. In general, the reduction of target cold rolling and a reduction of current cold rolling are controlled to become substantially the same value, and cold rolling is carried out. No Petition 870190003384, of 11/01/2019, p. 32/59 30/46 it is preferable to perform the target cold lamination after doing the reduction of the current cold lamination unnecessarily different from the reduction of cold lamination. In a case where there is a big difference between a reduction in target lamination and a reduction in current lamination, it is possible to consider that the modality is performed when the reduction in current cold lamination satisfies the expression e. The current cold rolling reduction is preferably converged within ± 10% of the cold rolling reduction. [0098] After cold rolling, annealing is carried out. When annealing is carried out, recrystallization is caused on the steel sheet, and the desired martensite is formed. Regarding an annealing temperature, it is preferable to perform annealing by heating the steel sheet to a range of 700 ° C to 850 ° C according to a conventional method, and to cool the steel sheet to 20 ° C or a temperature in the which a surface treatment such as hot dip galvanizing is carried out. When annealing is carried out in the range described above, it is possible to ensure a desirable fraction of the ferrite and a fraction of the desirable area of the martensite and obtain a total of the fraction of the ferrite area and the fraction of the area of the martensite of 60% or more, TS x Improvement. [0099] Conditions other than annealing temperature are not particularly specified, but a lower limit of a containment time at 700 ° C to 850 ° C is preferably adjusted by 1 second or more to confidently obtain a predetermined structure, for example, about 10 minutes as long as productivity is not impaired. It is preferable to suitably determine the temperature rise rate to 1 ° C / second to an upper limit of a capacity of the facility, for example, 1000 ° C / sec, and to properly determine the cooling rate of 1 ° C / second to the upper limit of the facility's capacity, for Petition 870190003384, of 11/01/2019, p. 33/59 31/46 example, 500 ° C / second. Hardening lamination can be carried out with a conventional method. An elongation ratio of hardening lamination is, in general, about 0.2% to 5%, and is preferable when yield point elongation is avoided and the shape of the steel sheet can be corrected. [00100] As another more preferable condition of the present invention, when [C] represents the amount of C (% by mass), [Mn] represents the amount of Mn (% by mass), [Si] represents the amount of Si (% by mass), and [Mo] represents the amount of Mo (% by mass) in steel, the winding temperature CT in a winding process preferably satisfies the following expression f. 560 - 474 x [C] - 90 x [Mn] - 20 x [Cr] - 20 x [Mo] <CT <830 - 270 x [C] - 90 x [Mn] - 70 x [Cr] - 80 x [Mo] (f) [00101] When the CT winding temperature is less than 560 - 474 x [C] - 90 x [Mn] - 20 x [Cr] - 20 x [Mo], that is, CT - ( 560 - 474 x [C] - 90 x [Mn] - 20 x [Cr] - 20 x [Mo]) is less than zero as illustrated in FIG. 5A, martensite is formed excessively, and the steel sheet becomes very hard so that it is a case where cold rolling becomes difficult. On the other hand, when the CT winding temperature is greater than 830 - 270 x [C] - 90 x [Mn] - 70 x [Cr] - 80 x [Mo], that is, CT (830 - 270 x [C ] - 90 x [Mn] - 70 x [Cr] - 80 x [Mo]) is greater than zero as illustrated in FIG. 5B, a banded structure including ferrite and pearlite is likely to be formed. In addition, a fraction of the pearlite in the central part of the leaf thickness is likely to become high. Therefore, a uniformity of a distribution of martensite that is formed in the subsequent annealing process degrades, and it is difficult to satisfy the expression described above b. In addition, there is a case where it is difficult for a sufficient amount of martensite to be formed. Petition 870190003384, of 11/01/2019, p. 34/59 [00102] When the expression f is satisfied, the ferrite and the hard phase have an ideal distribution form before hot stamping as described above. In addition, in this case, C and others are likely to diffuse evenly after heating is