[0001]The present invention relates to a steel sheet. BACKGROUND ART [0002]
In order to ensure safety of an automobile at a time of collision and weight reduction, members of an automobile structure are required to establish compatibility between high strength and excellent crash resistance. [0003]
Patent Document 1 (JP2013-227614A) describes a high-strength steel sheet made to have a tensile strength of 1470 MPa or more after hot stamping by heating a cold-rolled steel sheet having a predetennined chemical composition at a heating rate of 5 to 100°C/s to a temperature range of an Ac3 point or more to 950°C or less and cooling, after heating, the steel sheet through a temperature range of Ar3 to 350°C at a cooling rate of 50°C/s or more. [0004]
Patent Document 2 (JP2015-117403A) describes a high-strength galvanized steel sheet of which a value obtained by subtracting a Vickers hardness at a 20-p.m-depth point from a surface of the steel sheet from a Vickers hardness at a lOO-iam point from the surface of the steel sheet (AHv) is 30 or more, and describes a method for producing the high-strength galvanized steel sheet. [0005]
Patent Documents 3 and 4 each describe a cold-rolled steel sheet having a predetermined chemical composition.
LIST OF PRIOR ART DOCUMENTS
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PATENT DOCUMENT [0006]
Patent Document 1: JP2013-227614A
Patent Document 2: JP2015-117403A
Patent Document 3: WO 2009/110607
Patent Document 4: JP2009-215571A
SUMMARY OF INVENTION TECHNICAL PROBLEM [0007]
According to the invention described in Patent Document 1, the steel sheet has an excellent effect in that a high-strength component is obtained; however, there is a need for a steel sheet that has improved tensile strength and improved crash resistance. [0008]
According to the invention described in Patent Document 2, the steel sheet includes a microstructure containing, in volume fraction, 20 to 50% of tempered martensite, and thus a sufficient hardness is not obtained, which results in degraded crash resistance. [0009]
The invention described in each of Patent Documents 3 and 4 involves a two-step heat treatment; however, a temperature of first heat treatment is as high as 1100 to 1200°C. Thus, a sufficient hardness is not obtained, which results in degraded crash resistance. [0010]
In order to ensure crash resistance, it is important to restrain cracks from being formed and propagating. For restraining cracks from being formed and propagating, it has been conceived to uniformize a steel micro-structure of a steel sheet, specifically, to form the steel micro-structure into a single structure. A steel micro-structure of the high-strength component described in Patent Document 1 is substantially a single martensite phase and therefore can be considered to be substantially uniform, from a
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steel micro-structure viewpoint. [0011]
However, as a result of more elaborate studies, the present inventors found that crash resistance can be more improved by decreasing not only variations in a steel micro-structure but also variations in hardness. [0012]
An objective of the present invention is to provide a steel sheet that establishes compatibility between high strength and excellent crash resistance.
SOLUTION TO PROBLEM [0013]
First, the present inventors measured both Vickers hardnesses (macro hardnesses) and nano hardnesses (micro hardnesses) of various kinds of steel sheets in their cross sections parallel to a sheet-thickness direction (hereinafter, referred to as a sheet-thickness cross section). As a result, it was revealed that a steel sheet excellent in crash resistance has small variations in both macro hardness and micro hardness as compared with a steel sheet poor in crash resistance. It is considered that such unevenness in macro and micro hardnesses is attributable to coarse carbide produced in hot rolling. [0014]
Hence, the present inventors conducted further studies about how to reduce coarse carbide. In general, coarse carbide is difficult to dissolve through a typical heat treatment cycle. In particular, dissolving of carbide in which an alloying element such as Mn is concentrated is significantly delayed in a typical heat treatment cycle. For accelerating the dissolving of carbide, increasing a heating temperature and a heating duration is useful. It was however confirmed that adjustment of a heating temperature and a heating duration within ranges under heat treatment conditions manageable in a real operation results in a little effect of accelerating the dissolving of carbide. [0015]
Dissolving of carbide is a phenomenon attributable to diffusion of elements.
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The present inventors paid attention to the fact that diffusion coefficients of elements are higher in grain boundary diffusion in which grain boundaries serve as diffusion paths than in intraparticle diffusion in which elements diffuse inside grains. In order to utilize the grain boundary diffusion usefully, the present inventors then attempted to utilize martensite, which includes grain boundaries in a large quantity. Specifically, it was confirmed that coarse carbide was reduced by performing multi-step heat treatment, in which heat treatment to obtain a martensitic steel micro-structure including grain boundaries in a large quantity is performed, and then heat treatment is performed again. It was additionally confirmed that, by setting a coiling temperature after hot rolling at 550°C or less, it is possible to reduce an amount of carbide after the hot rolling and to restrain alloying elements from concentrating in carbide. [0016]
In addition, the present inventors found that crash resistance can be further improved by increasing bendability of a steel sheet. When a steel sheet is subjected to bending deformation, while large tensile stress is applied to a bending-outer-circumferential near-surface portion in a circumferential direction, large compressive stress is applied to a bending-inner-circumferential near-surface portion. By providing a soft layer in an outer layer of a steel sheet, tensile stress and compressive stress occurring in the outer layer of the steel sheet in bending deformation of the steel sheet can be mitigated, which makes it possible to improve bendability of the steel sheet. The present inventors found that bendability of a steel sheet can be further improved by providing a soft layer in an outer layer of the steel sheet and increasing uniformity in hardness in the soft layer. [0017]
The gist of the present invention obtained in this manner is as described in the following (1) or (2). [0018]
(1) A steel sheet having a tensile strength of 1100 MPa or more,
wherein the steel sheet has a micro-structure containing, in volume fraction, tempered martensite: 95% or more, and one or more kinds of ferrite, pearlite, bainite,
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as-quenched martensite, and retained austenite: less than 5% in total,
wherein in a cross section parallel to a sheet-thickness direction of the steel sheet, when a sheet thickness is denoted by t,
in a 300-um-square region centered about a t/2 point, a standard deviation of Vickers hardnesses that are measured under a load of 9.8 N at 30 points is 30 or less,
wherein when a 100-p.m-square region centered about a t/2 point is divided into 10x10, 100 subregions, and at a center of each of the subregions, a nano hardness is measured under a maximum load of 1 mN, out of the subregions, the number of subregions each of which makes a difference in nano hardness of 3 GPa or more from any one of eight surrounding subregions is 10 or less, and
wherein the steel sheet has a chemical composition comprising, in mass%:
C: 0.18% or more to 0.40% or less,
Si: 0.01%) or more to 2.50% or less,
Mn: 0.60% or more to 5.00% or less,
P: 0.0200% or less,
S: 0.0200% or less,
N: 0.0200% or less,
O: 0.0200% or less,
Al: 0%> or more to 1.00% or less,
Cr: 0% or more to 2.00% or less,
Mo: 0% or more to 0.50% or less,
Ti: 0% or more to 0.10%) or less,
Nb: 0% or more to 0.100% or less,
B: 0%> or more to 0.0100% or less,
V: 0% or more to 0.50% or less,
Cu: 0% or more to 0.500% or less,
W: 0% or more to 0.100% or less,
Ta: 0% or more to 0.100% or less,
Ni: 0% or more to 1.00% or less,
Co: 0% or more to 1.00% or less,
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Sn: 0% or more to 0.050% or less, Sb: 0% or more to 0.050% or less, As: 0% or more to 0.050% or less, Mg: 0% or more to 0.050% or less, Ca: 0% or more to 0.050%) or less, Y: 0% or more to 0.050% or less, Zr: 0% or more to 0.050%) or less, La: 0%o or more to 0.050%> or less, Ce: 0%> or more to 0.050%> or less, and the balance: Fe and impurities. [0019]
(2) A steel sheet that includes a substrate layer including the steel sheet according to (1) and a soft layer formed on at least one of surfaces of the substrate layer, wherein a thickness of the soft layer is more than 10 |_im to 0.15t or less per side,
wherein at a 10-(a.m point from a surface of the soft layer, a standard deviation of Vickers hardnesses that are measured under a load of 4.9 N at 150 points is 30 or less, and
wherein an average Vickers hardness Hvi of the soft layer is 0.9 times or less an average Vickers hardness Hvo at a t/2 point. [0020]
The steel sheet according to (1) or (2) may include a galvanized layer, a galvannealed layer, or an electrogalvanized layer on its surface.
ADVANTAGEOUS EFFECTS OF INVENTION [0021]
According to the present invention, a steel sheet that establishes compatibility between high strength and excellent crash resistance is obtained.
BRIEF DESCRIPTION OF DRAWINGS
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[0022]
[Figure 1] Figure 1 is a diagram schematically illustrating locations and regions for measuring hardnesses of a steel sheet. Figure 1(a) is a diagram illustrating a part of a cross section of the steel sheet, and Figure 1(b) is an enlarged view of a region B illustrated in Figure 1(a).
DESCRIPTION OF EMBODIMENTS [0023]
An embodiment of the present invention will be described below. [0024]
(Steel Micro-Structure)
A steel micro-structure of a steel sheet according to the present embodiment will be described. The steel micro-structure of the steel sheet according to the present embodiment contains, in volume fraction, tempered martensite: 95% or more, and one or more kinds of ferrite, pearlite, bainite, as-quenched martensite, and retained austenite: less than 5% in total.
With 95% or more of tempered martensite, the steel sheet can have sufficient strength. From this viewpoint, 98% or more of tempered martensite is preferably contained.
In addition, less than 5% of one or more kinds of ferrite, pearlite, bainite, as-quenched martensite, and retained austenite, in total, is allowed. [0025]
(Macro Hardness)
Next, hardnesses of the steel sheet according to the present embodiment will be described. Figure 1(a) and Figure 1(b) schematically illustrate locations and regions for measuring hardnesses of a steel sheet. Figure 1(a) illustrates a part of a cross section of a steel sheet 10 according to the present embodiment, where the cross section is parallel to a sheet-thickness direction (a sheet-thickness cross section parallel to a rolling direction R). Figure 1(b) is an enlarged view of a region B illustrated in Figure 1(a).
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[0026]
A macro hardness of the steel sheet according to an embodiment is measured in a region A illustrated in Figure 1(a). When a sheet thickness of the steel sheet 10 is denoted by t, the region A is a 300-um-square region that is set in a cross section parallel to the sheet-thickness direction of the steel sheet 10 and is centered about a t/2 point from a surface 10a of the steel sheet 10. ' At the region A, Vickers hardnesses are measured under a load of 9.8 N at 30 randomly selected points, and a standard deviation of these Vickers hardnesses is determined. The steel sheet according to the present embodiment should make this standard deviation 30 or less. The macro hardness tends to vary if coarse carbides are formed. For that reason, small variations in macro hardness can serve as an indicator of restraint on formation of coarse carbides. By making the standard deviation 30 or less, variations in macro hardness attributable to coarse carbides are decreased, so that crash resistance of the steel sheet can be improved. When an operation of determining the standard deviation of Vickers hardnesses as described above is performed in the same manner at five regions, an arithmetic average value of standard deviations of the regions is preferably 30 or less, and the arithmetic average value is more preferably 25 or less. A fracture that occurs when a steel sheet suffers tensile stress tends to occur from a sheet-thickness center portion. For that reason, it is preferable that variations in hardness are small at the t/2 point. The Vickers hardnesses are thus measured in the region centered about the t/2 point. [0027]
(Micro Hardness)
A micro hardness of the steel sheet according to an embodiment is measured in the region B illustrated in Figure 1(a) and Figure 1(b). When the sheet thickness of the steel sheet 10 is denoted by t, the region B is a 100-p.m-square region that is set in a cross section parallel to the sheet-thickness direction of the steel sheet 10 and is centered about a t/2 point from a surface 10a of the steel sheet 10. The region B is divided into 10x10, 100 subregions of equal size, and at a center of each subregion, a nano hardness is measured under a maximum load of 1 mN. That is, the nano
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hardness is measured under a maximum load of 1 mN at 100 points. Out of the subregions, the number of subregions each of which makes a difference in nano hardness of 3 GPa or more from any one of its eight surrounding subregions should be 10 or less. This will be described below in detail. [0028]
As illustrated in Figure 1(b), if a nano hardness in a given subregion is denoted by Hoo, eight subregions that surround the given subregion are the "eight surrounding subregions". If nano hardnesses of the subregions are denoted by Hoi, H02, H03, H04, H05, H06, H07, and Hos, differences in nano hardness are calculated as |Hoo - Hoi |, |Hoo -H02I, |Hoo - H03I, |Hoo - H04I, |Hoo - Hos|, |Hoo - Ho6|, |Hoo - H07I, and |Hoo - Hog|. If any one of the eight differences is 3 GPa or more, the given subregion is determined as "a subregion that makes a difference in nano hardness of 3 GPa or more from any one of its eight surrounding subregions". This operation is performed on 64 subregions, excluding outermost subregions in the region B, and the number of "subregions each of which makes a difference in nano hardness of 3 GPa or more from any one of its eight surrounding subregions" is determined. The steel sheet according to the present embodiment should make this number ten or less. The number is preferably eight or less. Furthermore, the operation of determining nano hardness described above is performed similarly on five regions, and an arithmetic average value of numbers described above is preferably ten or less, and more preferably eight or less. It is considered that variations in micro hardness being small in this manner make variations in hardness attributable to segregation of an element small, and crash resistance of the steel sheet can be improved. Note that the reason for measuring nano hardness in the region centered about the t/2 point is the same as in the measurement of the macro hardness. [0029]
(Tensile Strength)
A tensile strength of the steel sheet according to the present embodiment is 1100 MPa or more. In particular, the tensile strength is preferably 1200 MPa or more, more preferably 1400 MPa or more, and still more preferably 1470 MPa or more. The
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tensile strength of the steel sheet according to the present invention is determined by a tensile test. Specifically, the tensile test is performed in conformance with JIS Z 2241(2011) and using JIS No. 5 test coupons that are taken from the steel sheet in a direction perpendicular to a rolling direction of the steel sheet, and the maximum of measured tensile strengths is determined as the tensile strength of the steel sheet. [0030]
(Chemical Composition)
Next, a chemical composition of the steel sheet according to the present embodiment will be described. Note that the symbol "%" for a content of each element means "mass%." [0031]
C: 0.18% or more to 0.40% or less
C (carbon) is an element that keeps a predetermined amount of martensite to improve a strength of the steel sheet. A content of C being 0.18% or more produces the predetermined amount of martensite, makes it easy to increase the strength of the steel sheet to 1100 MPa or more. Other conditions may make it difficult to obtain a strength of 11000 or more, and thus the content of C is preferably to be 0.22% or more. On the other hand, the content of C is to be 0.40% or less from the viewpoint of restraining embrittlement caused by an excessive increase in the strength of the steel sheet. The content of C is preferably 0.38% or less. [0032]
Si: 0.01% or more to 2.50% or less
Si (silicon) is an element acting as a deoxidizer. In addition, Si is an element that improves the strength of the steel sheet through solid-solution strengthening. In order to obtain these effects by making the steel sheet contain Si, a content of Si is to be 0.01%) or more. On the other hand, the content of Si is to be 2.50% or less from the viewpoint of restraining decrease in workability due to embrittlement of the steel sheet. Si is a ferrite stabilizing element; a high content of Si may lead to an excess of a ferrite amount. This can raise a problem particularly when a cooling rate in heat treatment is high. Therefore, the content of Si is preferably less than 0.60%, and more preferably
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0.58% or less. [0033]
Mn: 0.60% or more to 5.00% or less
Mn (manganese) is an element acting as a deoxidizer and is also an element improving hardenability. In order to obtain tempered martensite sufficiently with Mn, a content of Mn is to be 0.60% or more. On the other hand, if the content of Mn becomes excessive, coarse Mn oxide is formed and can serve as a starting point of a fracture in press molding. From the viewpoint of restraining workability of the steel sheet from deteriorating in this manner, the content of Mn is to be 5.00% or less. [0034]
P: 0.0200% or less
P (phosphorus) is an impurity element and is an element segregating in a sheet-thickness-center portion of the steel sheet to decrease toughness and embrittling a weld zone. A content of P is preferably as low as possible from the viewpoint of restraining decrease in workability and crash resistance of the steel sheet. Specifically, the content of P is to be 0.0200% or less. The content of P is preferably 0.0100% or less. However, in a case where a content of P of a practical steel sheet is decreased to less than 0.00010%, production costs of the steel sheet significantly increase, which is economically disadvantageous. For that reason, the content of P may be 0.00010%) or more. [0035]
S: 0.0200% or less
S (sulfur) is an impurity element and is an element spoiling weldability and spoiling productivity in casting and hot rolling. S is also an element forming coarse MnS to spoil hole expandability. From the viewpoint of restraining decrease in weldability, productivity, and crash resistance, a content of S is preferably as low as possible. Specifically, the content of S is to be 0.0200% or less. The content of S is preferably 0.0100% or less. However, in a case where a content of S of a practical steel sheet is decreased to less than 0.000010%), production costs of the steel sheet significantly increase, which is economically disadvantageous. For that reason, the
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content of S may be 0.000010% or more. [0036]
N: 0.0200% or less
N (nitrogen) is an element forming coarse nitride to degrade formability and crash resistance of the steel sheet and to cause a blowhole to develop during welding. For this reason, a content of N is preferably to be 0.0200%o or less. [0037]
O: 0.0200%) or less
O (oxygen) is an element forming coarse oxide to degrade formability and crash resistance of the steel sheet and to cause a blowhole to develop during welding. For this reason, a content of O is preferably 0.0200%) or less. [0038]
Al: 0% or more to 1.00% or less
Al (aluminum) is an element acting as a deoxidizer and is added when necessary. In order to obtain the effect by making the steel sheet contain Al, a content of Al is preferably 0.02%> or more. However, the content of Al is preferably 1.00% or less from the viewpoint of restraining coarse Al oxide from being produced to decrease workability of the steel sheet. [0039]
Cr: 0% or more to 2.00%> or less
As with Mn, Cr (chromium) is an element being useful in enhancing strength of steel by increasing hardenability. Although a content of Cr may be 0%>, in order to obtain the effect by making the steel sheet contain Cr, the content of Cr is preferably 0.10%) or more. On the other hand, the content of Cr is preferably 2.00% or less from the viewpoint of restraining coarse Cr carbide from being formed to decrease cold formability. [0040]
Mo: 0% or more to 0.50% or less
As with Mn and Cr, Mo (molybdenum) is an element being useful in enhancing strength of steel. Although a content of Mo may be 0%>, in order to obtain the effect by
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making the steel sheet contain Mo, the content of Mo is preferably 0.01% or more. On the other hand, the content of Mo is preferably 0.50% or less from the viewpoint of restraining coarse Mo carbide from being formed to decrease cold workability. [0041]
Ti: 0% or more to 0.10% or less
Ti (titanium) is an element being useful in controlling morphology of carbide. For that reason, Ti may be contained in the steel sheet when necessary. In a case where Ti is contained in the steel sheet, a content of Ti is preferably 0.001% or more. However, from the viewpoint of restraining decrease in workability of the steel sheet, the content of Ti is preferably as low as possible, preferably 0.10% or less. [0042]
Nb: 0% or more to 0.100% or less
As with Ti, Nb (niobium) is an element being useful in controlling morphology of carbide and is also an element being effective at improving toughness by refining the steel micro-structure. For that reason, Nb may be contained in the steel sheet when necessary. In a case where Nb is contained in the steel sheet, a content of Nb is preferably 0.001% or more. However, the content of Nb is preferably 0.100% or less from the viewpoint of restraining fine, hard Nb carbide from precipitating in a large quantity to increase the strength of the steel sheet and degrade ductility of the steel sheet. [0043]
B: 0% or more to 0.0100% or less
B (boron) is an element that restrains ferrite and pearlite from being produced in a cooling process from austenite and accelerates production of a low-temperature transformation structure such as bainite and martensite. In addition, B is an element being beneficial to enhancing strength of steel. For that reason, B may be contained in the steel sheet when necessary. In a case where B is contained in the steel sheet, a content of B is preferably 0.0001% or more. Note that B being less than 0.0001% requires analysis with meticulous attention to detail for its identification and reaches the lower limit of detection for some analyzing apparatus. On the other hand, the content
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of B is preferably 0.0100% or less from the viewpoint of restraining production of coarse B nitride, which can serve as a starting point of a void occurring in press molding of the steel sheet. [0044]
V: 0% or more to 0.50% or less
As with Ti and Nb, V (vanadium) is an element being useful in controlling morphology of carbide and is also an element being effective at improving toughness of the steel sheet by refining the steel micro-structure. For that reason, V may be contained in the steel sheet when necessary. In a case where V is contained in the steel sheet, a content of V is preferably 0.001% or more. On the other hand, the content of V is preferably 0.50% or less from the viewpoint of restraining fine V carbide from precipitating in a large quantity to increase the strength of the steel sheet and degrade ductility of the steel sheet. [0045]
Cu: 0% or more to 0.500% or less
Cu (copper) is an element that is useful in improving strength of steel. Although a content of Cu may be 0%, in order to obtain the effect by making the steel sheet contain Cu, the content of Cu is preferably 0.001% or more. On the other hand, the content of Cu is preferably 0.500% or less from the viewpoint of restraining productivity from being decreased due to hot-shortness in hot rolling. [0046]
W: 0% or more to 0.100% or less
As with Nb and V, W (tungsten) is an element being useful in controlling morphology of carbide and increasing strength of steel. Although a content of W may be 0%, in order to obtain the effect by making the steel sheet contain W, the content of W is preferably 0.001% or more. On the other hand, the content of W is preferably 0.100% or less from the viewpoint of restraining fine W carbide from precipitating in a large quantity to increase the strength of the steel sheet and degrade ductility of the steel sheet. [0047]
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Ta: 0% or more to 0.100% or less
As with Nb, V, and W, Ta (tantalum) is an element being useful in controlling morphology of carbide and increasing strength of steel. Although a content of Ta may be 0%, in order to obtain the effect by making the steel sheet contain Ta, the content of Ta is preferably 0.001% or more, and more preferably 0.002% or more. On the other hand, the content of Ta is preferably 0.100% or less, and more preferably 0.080% or less from the viewpoint of restraining fine Ta carbide from precipitating in a large quantity to increase the strength of the steel sheet and degrade ductility of the steel sheet. [0048]
Ni: 0% or more to 1.00% or less
Ni (nickel) is an element that is useful in improving strength of steel. Although a content of Ni may be 0%, in order to obtain the effect by making the steel sheet contain Ni, the content of Ni is preferably 0.001% or more. On the other hand, the content of Ni is preferably 1.00% or less from the viewpoint of restraining decrease in ductility of the steel sheet. [0049]
Co: 0% or more to 1.00% or less
As with Ni, Co (cobalt) is an element that is useful in improving strength of steel. Although a content of Co may be 0%, in order to obtain the effect by making the steel sheet contain Co, the content of Co is preferably 0.001% or more. On the other hand, the content of Co is preferably 1.00% or less from the viewpoint of restraining decrease in ductility of the steel sheet. [0050]
Sn: 0% or more to 0.050% or less
Sn (tin) is an element that can be contained in steel in a case where scrap is used as a raw material of the steel. A content of Sn is preferably as low as possible and may be 0%. From the viewpoint of restraining cold formability from being decreased due to embrittlement of ferrite, the content of Sn is preferably 0.050% or less, and more preferably 0.040% or less. However, the content of Sn may be 0.001% or more from the viewpoint of restraining increase in refining costs.
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[0051]
Sb: 0% or more to 0.050% or less
As with Sn, Sb (antimony) is an element that can be contained in steel in a case where scrap is used as a raw material of the steel. A content of Sb is preferably as low as possible and may be 0%. From the viewpoint of restraining decrease in cold formability of the steel sheet, the content of Sb is preferably 0.050% or less, and more preferably 0.040% or less. However, the content of Sb may be 0.001% or more from the viewpoint of restraining increase in refining costs. [0052]
As: 0% or more to 0.050% or less
As with Sn and Sb, As (arsenic) is an element that can be contained in steel in a case where scrap is used as a raw material of the steel. A content of As is preferably as low as possible and may be 0%. From the viewpoint of restraining decrease in cold formability of the steel sheet, the content of As is preferably 0.050% or less, and more preferably 0.040% or less. However, the content of As may be 0.001% or more from the viewpoint of restraining increase in refining costs. [0053]
Mg: 0% or more to 0.050% or less
Mg (magnesium) is an element being, in a trace quantity, capable of controlling morphology of sulfide. Although a content of Mg may be 0%, in order to obtain the effect by making the steel sheet contain Mg, the content of Mg is preferably 0.0001% or more, and more preferably 0.0005% or more. On the other hand, from the viewpoint of restraining cold formability from being decreased due to formation of coarse inclusions, the content of Mg is preferably 0.050%> or less, and more preferably 0.040% or less. [0054]
Ca: 0% or more to 0.050% or less
As with Mg, Ca (calcium) is an element being, in a trace quantity, capable of controlling morphology of sulfide. Although a content of Ca may be 0%, in order to obtain the effect by making the steel sheet contain Ca, the content of Ca is preferably
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0.001% or more. On the other hand, from the viewpoint of restraining cold formability of the steel sheet from being decreased by production of coarse Ca oxide, the content of Ca is preferably 0.050% or less, and more preferably 0.040% or less. [0055]
Y: 0% or more to 0.050% or less
As with Mg and Ca, Y (yttrium) is an element being, in a trace quantity, capable of controlling morphology of sulfide. Although a content of Y may be 0%, in order to obtain the effect by making the steel sheet contain Y, the content of Y is preferably 0.001% or more. On the other hand, from the viewpoint of restraining cold formability of the steel sheet from being decreased by production of coarse Y oxide, the content of Y is preferably 0.050% or less, and more preferably 0.040% or less. [0056]
Zr: 0% or more to 0.050% or less
As with Mg, Ca, and Y, Zr (zirconium) is an element being, in a trace quantity, capable of controlling morphology of sulfide. Although a content of Zr may be 0%, in order to obtain the effect by making the steel sheet contain Zr, the content of Zr is preferably 0.001%) or more. On the other hand, from the viewpoint of restraining cold formability of the steel sheet from being decreased by production of coarse Zr oxide, the content of Zr is preferably 0.050% or less, and more preferably 0.040%) or less. [0057]
La: 0% or more to 0.050% or less
La (lanthanum) is an element being, in a trace quantity, useful in controlling morphology of sulfide. Although a content of La may be 0%, in order to obtain the effect by making the steel sheet contain La, the content of La is preferably 0.001% or more. On the other hand, from the viewpoint of restraining cold formability of the steel sheet from being decreased by production of coarse La oxide, the content of La is preferably 0.050% or less, and more preferably 0.040% or less. [0058]
Ce: 0% or more to 0.050% or less
As with La, Ce (cerium) is an element being, in a trace quantity, useful in
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controlling morphology of sulfide. Although a content of Ce may be 0%, in order to obtain the effect by making the steel sheet contain Ce, the content of Ce is preferably 0.001% or more. On the other hand, from the viewpoint of restraining formability of the steel sheet from being decreased by production of Ce oxide, the content of Ce is preferably 0.050% or less, and more preferably 0.040% or less. [0059]
The balance of the chemical composition of the steel sheet according to the present embodiment is Fe (iron) and impurities. Examples of the impurities can include elements that are unavoidably contained from raw materials of steel or scrap or unavoidably contained in a steel-making process and are allowed to be contained within ranges within which the steel sheet according to the present invention can exert the effects according to the present invention. [0060]
(Steel Sheet Including Soft Layer)
The steel sheet according to the present invention may be a steel sheet that includes a substrate layer including the steel sheet described above and a soft layer formed on at least one of surfaces of the substrate layer. The soft layer is determined as follows. First, at a 1/2 sheet-thickness point, five Vickers hardnesses are measured under an indentation load of 4.9 N on a line that is perpendicular to a sheet-thickness direction and parallel to a rolling direction. An arithmetic average value of the five Vickers hardnesses measured in this manner is defined as an average Vickers hardness Hvo at the 1/2 sheet-thickness point. Next, five Vickers hardnesses are measured at each of points that are set every 2% of the sheet thickness from the 1/2 sheet-thickness point toward the surface, on a line that is perpendicular to the sheet-thickness direction and parallel to the rolling direction. An average value of the five Vickers hardnesses measured in this manner at each of sheet-thickness-direction points is determined, and the average value is defined as an average Vickers hardness at each sheet-thickness-direction point. Next, a surface side of a sheet-thickness-direction point at which an average Vickers hardness is 0.9 times or less the average Vickers hardness Hvo at the 1/2 sheet-thickness point is defined as the soft layer.
18