performed in hot stamping. Therefore, the distribution of martensite hardness in hot stamped steel is close to ideal. When it is possible to ensure the metallographic structure described above more reliably satisfying the expression f, the formability of the hot-stamped steel becomes excellent. [00103] In addition, to improve a rust-preventing ability, it is also preferable to include a hot dip galvanizing process in which a hot dip galvanizing is formed between the annealing process and the hardening and forming lamination process hot-dip galvanizing on a cold-rolled steel sheet surface. In addition, it is also preferable to include an alloying process in which a bond is formed between the hot dip galvanizing process and the hardening lamination process to obtain a galvanized and annealed coating by forming the alloy after galvanizing by hot immersion. In a case where the formation of alloys is carried out, a treatment in which a surface with a galvanized and annealed coating is brought into contact with a substance that oxidizes a bathed surface such as water vapor, thus thickening an oxidized film can still be used on the surface. [00104] It is also preferable to include, for example, an electrogalvanization process in which an electrogalvanization is formed on the surface of the cold rolled steel sheet after the hardening lamination process other than the hot dip galvanizing process and the process formation of galvanized and annealed coating. In addition, it is also preferable to include, rather than Petition 870190003384, of 11/01/2019, p. 35/59 33/46 hot dip galvanizing, an aluminization process in which an aluminization is formed between the annealing process and the hardening lamination process, and forming the aluminization on the surface of the cold-rolled steel sheet. Aluminization is generally hot-dip aluminization and is preferable. [00105] After a series of the treatments described above, hot stamping was performed on the cold-rolled steel sheet obtained for hot stamping, thus producing a hot stamped steel. In a hot stamping process, hot stamping is desirably carried out under, for example, the following conditions. First, the steel sheet is heated to 750 ° C to 1000 ° C at the temperature rise rate of 5 ° C / second to 500 ° C / sec. After warming up, work (training) is carried out for 1 second to 120 seconds. To obtain a high resistance, the heating temperature is preferably higher than an Ac3 temperature. The temperature of Ac3 was estimated from the tipping point of the test specimen length after performing the dilatometer test. [00106] Subsequently, it is preferable to cool the steel sheet to 20 ° C to 300 ° C at the cooling rate of, for example, 10 ° C / second to 1000 ° C / second. When the heating temperature is less than 750 ° C, in hot stamped steel, the martensite fraction is not sufficient, and the resistance cannot be guaranteed. When the heating temperature is greater than 1000 ° C, the steel sheet becomes very soft, and in a case where a metallic coating is formed on the surface of the steel sheet, particularly in a case where zinc is bathed, there is a concern that zinc can be evaporated and burned which is not preferable. Therefore, the heating temperature in the hot stamping process is preferably 750 ° C to 1000 ° C. When the rate of increase has Petition 870190003384, of 11/01/2019, p. 36/59 34/46 perature is less than 5 o C / second, since its control is difficult, and productivity degrades significantly, it is preferable to heat the steel sheet at a rate of temperature increase of 5 o C / second or more . On the other hand, an upper limit on the rate of temperature rise of 500 ° C / second is for current heating capacity, but is not limited to this. At the cooling rate of less than 10 ° C / second, since controlling its rate is difficult, and productivity also significantly degrades, it is preferable to cool the steel sheet at the cooling rate of 10 ° C / second or more. An upper limit on the cooling rate is not particularly specified, but it becomes 1000 ° C / second or less in view of current cooling capacity. One reason for carrying out the temperature rise and forming work within 1 second to 120 seconds is to avoid evaporation of zinc and others in a case where hot