[0061]
When the sheet thickness of the steel sheet is denoted by t, a thickness to of the soft layer is preferably more than 10 urn and 0.15t or less. Making the thickness of the soft layer more than 10 urn makes it easy to improve bendability of the steel sheet. Making the thickness to of the soft layer 0.15t or less restrains excessive decrease in the strength of the steel sheet. The thickness to of the soft layer is a thickness of a soft layer per side. The soft layer is to be formed to have a thickness of more than 10 |j,m and 0.15t or less on at least one of the surfaces of the substrate layer. For example, as long as a soft layer having a thickness of more than 10 [im and 0.15t or less is formed on one surface of the substrate layer, a soft layer formed on the other surface may have a thickness to of 10 p.m or less. However, it is preferable that soft layers each having a thickness of more than 10 um and 0.15t or less be formed on both surfaces. Note that the sheet thickness t of the steel sheet according to the embodiment of the present invention is not limited to a specific thickness; however, the sheet thickness t is preferably 0.8 mm or more to 1.8 mm or less. [0062]
(Hardness of Soft Layer)
A standard deviation of Vickers hardnesses that are measured at 150 points under a load of 4.9 N at a 10 |j.m point from a surface of the steel sheet on a cross section parallel to the sheet-thickness direction of the steel sheet (a sheet-thickness cross section parallel to the rolling direction R) is preferably 30 or less. In order to reduce starting points of cracks occurring in bending deformation of the steel sheet, uniformity of a steel micro-structure of the soft layer present in an outer layer of the steel sheet is important. An average Vickers hardness Hvi of the soft layer is preferably 0.9 times or less the average Vickers hardness Hvo at the t/2 point, more preferably 0.8 times or less, and still more preferably 0.7 times or less. This is because the relatively softer the soft layer in the outer layer, the more easily the bendability of the steel sheet is improved. The determination of the average Vickers hardness Hvo at the t/2 point is as described above, and the average Vickers hardness Hvi of the soft layer is an average value often Vickers hardnesses measured at ten randomly selected points under a load of 4.9 N in
19

the soft layer defined as described above. [0063]
(Plated Steel Sheet)
The steel sheet according to the present embodiment may include a plating layer on its surface. The plating layer may be any one of, for example, a galvanized layer, a galvannealed layer, and an electrogalvanized layer. [0064]
(Production Method)
Next, a production method of the steel sheet according to the present embodiment will be described. The production method described below is an example of a production method of the steel sheet according to the present embodiment, which is not limited to the method described below. [0065]
A cast piece having the chemical composition is produced, and from the obtained cast piece, the steel sheet according to the present embodiment can be produced by the following production method. [0066]
"Casting Step"
There are no specific constraints on a method for producing the cast piece from molten steel having the chemical composition; for example, the cast piece may be produced by a typical method such as continuous slab caster and a thin slab caster. [0067]
"Hot Rolling Step"
There are no specific constraints on hot rolling conditions, either. For example, in a hot rolling step, it is preferable that the cast piece be first heated to 1100°C or more and subjected to holding treatment for 20 minutes or more. This is for driving remelting of coarse inclusions. A heating temperature is more preferably 1200°C or more, and a holding duration is more preferably 25 minutes or more. The heating temperature is preferably 1350°C or less, and the holding duration is preferably 60 minutes or less.
20

In the hot rolling step, when the cast piece heated as described above is subjected to hot rolling, it is preferable that the cast piece be subjected to finish rolling in a temperature range of 850°C or more to. 1000°C or less. In the finish rolling, a more preferable lower limit is 860°C, and a more preferable upper limit is 950°C. [0068]
"Coiling Step"
The hot-rolled steel sheet subjected to the finish rolling is coiled into a coil at 550°C or less. Setting a coiling temperature at 550°C or less makes it possible to restrain concentration of alloying elements such as Mn and Si in carbide that is produced in the coiling step. This enables undissolved carbide in the steel sheet to be reduced sufficiently in a multi-step heat treatment to be described later. As a result, it becomes easy to keep the macro hardness and the micro hardness within their respective ranges defined in the present invention, which enables improvement in the crash resistance of the steel sheet. The coiling temperature is preferably 500°C or less. The coiling temperature is preferably 20°C or more because coiling at a temperature about room temperature decreases productivity.
When necessary, the hot-rolled steel sheet may be subjected to reheating treatment for softening. [0069]
"Pickling Step"
The coiled hot-rolled steel sheet is uncoiled and subjected to pickling. By pickling, oxide scales on surfaces of the hot-rolled steel sheet can be removed, which allows improvement in chemical treatment properties and plating properties of a cold-rolled steel sheet. The pickling may be performed once or may be performed a plurality of times. [0070]
"Cold Rolling Step"
The pickled hot-rolled steel sheet is subjected to cold rolling at a rolling reduction of 30%> or more to 90%> or less. Setting the rolling reduction at 30%> or more makes it easy to keep a shape of the steel sheet flat and to restrain decrease in ductility
21

of the finished product. On the other hand, setting the rolling reduction at 90% or less makes it possible to restrain a cold rolling load from becoming excessive, which makes the cold rolling easy. A lower limit of the rolling reduction is preferably to be 45%, and an upper limit of the rolling reduction is preferably to be 70%. There are no specific constraints on the number of rolling passes and the rolling reduction in each pass. [0071]
"Multi-Step Heat Treatment Step"
After the cold rolling step, the steel sheet according to the present invention is subjected to at least two heat treatments to be produced.
(First Heat Treatment)
In first heat treatment, the steel sheet is first subjected to a heating step in which the steel sheet is heated to a temperature of an Ac3 point or more to 1000°C or less and is held for 10 seconds or more. In a case of producing a steel sheet including a soft layer on its surface, dew-point control is performed to form an atmosphere with an oxygen partial pressure of 1.0 x 10"21 [atm] (1.013 x 10"16 [Pa]) or more, and the steel sheet is subjected to a heating step in which the steel sheet is heated to a temperature of the Ac3 point or more to 1000°C or less and is held for 20 seconds or more. Thereafter, a cooling step for cooling the steel sheet is performed under the following condition 1) or 2).
1) The steel sheet is cooled to a temperature range of 25°C or more to 300°C or less at an average cooling rate of 20°C/sec or more.
2) The steel sheet is cooled to a cooling stop temperature of 600°C or more to 750°C or less at an average cooling rate of 0.5°C/sec or more to less than 20°C/sec (first-stage cooling) and then cooled to a cooling stop temperature of 25°C or more to 300°C or less at an average cooling rate of 20°C/sec or more. An excessively high average cooling rate may tend to cause a poor shape such as bends to occur in the steel sheet, degrading bendability; therefore, the average cooling rates are preferably set at 200°C/sec or less. [0072]
Note that the Ac3 point is determined by the following Formula (a). In
22

Formula (a), each symbol of an element indicates a content of the element (mass%). A symbol of an element that is not contained in steel is to be substituted by zero.
Ac3 point (°C) = 901 - 203xVC - 15.2xNi + 44.7xSi +104xV +31.5xMo +
13.1xW Formula (a)
[0073]
By the first heat treatment step, the steel micro-structure of the steel sheet is formed into a steel micro-structure that mainly includes as-quenched martensite or tempered martensite. Martensite is a steel micro-structure that contains grain boundaries and dislocations in a large quantity. In grain boundary diffusion in which grain boundaries serve as diffusion paths and in dislocation diffusion in which dislocations serve as diffusion paths, elements diffuse faster than in intraparticle diffusion in which elements diffuse inside grains. Since dissolving of carbide is a phenomenon attributable to diffusion of elements, the more grain boundaries are present, the more easily carbide is dissolved. By accelerating dissolving of carbide, carbide is restrained from segregating. [0074]
Setting the heating temperature at the Ac3 point or more makes it easy to obtain a sufficient amount of austenite during heating and makes it easy to obtain a sufficient amount of tempered martensite after cooling. If the heating temperature is more than 1000°C, austenite becomes coarse, and variations in hardness are increased, resulting in a failure to obtain desired properties. Setting the holding duration at 10 seconds or more during heating makes it easy to obtain a sufficient amount of austenite and makes it easy to obtain a sufficient amount of tempered martensite after cooling.
When the heat treatment is performed in the atmosphere with an oxygen partial pressure of 1.0 x 10~21 [atm] or more, decarburization progresses in an outer layer of the steel sheet, as a result of which a soft layer is formed in the outer layer of the steel sheet. In order to obtain a steel sheet including a desired soft layer, it is necessary to control an oxygen partial pressure: P02 of furnace atmosphere within an appropriate range; the oxygen partial pressure is preferably set at 1.0 x 10"21 [atm] or more. [0075]
23