dip galvanizing and others are formed on the surface of the sheet. steel. One reason to adjust the refrigeration temperature to 20 ° C (room temperature) to 300 ° C is to ensure that the martensite sufficiently guarantees strength after hot stamping. [00107] According to what has been described above, when the conditions described above are met, it is possible to produce hot-stamped steel in which the hardness distribution or structure is almost maintained even after hot stamping, and therefore resistance is ensured and the most favorable orifice expandability can be achieved. [00108] FIG. 8 illustrates a flow chart (process S1 to S14) of an example of the production method described above. EXAMPLE [00109] A steel having a composition described in Table 1 was melted continuously at a melting rate of 1.0 m / minute at 2.5 Petition 870190003384, of 11/01/2019, p. 37/59 35/46 m / minute, then a plate was heated in a heating oven under a condition in Table 2 according to a conventional method such as casting or after cooling the steel once, and hot rolling was carried out at a temperature of finishing from 910 ° C to 930 ° C, thus producing a hot rolled steel sheet. After that, the hot rolled steel sheet was wound at a CT winding temperature described in Table 2. After that, scale on a surface of the steel sheet was removed by stripping, and a sheet thickness was adjusted to 1.2 mm to 1.4 mm through cold rolling. At this point, cold rolling was performed so that the expression value became the value described in Table 2. After cold rolling, annealing was carried out in a continuous annealing furnace at an annealing temperature described in Tables 3 and 4. In a part of the steel sheets, a hot dip galvanization was formed in the cooling medium after swelling in the continuous annealing furnace, and then alloying was additionally carried out in the part of it, thus forming a galvanized and annealed coating . In addition, an electrogalvanization or an aluminization was formed on the part of the steel sheets. Hardening lamination was carried out at an elongation rate of 1% according to a conventional method. In this state, a sample was taken to evaluate the qualities of the materials and others of the cold rolled steel sheet for hot stamping, and a quality test of the material or others was carried out. Thereafter, to obtain a hot stamped steel having a shape illustrated in FIG. 7, hot stamping where a temperature was raised to a temperature rise of 10 ° C / second, the steel sheet was held at a heating temperature of 850 ° C for 10 seconds, and cooled to 200 ° C or less at a cooling rate of 100 ° C / second was performed. A sample was cut from a location Petition 870190003384, of 11/01/2019, p. 38/59 36/46 of FIG. 7 on a molded article obtained, a material quality test and an observation of the structure were performed, and fractions of individual structures, a density in number of MnS, a hardness, a tensile strength (TS), an elongation (El) , an orifice expansion ratio (À) and others were obtained. The results are described in Tables 3 to 8. Expansion ratios of hole À in Tables 3 to 6 are obtained with the following expression i. À (%) = {(d'- d) / d} x 100 (i) [00110] d ': an orifice diameter when a crack penetrates a sheet thickness [00111] d: an initial orifice diameter [00112 ] With respect to the types of metallic coating in Tables 5 and 6, CR represents a cold-rolled sheet of cold rolled steel, Gl represents a formation of hot dip galvanizing, GA represents a formation of the galvanized and annealed coating, EG represents a formation electrogalvanization, and Al represents a formation of aluminization. [00113] A quantity of 0 in Table 1 indicates that a quantity is equal to or less than a lower measurement limit. [00114] Determinations G and B in Tables 2, 7 and 8 are defined as follows. [00115] G: a target condition expression is satisfied. [00116] B: the expression of target condition is not satisfied. 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INDUSTRIAL APPLICABILITY [00118] According to the present invention, once an appropriate relationship is established between the amount of C, the amount of Mn and the amount of Si, and an appropriate hardness measured with a nano-indent is provided to martensite, it is provided it is possible to supply hot stamped steel ensuring resistance of 1.5 GPa or more, and having a more favorable orifice expandability. BRIEF DESCRIPTION OF THE REFERENCE SYMBOLS S1: SOFTENING PROCESS S2: CASTING PROCESS S3: HEATING PROCESS S4: HOT LAMINATION PROCESS S5: COILING PROCESS S6: STRIPPING PROCESS S7: COLD LAMINATION PROCESS S8: RECOVERY PROCESS S9: CRUISE LAMINATION PROCESS S10: HOT STAMPING PROCESS S11: GALVANIZATION PROCESS S12: ALLOY FORMATION PROCESS S13: ALUMINIZATION PROCESS S14: ELECTROGALVANIZATION PROCESS Petition 870190003384, of 11/01/2019, p. 49/59