In the cooling step described in 1), setting the average cooling rate at 20°C/sec or more causes sufficient quenching, which makes it easy to obtain martensite. This enables dissolving of carbide to sufficiently progress in second heat treatment to be described later. Setting the cooling stop temperature at 25°C or more makes it possible to restrain decrease in productivity. Setting the cooling stop temperature at 300°C or less makes it easy to obtain a sufficient amount of martensite. This enables dissolving of carbide to sufficiently progress in the second heat treatment to be described later. [0076]
The cooling step described in 2) is performed, for example, in a case where the steel sheet is rapidly cooled through a slow-cooling zone. In the first-stage cooling, setting the average cooling rate at less than 20°C/sec makes it possible to produce ferrite and pearlite. However, with the chemical composition, ferrite transformation and pearlite transformation are unlikely to occur, which can make it easy to restrain excessive production of ferrite and pearlite. Setting the cooling rate in the first-stage cooling at 20°C/sec or more only leads to the same result as in the case where the cooling step described in 1) is performed, and a material quality of the steel sheet does not necessarily deteriorate. At the same time, setting the average cooling rate in the first-stage cooling at 0.5°C/sec or more restrains excessive progress of the ferrite transformation and the pearlite transformation, which makes it easy to obtain a predetermined amount of martensite. [0077]
(Second Heat Treatment)
In the second heat treatment, the steel sheet is first subjected to a heating step in which the steel sheet is reheated to a temperature of the Ac3 point or more and is held for 10 seconds or more. In a case of producing a steel sheet including a soft layer on its surface, dew-point control is performed to form an atmosphere with an oxygen partial pressure of 1.0 x 10"21 [atm] (1.013 x 10"16 [Pa]) or more, and the steel sheet is subjected to a heating step in which the steel sheet is reheated to the temperature of the AC3 point or more and is held for 10 seconds or more. Thereafter, a cooling step for cooling the steel sheet is performed under the following condition 1) or 2).
24

1) The steel sheet is cooled to a temperature range of 25°C or more to 300°C or less at an average cooling rate of 20°C/sec or more.
2) The steel sheet is cooled to a cooling stop temperature of 600°C or more to 750°C or less at an average cooling rate of 0.5°C/sec or more to less than 20°C/sec (first-stage cooling) and then cooled to a cooling stop temperature of 25°C or more to 300°C or less at an average cooling rate of 20°C/sec or more.
[0078]
By the first heat treatment step, a steel micro-structure that mainly includes as-quenched martensite or tempered martensite is formed, where elements easily diffuse. By further performing the second heat treatment step, the steel micro-structure can be formulated, and a sufficient amount of coarse carbide in the substrate layer of the steel sheet can be dissolved. This makes it possible to sufficiently reduce segregation of carbide. As a result, it is possible to increase uniformities in the macro hardness and the micro hardness of the substrate layer. [0079]
Setting the heating temperature at the AC3 point or more makes it easy to obtain a sufficient amount of austenite during heating and makes it easy to obtain a sufficient amount of tempered martensite after cooling. Setting the holding duration at 10 seconds or more during heating makes it easy to obtain a sufficient amount of austenite and makes it easy to obtain a sufficient amount of tempered martensite after cooling. Setting the holding duration at 10 seconds or more during heating makes it possible to dissolve carbide sufficiently. [0080]
In a case of producing a steel sheet including a soft layer on its surface, the heat treatment is performed in an atmosphere with an oxygen partial pressure of 1.0 x 10"21 [atm] or more as described above. By the heat treatment in this manner, decarburization progresses in the outer layer of the steel sheet, as a result of which a soft layer is formed in the outer layer of the steel sheet. In order to obtain a steel sheet including a desired soft layer, it is necessary to control an oxygen partial pressure: P02 of furnace atmosphere within an appropriate range; the oxygen partial pressure is
25

preferably set at 1.0 x 10 [atm] or more. [0081]
In the cooling step described in 1), setting the average cooling rate at 20°C/sec or more causes sufficient quenching, which makes it easy to obtain desired tempered martensite. For that reason, a tensile strength of the steel sheet can be increased to 1100 MPa or more. Setting the cooling stop temperature at 25°C or more makes it possible to restrain decrease in productivity. Setting the cooling stop temperature at 300°C or less makes it easy to obtain desired tempered martensite. For that reason, a tensile strength of the steel sheet can be increased to 1100 MPa or more. [0082]
The cooling step described in 2) is performed, for example, in a case where the steel sheet is rapidly cooled through a slow-cooling zone. In the first-stage cooling, setting the average cooling rate at less than 20°C/sec makes it possible to produce ferrite and pearlite. However, with the chemical composition, ferrite transformation and pearlite transformation are unlikely to occur, which can make it easy to restrain excessive production of ferrite and pearlite. Setting the cooling rate in the first-stage cooling at 20°C/sec or more only leads to the same result as in the case where the cooling step described in 1) is performed, and a material quality of the steel sheet does not necessarily deteriorate. At the same time, setting the average cooling rate in the first-stage cooling at 0.5°C/sec or more restrains excessive progress of the ferrite transformation and the pearlite transformation, which makes it easy to obtain a desired amount of martensite. [0083]
Although effects of the multi-step heat treatment step are sufficiently exerted by performing the two heat treatments, three or more heat treatment steps may be performed in total by performing the second heat treatment step a plurality of times after the first heat treatment step. In a case of producing a steel sheet including a soft layer, the oxygen partial pressure is to be set at 1.0 x 10"21 [atm] or more in at least one of the first heat treatment and the second heat treatment. [0084]
26

"Holding Step"
After the cooling in the last heat treatment step in the multi-step heat treatment-step, the steel sheet is held in a temperature range of 450°C or less to 150°C or more for 10 seconds or more to 500 seconds or less. In this holding step, the steel sheet may be held at a constant temperature or may be heated and cooled in the middle of the step as appropriate. Through this holding step, the as-quenched martensite obtained by the cooling can be tempered. Setting the holding temperature at 450°C or less to 150°C or more makes it possible to restrain the tempering from progressing excessively to increase the tensile strength of the steel sheet to 1100 MPa or more. Setting the holding duration at 10 seconds or more makes it possible to cause the tempering to progress sufficiently. In addition, setting a tempering duration at 500 seconds or less makes it possible to restrain the tempering from progressing excessively to increase the tensile strength of the steel sheet to 1100 MPa or more. [0085]
"Tempering Step"
After the holding step, the steel sheet may be tempered. This tempering step may be a step in which the steel sheet is held or reheated at a predetermined temperature in the middle of cooling to room temperature after the holding step or may be a step in which the steel sheet is reheated to the predetermined temperature after the cooling to room temperature has been finished. A method for heating the steel sheet in the tempering step is not limited to a specific method. However, from the viewpoint of restraining decrease in the strength of the steel sheet, the holding temperature or the heating temperature in the tempering step is preferably 500°C or less. Before the holding step, austenite may not be transformed into martensite but remain as it is; if such austenite is quenched during or after the holding step, an excess of as-quenched martensite may be produced in the steel sheet. By performing the tempering step after the holding step, such as-quenched martensite can be tempered. [0086]
"Plating Step"
The steel sheet may be subjected to plating treatment such as electrolytic
27

plating treatment and deposition plating treatment and may be further subjected to galvannealing treatment after the plating treatment. The steel sheet may be subjected to surface treatment such as formation of an organic coating film, film laminating, treatment with organic salt or inorganic salt, and non-chromium treatment. [0087]
In a case where galvanizing treatment is performed on the steel sheet as the plating treatment, the steel sheet is heated or cooled to a temperature of (temperature of galvanizing bath - 40°C) to (temperature of galvanizing bath + 50°C) and immersed in a galvanizing bath. Through the galvanizing treatment, a steel sheet with a galvanized layer on its surface, that is, a galvanized steel sheet is obtained. As the galvanized layer, for example, one having a chemical composition containing Fe: 7 mass% or more to 15 mass% or less, with the balance expressed as: Zn, Al, and impurities can be used. Alternatively, the galvanized layer may be made of a zinc alloy. [0088]
In a case where the galvannealing treatment is performed after the galvanizing treatment, the galvanized steel sheet is heated to a temperature of 460°C or more to 600°C or less, for example. Setting this heating temperature at 460°C or more allows the steel sheet to be galvannealed sufficiently. Setting this heating temperature at 600°C or less makes it possible to restrain the steel sheet from being galvannealed excessively and deteriorating in corrosion resistance. Through such galvannealing treatment, a steel sheet with a galvannealed layer on its surface, that is, a galvannealed steel sheet is obtained.
EXAMPLE 1 [0089]
Next, Example of the present invention will be described; however, conditions described in Example are merely an example of conditions that was adopted for confirming feasibility and effects of the present invention, and the present invention is not limited to this example of conditions. In the present invention, various conditions can be adopted as long as the conditions allow the objective of the present invention to
28

be achieved without departing from the gist of the present invention. [0090]
Cast pieces having chemical compositions shown in Tables 1 to 3 and Tables 11 to 13 were subjected to hot rolling under conditions shown in Tables 4 to 6 and Tables 14 to 16 and then coiled. The resulting hot-rolled steel sheets were subjected to cold rolling under conditions shown in Tables 4 to 6 and Tables 14 to 16. Subsequently, the resulting cold-rolled steel sheets were subjected to heat treatment under conditions shown in Tables 4 to 6 and Tables 14 to 16. Some of the steel sheets were plated by a conventional method, and some of the plated steel sheets were subjected to galvannealing treatment by a conventional method. The steel sheets obtained in this manner were subjected to identification of their steel micro-structures, measurement of their hardnesses and tensile strengths, and a bending test and a hole expansion test for evaluating their crash resistances, by the following methods. The results are shown in Tables 7 to 10 and Tables 17 to 20. [0091]
(Identification of Steel Micro-Structures)
In the present invention, identification of steel micro-structures and calculation of their volume fractions are performed as follows. [0092]
"Ferrite"
First, a sample including a sheet-thickness cross section that is parallel to a rolling direction of a steel sheet is taken, and the cross section is determined as an observation surface. Of the observation surface, a 100 urn x 100 |_im region centered about a 1/4 sheet-thickness point from a surface of the steel sheet is determined as an observation region. An electron channeling contrast image, which is seen by observing this observation region under a scanning electron microscope at 1000 to 50000x magnification, is an image illustrating a difference in crystal orientation between grains in a form of a difference in contrast. In this electron channeling contrast image, an area of a uniform contrast illustrates ferrite. An area fraction of ferrite identified in this manner is then calculated by a point counting procedure
29

(conforming to ASTM E562). The area fraction of ferrite calculated in this manner is
regarded as a volume fraction of ferrite.
[0093]
"Pearlite"
First, the observation surface is etched with Nital reagent. Of the etched observation surface, a 100 (j.m x 100 |j.m region centered about a 1/4 sheet-thickness point from a surface of the steel sheet is determined as an observation region. This observation region is observed under an optical microscope at 1000 to 50000x magnification, and in an observed image, an area of a dark contrast is regarded as pearlite. An area fraction of pearlite identified in this manner is then calculated by the point counting procedure. The area fraction of pearlite calculated in this manner is regarded as a volume fraction of pearlite. [0094]
"Bainite and Tempered Martensite"
An observation region obtained by the etching with Nital reagent is observed under a field emission scanning electron microscope (FE-SEM) at 1000 to 50000x magnification. In this observation region, bainite and tempered Martensite are identified from positions and arrangement of cementite grains included inside a steel micro-structure, as follows. [0095]
Bainite is present in a state where cementite or retained austenite grains are present in lath bainitic ferrite boundaries and in a state where cementite is present inside lath bainitic ferrite. In a case where cementite or retained austenite grains are present in the lath bainitic ferrite boundaries, the bainitic ferrite boundaries are found, so that bainite can be identified. In a case where cementite is present inside the lath bainitic ferrite, the number of relations in crystal orientation between bainitic ferrite and cementite is one, and cementite grains have the same variant, so that bainite can be identified. An area fraction of bainite identified in this manner is calculated by the point counting procedure. The area fraction of bainite is regarded as a volume fraction of bainite.
30

[0096]
In tempered martensite, cementite grains are present inside martensite laths; the number of relations in crystal orientation between martensite laths and cementite is two or more, and cementite has a plurality of variants, so that tempered martensite can be identified. An area fraction of tempered martensite identified in this manner is calculated by the point counting procedure. The area fraction of tempered martensite is regarded as a volume fraction of tempered martensite. [0097]
"As-quenched Martensite"
First, an observation surface similar to the observation surface used for the identification of ferrite is etched with LePera reagent, and a region similar to that used for the identification of ferrite is determined as an observation region. In the etching with the LePera reagent, martensite and retained austenite are not etched. For that reason, the observation region etched with the LePera reagent is observed under the FE-SEM, and areas that are not etched are regarded as martensite and retained austenite. Then, a total area fraction of martensite and retained austenite identified in this manner is calculated by the point counting procedure, and the area fraction is regarded as a total volume fraction of martensite and retained austenite.
Next, from the total volume fraction, a volume fraction of retained austenite that is calculated as follows is subtracted, so that a volume fraction of as-quenched martensite can be calculated. [0098]
"Retained Austenite"
In the present invention, an area fraction of retained austenite is determined by X-ray measurement as follows. First, a portion of the steel sheet from its surface to 1/4 of its sheet thickness is removed by mechanical polishing and chemical polishing. Next, a surface subjected to the chemical polishing is subjected to measurement using MoKot X-ray as a characteristic X-ray. Then, based on an integrated intensity ratio between diffraction peaks of (200) and (211) of a body-centered cubic lattice (bcc) phase and diffraction peaks of (200), (220), and (311) of a face-centered cubic lattice
31

(fee) phase, an area fraction Sy of retained austenite is calculated by the following formula. The area fraction Sy of retained austenite calculated in this manner is regarded as a volume fraction of retained austenite. Sy = (I200f + I220f + I311f) / (1200b + 1211b) x 100
Here, I200f, I220f, and 131 If represent intensities of diffraction peaks of (200), (220), and (311) of an fee phase, respectively, and 1200b and 1211b represent intensities of diffraction peaks of (200) and (211) of a bec phase, respectively. [0099]
(Thickness of Soft Layer)
A method for measuring the thickness to of a soft layer, that is, a definition of a soft layer is as described above. [0100]
(Measurement of Hardness)
A method for measuring the macro hardness of the steel sheet is as described above. That is, in a 300-um-square region that is set in a cross section parallel to a sheet-thickness direction of the steel sheet and is centered about a t/2 point from a surface of the steel sheet, Vickers hardnesses are measured under a load of 9.8 N at 30 randomly-selected points, and a standard deviation of these Vickers hardnesses (macro-hardness standard deviation) is determined. In addition, a method for measuring the micro hardness of the steel sheet is as described above. That is, in a 100-um-square region that is set in a cross section parallel to the sheet-thickness direction of the steel sheet and is centered about a t/2 point from the surface of the steel sheet, the region is divided into 10x10, 100 subregions of equal size. At a center of each subregion, a nano hardness is measured under a maximum load of 1 mN. Then, out of the subregions, the number of subregions each of which makes a difference in nano hardness of 3 GPa or more from any one of its eight surrounding subregions (micro-hardness variation) was determined.
A method for measuring a hardness of the soft layer is as described above. That is, at a 10 jam point from a surface of the steel sheet on a cross section parallel to the sheet-thickness direction of the steel sheet, Vickers hardnesses are measured at 150
32

points under a load of 4.9 N, and a standard deviation of the Vickers hardnesses was determined. A method for measuring an average Vickers hardness Hvi of the soft layer is as described above.
In the present example, soft layers are formed on both surfaces of the steel sheet; however, thicknesses of the soft layers formed on respective surfaces under the production conditions make no significant difference, and thus the tables show thicknesses of soft layers each formed on one surface. [0101]
(Measurement of Tensile Strength TS and Elongation El)
Measurement was performed in conformance with JIS Z 2241(2011) and using No. 5 test coupons that were taken from the steel sheet in a direction perpendicular to a rolling direction of the steel sheet, and tensile strengths TS (MPa) and elongations El (%) were determined. [0102]
(Bending Test)
Bendability was evaluated in accordance with the VDA standard (VDA238-100) defined by German Association of the Automotive Industry under the following measurement conditions. In the present invention, a maximum bending angle a was determined by converting a displacement at a maximum load obtained by the bending test into an angle in accordance with the VDA standard. A test specimen resulting in a maximum bending angle a (deg) of 2.37t2 - 14t + 65 or more was rated as good. For a steel sheet including a soft layer, a test specimen resulting in a maximum bending angle a (deg) of 2.37t2 - 14t + 80 or more was rated as good. Here, t denotes a sheet thickness (mm).
Test specimen dimensions: 60 mm (rolling direction) x 60 mm (direction perpendicular to rolling direction)
Bending ridge line: A punch was pressed such that a bending ridge line extends in a direction perpendicular to the rolling direction.
Test method: Roll supported, punch press
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TABLE 2
No. Chemical composition(mass% the balance: Fe and impurities)