权利要求:
Claims (12) [1] 1. Hot stamped steel consisting of,% by mass: C: more than 0.150% to 0.300%; Si: 0.010% to 1,000%; Mn: 1.50% to 2.70%; P: 0.001% to 0.060%; S: 0.001% to 0.010%; N: 0.0005% to 0.0100%; Al: 0.010% to 0.050%; and optionally one or more of: B: 0.0005% to 0.0020%; Mo: 0.01% to 0.50%; Cr: 0.01% to 0.50%; V: 0.001% to 0.100%; Ti: 0.001% to 0.100%; Nb: 0.001% to 0.050%; Ni: 0.01% to 1.00%; Cu: 0.01% to 1.00%; Ca: 0.0005% to 0.0050%; REM: 0.0005% to 0.0050%; and a balance consisting of Fe and unavoidable impurities, characterized by the fact that when [C] represents a quantity of C% by mass, [Si] represents a quantity of Si% by mass, and [Mn] represents a quantity of Mn % by mass, an expression to be satisfied, a metallographic structure consists of 80% or more of a martensite in a fraction of area, and optionally, one or more than 10% or less of a pearlite in a fraction of area, 5 % or less of an austenite retained in a volume ratio, 20% or less of a ferrite in a fraction of area, and less than 20% of a bai Petition 870190003384, of 11/01/2019, p. 50/59 [2] 2/5 nita in a fraction of area, TS χ À which is a product of TS which is a tensile strength and À which is an orifice expansion ratio is 50000 MPa% or more, and a martensite hardness measured with a nanoindentator satisfies an expression b following and an expression c next, (5x [Si] + [Mn]) / [C]> 10 (a) H2 / H1 <1.10 (b) oHM <20 (c) here, H1 represents an average hardness of the martensite in a superficial portion, ο H2 represents the average hardness of the martensite in a central part of a leaf thickness that is an area that has a width of ± 100 pm in the direction of the thickness of a center of the thickness of the leaf, and oHM represents a variance of the martensite hardness that exists in the central part of the leaf thickness. 2. Hot stamped steel, according to claim 1, characterized by the fact that a fraction of an MnS area existing in the metallographic structure and having an equivalent circular diameter of 0.1 pm to 10 pm is 0.01% or minus, and an expression d following is satisfied, n2 / n1 <1.5 (d) here, n1 represents an average density in number per 10,000 pm 2 of MnS in a 1/4 part of the thickness of the leaf, and n2 represents an average density in number per 10,000 pm 2 of MnS in the central part of the leaf thickness. [3] 3. Hot stamped steel according to claim 1 or 2, characterized by the fact that a hot dip galvanized layer is formed on a surface of the same. [4] 4. Hot stamped steel according to claim Petition 870190003384, of 11/01/2019, p. 51/59 3/5 3, characterized by the fact that the hot dip galvanized layer includes a galvanized and annealed layer. [5] 5. Hot stamped steel according to claim 1 or 2, characterized by the fact that an electrogalvanized layer is formed on a surface thereof. [6] 6. Hot stamped steel according to claim 1 or 2, characterized by the fact that an aluminized layer is formed on a surface thereof. [7] 7. Method for producing hot stamped steel, as defined in claim 1, characterized by the fact that it comprises: melting a molten steel having a chemical composition, as defined in claim 1, and obtaining a steel; heat the steel; hot rolling steel with a hot rolling instrument having a plurality of platforms; wind the steel after hot rolling; stripping steel after rolling; cold rolling the steel after pickling with a cold rolling mill having plurality of platforms under one condition that satisfies one expression and following; annealing in which the steel is heated under 700 ° C to 850 ° C and cooled after cold rolling; to harden the steel after annealing; and hot stamping in which the steel is heated to a temperature range of 750 ° C or more at a temperature rise rate of 5 o C / second or more, formed within the temperature range, and cooled to 20 ° C at 300 ° C at a cooling rate of 10 ° C / second or more after hardening lamination, 1.5 x r1 / r + 1.2 x r2 / r + r3 / r> 1 (e) Petition 870190003384, of 11/01/2019, p. 52/59 4/5 here, when i is 1, 2 or 3, ri represents a rolling reduction in cold% individual unit in a non platform based on an upper deck of a plurality of platforms in the cold rolling, R represents a reduction of total cold rolling in% of unit after cold rolling, where, when the CT in the ° C unit represents a winding temperature in the rolling mill, [C] represents an amount of C% by mass, [Mn] represents an amount of Mn% by mass, [Si] represents an amount of Si% by mass, and [Mo] represents an amount of Mo% by mass in steel; a following expression f is satisfied; 560 - 474 x [C] - 90 x [Mn] - 20 x [Cr] - 20 x [Mo] <CT <830 - 270 x [C] - 90 x [Mn] - 70 x [Cr] - 80 x [Mo] (f) [8] 8. Method for producing a hot stamped steel according to claim 7, characterized in that, when T in unit ° C represents a heating temperature in the heating, t in minutes of unit represents a furnace time; and [Mn] represents an amount of Mn% by weight, and [S] represents an amount of S% by weight in steel, an expression following-g is satisfied, T x ln (t) / (1.7 x [Mn] + [S])> 1500 (g). [9] 9. Method for producing a hot-stamped steel according to claim 7, characterized by the fact that it further comprises: galvanize the steel between annealing and hardening lamination. [10] 10. Method for producing a hot stamped steel, according to claim 9, characterized by the fact that it comprisesPetition 870190003384, from 11/01/2019, pg. 53/59 5/5 further: forming alloy steel between hot dip galvanizing and hardening lamination. [11] 11. Method for producing hot stamped steel according to claim 7, characterized by the fact that it further comprises: electrogalvanize steel between hardening lamination and hot stamping. [12] 12. Method for producing a hot stamped steel according to claim 7, characterized by the fact that it further comprises: aluminize the steel between annealing and hardening lamination.
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同族专利:
公开号 | 公开日 KR101660144B1|2016-09-26| BR112014017113A2|2017-06-13| EP2803746A1|2014-11-19| JP5382278B1|2014-01-08| CN104040008A|2014-09-10| CA2863218A1|2013-07-18| US20150050519A1|2015-02-19| US9725782B2|2017-08-08| TW201343932A|2013-11-01| WO2013105631A1|2013-07-18| ZA201404811B|2016-01-27| CN104040008B|2016-08-24| BR112014017113A8|2017-07-04| PL2803746T3|2019-09-30| RU2014129326A|2016-03-10| KR20140102310A|2014-08-21| EP2803746B1|2019-05-01| JPWO2013105631A1|2015-05-11| MX2014008429A|2014-10-06| CA2863218C|2017-07-18| TWI468532B|2015-01-11| EP2803746A4|2016-03-16| ES2733320T3|2019-11-28| RU2581333C2|2016-04-20|
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法律状态:
2018-10-16| B06A| Patent application procedure suspended [chapter 6.1 patent gazette]| 2019-01-22| B09A| Decision: intention to grant [chapter 9.1 patent gazette]| 2019-03-26| B16A| Patent or certificate of addition of invention granted [chapter 16.1 patent gazette]|Free format text: PRAZO DE VALIDADE: 20 (VINTE) ANOS CONTADOS A PARTIR DE 11/01/2013, OBSERVADAS AS CONDICOES LEGAIS. | 2019-10-01| B25D| Requested change of name of applicant approved|Owner name: NIPPON STEEL CORPORATION (JP) | 2021-11-03| B21F| Lapse acc. art. 78, item iv - on non-payment of the annual fees in time|Free format text: REFERENTE A 9A ANUIDADE. | 2022-02-22| B24J| Lapse because of non-payment of annual fees (definitively: art 78 iv lpi, resolution 113/2013 art. 12)|Free format text: EM VIRTUDE DA EXTINCAO PUBLICADA NA RPI 2652 DE 03-11-2021 E CONSIDERANDO AUSENCIA DE MANIFESTACAO DENTRO DOS PRAZOS LEGAIS, INFORMO QUE CABE SER MANTIDA A EXTINCAO DA PATENTE E SEUS CERTIFICADOS, CONFORME O DISPOSTO NO ARTIGO 12, DA RESOLUCAO 113/2013. |
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申请号 | 申请日 | 专利标题 JP2012004552|2012-01-13| JP2012-004552|2012-01-13| PCT/JP2013/050377|WO2013105631A1|2012-01-13|2013-01-11|Hot stamp molded article and method for producing same| 相关专利
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