C Si Mn P S N 0 Al B Ti Nb V Mo Cr Co Ni Cu w Ta Sn Sb As Mg Ca

21 0.18 0.27 1.30 0.0030 0.0068 0.0006 0.0012 0.58 0.0016 0.01 - - - - - - - - - - - - - -
22 0.18 1.91 1.50 0.0027 0.0016 0.0023 0.0014 0.10 0.0008 - 0.013 - - - - - - - - - - - - -
23 0.21 0.38 0.80 0.0036 0.0164 0.0007 0.0156 0.67 0.0012 - - - - 0.23 - - - - - - - - -
24 0.18 0.44 0.60 0.0016 0.0115 0.0015 0.0015 0.03 0.0016 0.05 - - - - - 0.32 - - - - - - - -
25 0.19 0.20 1.70 0.0014 0.0171 0.0055 0.0022 0.08 0.0010 - 0.038 0.22 - - - - - - - - - - - -
26 0.34 0.10 0.90 0.0006 0.0015 0.0113 0.0137 0.23 0.0019 - - - - - 0.12 - - - - - - - - -
27 0.20 1.44 1.10 0.0027 0.0180 0.0034 0.0035 0.06 0.0019 - 0.018 - - - - - - - - - - - -
28 0.21 0.34 2.30 0.0079 0.0029 0.0011 0.0030 0.17 0.0008 0.01 - - 0.15 - - - - - - - - - -
29 0.19 0.33 4.10 0.0013 0.0044 0.0045 0.0028 0.15 - - 0.043 - - - - - 0.020 - - - - - -
30 0.20 0.82 1.60 0.0040 0.0012 0.0035 0.0015 0.74 0.0068 - 0.015 0.05 - - - - - - - - 0.020 - - -
31 0.37 0.47 1.40 0.0052 0.0004 0.0033 0.0181 0.08 0.0030 0.01 - - - - - - - - - - - - - -
32 0.36 0.53 0.60 0.0024 0.0103 0.0033 0.0035 - 0.0016 - - 0.41 - - - - - - - - - - - -
33 0.18 0.20 4.00 0.0031 0.0130 0.0027 0.0121 - 0.0011 - - 0.14 - - - - - - - - - - -
M QJ^ 1.45 3.70 0.0011 0.0024 0.0014 0.0011 0.14 0.0079 - - - - - - - - - - - - - -
35 0.41 0.82 4.50 0.0021 0.0007 0.0072 0.0028 0.10 0.0002 - - - - - - - - - - - - - -
36 0.38 2.60 2.60 0.0155 0.0003 0.0173 0.0013 0.12 0.0011 - - - - - - - - - - 0.011 - - -
37 0.26 0.03 0.25 0.0024 0.0162 0.0012 0.0047 0.72 0.0014 - - - - - - - - - - - - - - -
38 0.21 0.54 5.10 0.0013 0.0176 0.0049 0.0025 0.67 0.0079 - - - - - - - - - - - - - - -
39 0.37 1.72 4.00 0.0205 0.0014 0.0127 0.0150 0.16 0.0020 - - - - 0.34 - - - - - - - -
40 0.32 0.69 2.10 0.0009 0.0208 0.0131 0.0028 0.02 0.0006 - - - - - - - - - - - - - -

Underline shows that it does not meet the claimed range.

CO

TABLE 3
No. Chemical composition(mass% the balance: Fe and impurities)

C Si Mn P S N 0 Al B Ti Nb V Mo Cr Co Ni Cu W Ta Sn Sb As Mg Ca

41 0.33 1.10 2.40 0.0029 0.0119 0.0206 0.0036 0.49 0.0020 - - • - - - - - • -
42 0.34 1.11 3.80 0.0011 0.0034 0.0062 0.0031 M3 0.0001 - - - - - - - - - - - - -
4j 0.30 0.01 3.60 0.0022 0.0033 0.0055 0.0024 0.13 0.0103 - - - - - - - - - - - - -
44 0.25 0.36 3.80 0.0001 0.0062 0.0101 0.0022 0.05 0.0013 0.10 - - - - - - • - - - -
45 0.36 0.50 3.00 0.0012 0.0001 0.0141 0.0020 0.05 0.0015 0.103 - - - - - • - - - -
46 0.28 0.21 2.80 0.0036 0.0018 0.0133 0.0045 0.74 0.0091 - 0.52 - • - - - - - -
a. 0.25 0.44 1.30 0.0032 0.0044 0.0050 0.0204 0.15 0.0048 - - - - - - - - - -
4S 0.30 1.19 1.80 0.0001 0.0015 0.0183 0.0039 0.18 0.0002 - - - SU2 - - - -
42 0.34 0.65 2.20 0.0122 0.0012 0.0094 0.0171 0.03 0.0066 - - 2,04 - - - - -
50 0.29 1.50 1.70 0.0008 0.0055 0.0090 0.0037 0.04 0.0018 - - - 1.20 • - - - - -
£1 0.38 1.59 1.60 0.0001 0.0032 0.0189 0.0021 0.11 0.0019 - - 1M. - • - - - - - -
£2 0.38 0.54 4.70 0.0056 0.0179 0.0028 0.0124 0.10 0.0006 - - - 0.52 • - - - - -
52 0.28 1.87 4.10 0.0144 0.0008 0.0022 0.0035 0.16 0.0024 - - - - - - - 0.102 - 0.032 - - -
54 0.23 1.56 2.90 0.0042 0.0033 0.0136 0.0011 - 0.0006 - • - - - - - - 0.102 - - - - -
a 0.21 1.37 2.70 0.0039 0.0046 0.0147 0.0017 0.12 0.0018 - - - - • - - - - 0.052 - - • -
££ 0.24 0.78 1.40 0.0010 0.0004 0.0099 0.0021 0.38 - - - - - - - - - - 0.052 - - -
5Z 0.28 0.89 3.00 0.0041 0.0158 0.0051 0.0001 0.01 0.0016 - - - • - - - - - 0.051 • -
58 0.34 0.46 2.10 0.0091 0.0021 0.0112 0.0086 0.07 0.0010 - - - - • - - 0.051 -
59 0.21 1.05 3.80 0.0021 0.0103 0.0039 0.0044 0.10 0.0018 - - - - - - - - - - - - 0.052
£Q 0.27 0.44 4.00 0.0122 0.0040 0.0068 0.0009 0.17 - - - - -
SI 0.36 0.99 2.50 0.0026 0.0006 0.0167 0.0028 - 0.0020 - - - - - - - - - - - -
£2 0.36 1.43 3.60 0.0014 0.0024 0.0102 0.0027 0.06 0.0052 - - - - - - - - - - -
63 0.28 0.64 0.60 0.0030 0.0031 0.0105 0.0148 0.04 0.0002 - - • - - - - - - - - -
64 0.25 0.50 2.80 0.0017 0.0064 0.0187 0.0015 0.01 0.0020 0.02 0.021

Underline shows that it does not meet the claimed range.

CO 00

No. Hot Rolling Cold Rolling First Heat Treatment Second Heat Treatment

Heat Temp.
CO Held Time
(sec) First-stage Cooling Colling Rate
CC/s) Stop Temp.
CO Heat Temp.
CC) Held Time
(sec) First-stage Cooling Colling Rate
CC/s) Stop Temp.
CO Holding Temp.
CO Holding Time
(sec)

Heat
Temp.
CC) Finish
Temp.
CC) Coiling
Temp.
TO Rolling
Reduction
(%)

Colling Rate CC/s) Stop
Temp.
CC)



Colling Rate CC/s) Stop
Temp.
CC)

A 1,228 958 213 53 900 375 - 31 230 900 130 - 45 210 100 150
B 1,338 899 543 84 890 225 - 45 187 890 95 - 36 180 250 300
C 1,337 975 331 30 880 90 - 32 233 880 110 - 22 105 105 100
D 1,263 867 116 66 890 314 - 82 99 890 115 - 146 70 70 100
E 1,114 978 120 62 880 403 - 120 158 880 440 32 | 701 99 150 100 130
F 1,242 951 109 37 855 267 - 174 226 860 472 - 38 59 50 50
G 1,165 917 135 41 850 273 - 168 209 851 316 - 38 53 50 30
H 1,129 890 343 88 890 170 - 35 299 875 469 - 131 202 250 40
I 1,293 860 386 58 832 480 - 93 182 880 510 - 59 162 200 100
J 1,256 884 330 69 860 592 - 142 229 870 346 - 67 156 250 400
K 1,261 941 334 63 895 449 - 101 149 900 390 - 72 134 300 150
L 1,301 860 190 80 860 319 - 161 123 871 207 - 141 200 150 300
M 1,319 988 215 43 880 194 - 53 274 875 206 5 | 680 171 200 350 210
N 1,258 934 251 60 885 41 - 112 211 877 14 - 86 159 150 30
0 1,159 888 414 74 839 580 - 168 54 843 269 - 100 118 118 100
P 1,283 973 291 74 880 169 - 145 81 880 123 - ISO 83 80 40
Q 1,174 904 132 43 890 102 - 63 60 870 170 22 | 603 160 259 300 100
R 1,128 950 68 44 890 106 - 194 91 890 248 - 176 256 300 100
S 1,273 975 270 81 879 341 - 40 32 880 340 - 136 216 250 100
T 1,247 922 397 55 888 185 - 86 67 890 221 - 78 208 200 50

TABLE 5

No. Cold Rolling First Heat Treatment Second Heat Treatment

Hot Rolling
Heat Temp.
CO Held Time
(sec) First-stage Cooling Colling Rate
CC/s) Stop Temp.
CC) Heat Temp.
(C) Held Time
(sec) First-stage Cooling Colling Rate
CC/s) Stop Temp.
(C) Holding Temp.
CC) Holding Time
(sec)

Heat
Temp.
CC) Finish
Temp.
CC) Coiling
Temp.
CC) Rolling
Reduction
(%)

Colling Rate CC/s) Stop
Temp.
CO



Colling Rate CC/s) Stop
Temp.
CC)

U 1,217 935 270 49 900 544 - 111 103 900 282 - 101 157 140 100
V 1,125 949 121 37 910 387 - 59 276 920 124 - 60 72 70 100
W 1,269 901 479 80 880 264 - 162 125 880 52 - 162 201 150 50
X 1,211 917 393 65 883 400 - 122 284 884 465 - 185 282 250 40
Y 1,215 974 386 53 890 453 23 691 124 98 881 363 - 161 233 200 30
Z 1,120 880 535 57 876 363 29 619 33 155 854 445 - 69 197 150 40
AA 1,307 894 408 49 900 446 11 644 73 104 900 124 - 119 135 100 30
AB 1,166 956 80 88 886 146 - 106 244 890 221 - 52 99 250 100
AC 1,166 956 80 88 886 146 - 106 244 870 221 - 52 99 250 100
AD 1,177 879 185 51 870 255 30 | 682 181 233 880 409 - 120 123 100 150
AE 1.093 925 380 78 833 29 - 161 122 819 523 - 45 58 50 150
AF 1,271 846 -
AG 1,326 1005 315 32 877 516 - 73 74 820 368 - 84 176 200 150
AH 1,149 976 561 69 838 294 - 99 144 852 483 - 107 230 200 150
AI 1,231 974 80 2§ -
AJ 1,334 867 287 22 -
AK 1,346 985 163 60 798 480 - 27 136 865 255 - 94 200 200 150
AL 1,306 898 328 47 850 0 - 160 222 880 417 - 47 118 200 150
Underline shows that it does not meet the recommeded condition.

TABLE 6
No. Cold Rolling First Heat Treatment Second Heat Treatment

Hot Rolling
Heat Temp.
(t) Held Time
(sec) First-stage Cooling Colling Rate
CC/s) Stop Temp.
CC) Heat Temp.
CC) Held Time
(sec) First-stage Cooling Colling Rate
CC/s) Stop Temp.
(C) Holding Temp.
CC) Holding Time
(sec)

Heat
Temp.
(T) Finish
Temp.
CC) Coiling
Temp.
(t) Rolling
Reduction
(%)

Colling Rate CC/s) Stop
Temp.
(t)



Colling Rate CC/s) Stop
Temp.
(C)

AM 1,262 942 98 41 900 230 0.1 682 139 255 900 127 51 689 144 195 200 150
AN 1,313 963 317 61 850 259 25 600 139 233 850 82 - 34 46 200 150
AO 1,201 949 29 85 882 339 - 14 212 856 112 - 182 170 200 150
AP 1,151 867 245 78 842 496 - 62 400 881 312 - 83 32 200 150
AQ 1,235 944 477 32 821 179 - 53 63 750 417 - 142 145 200 150
AR 1,251 882 384 53 950 362 - 36 53 950 1 - 72 154 200 150
AS 1,245 892 463 71 888 542 - 75 208 842 402 0.01 696 128 95 200 150
AT 1,271 971 153 77 900 507 - 116 187 900 145 5 595 35 268 200 150
AU 1,177 996 291 79 L 863 111 - 168 158 850 585 - 15 74 200 150
AV 1,308 965 322 80 874 83 - 173 134 864 498 - 117 309 200 150
AW 1,284 870 382 85 845 487 - 111 246 853 179 - 157 150 500 150
M 1,247 949 250 64 860 477 - 96 290 856 274 - 138 267 280 600
&Y 1,144 913 134 48 880 143 - 150 68 880 140 - 41 203 200 150
AZ 1,130 961 404 51 - 868 313 - 170 100 200 150
AY 1,228 958 213 53 1150 | 375 | - 1 31 | 230 900 130 - 45 210 100 150
Underline shows that it does not meet the recommeded condition.

[0111] [Table 7]
TABLE 7

Test No. a d
Si z Prodction No. Thickness (mm) Volume Fraction of Microstructure (%) TS (MPa) El (%) Standard
Deviation
of
Macro
hardness Variations
in
Micro
Hardness
(Number) A (%) Crash Resistance Remarks

F P B Retained V M TM




a
(deg) CD TSxEl TSxA Evalu -ation

1 I A 1.4 - - - - - 100 1,889 8.2 23 9 21 52 2 15,492 39,674 O Invention Steel
2 2 B 1.4 - - .- - - 100 1,422 10.4 27 9 40 63 13 14,785 56,867 O Invention Steel
3 3 C 0.8 " - - - - 100 2,061 7 20 6 24 63 8 14,428 49,467 O Invention Steel
4 4 D 1.4 " - - - - 100 1,666 9.3 24 6 23 59 9 15,493 38,315 O Invention Steel
5 5 E 1.4 - - 2 - - 98 1,597 10 28 8 30 63 13 15,972 47,917 o Invention Steel
6 6 F 1.4 - - - - - 100 1,720 9.8 27 8 22 60 10 16,857 37,843 o Invention Steel
7 7 G 1.4 - - - - - 100 2,256 8.6 21 5 19 51 1 19,404 42,870 o Invention Steel
8 8 H 1.4 - - - - - 100 1,428 11.2 23 8 38 66 16 15,996 54,272 o Invention Steel
9 9 I 1.4 - - - - - 100 1,416 10.8 23 8 36 63 13 15,298 50,992 o Invention Steel
10 10 : 1.4 - - - - - 100 1,409 11.6 20 6 39 68 18 16,350 54,968 o Invention Steel
11 11 K 1.4 - - - - - 100 1,504 10.8 21 7 41 63 13 16,241 61,655 o Invention Steel
12 12 L 1.4 - - 3 1 - 96 2,039 9.6 29 8 18 51 1 19,574 36,701 o Invention Steel
13 13 M 1.4 4 1 - - - 95 1,726 10.6 30 7 23 58 8 18,292 39,691 o Invention Steel
14 14 N 1.0 - - - - - 100 2,039 9.2 28 9 17 58 5 18,758 34,662 o Invention Steel
15 15 0 1.4 - - - - - 100 1,934 8.6 25 6 19 53 3 16,634 36,750 o Invention Steel
16 16 P 1.4 - - - - - 100 1,831 9.2 26 7 21 54 4 16,847 38,456 o Invention Steel
17 17 Q 1.4 3 - 2 - - 95 1,718 10.2 30 9 23 59 9 17,525 39,518 o Invention Steel
18 18 R 1.4 - - 4 1 - 95 1,446 9.6 29 8 36 61 11 13,884 52,064 o Invention Steel
19 19 S 1.4 - - - - - 100 1,641 10.2 29 8 24 56 6 16,743 39,395 o Invention Steel
20 20 T 1.4 - - - - - 100 1,538 10.3 29 8 31 59 9 15,840 47,674 o Invention Steel
The each symbol of the Microstructure means as follows:
F:ferrite, P:pearlite, B:bainite, TM:tempered martensite, M:as-quenched martensite
® means the calculated value of "a-(2.37t2-14t+65)", and the value is good if it is 0 or more.
" -" means the microstructure was not observed.
41

[0112] [Table 8]
TABLE 8
Test No. Steel
No. Prodction No. Thickness (mm) Volume Fraction of Microstructure (%) TS (MPa) El
(%) Standard
Deviation
of
Macro
hardness Variations
in
Micro
Hardness
(Number) (%) Crash Resistance Remarks

F P B Retained V M TM




a (deg) © TSxEl TSxA Evalu -ation

21 21 U 1.4 - - - - - 100 1,511 10.6 29 8 33 61 11 16,018 49,866 O Invention Steel
22 22 V 1.4 - - - - - 100 1,417 10.8 24 7 39 65 15 15,305 55,267 O Invention Steel
23 23 w 1.4 - - - - - 100 1,421 10.6 24 7 37 62 12 15,068 52,594 O Invention Steel
24 24 X 1.4 - - - - - 100 1,415 10.2 23 6 35 61 11 14,431 49,519 O Invention Steel
25 25 Y 1.4 - - " - - 100 1,402 10.6 21 6 41 66 16 14,866 57,502 O Invention Steel
26 26 z 1.4 - - - - - 100 1,953 8.6 25 6 17 51 1 16,797 33,203 O Invention Sted
27 27 AA 1.4 - - - - - 100 1,548 10.1 26 7 28 57 7 15,635 43,343 0 Invention Sted
28 28 AB 1.6 - - - - " 100 1,419 11.3 22 6 36 55 6 16,035 51,085 0 Invention Steel
29 29 AC 1.4 - - " - - 100 1,407 11.5 25 8 38 59 9 16,182 53,469 o Invention Steel
30 30 AD 1.4 - - - - - 100 1,543 10.6 20 6 42 64 14 16,358 64,815 0 Invention Steel
31 31 AE 1.4 - - - - - 100 2,231 8.8 38 15 17 40 -10 19,637 37,935 X Conparative Steel
32 32 AF It cannot be tested due to shape defect of hot rolled plate. Conparative Steel
33 33 AG 1.4 - - " - - 100 1,348 9.1 46 18 36 58 8 12.271 48,545 X Conparative Steel
34 1 AH 1.4 - - - - - 100 1,680 9.0 24 12 19 56 6 15,120 31.920 X Conparative Sted
35 2 AI It cannot be tested due to shape defect of cold rolled plate. Conparative Sted
36 3 A2 It cannot be tested due to the steel plate breaks during cold rolling Conparative Sted
37 5 AK 1.4 15 - - - - 85 1,250 13 45 IS 26 73 23 16,250 32.500 X Conparative Sted
38 9 AL 1.4 14 - - - - 86 1,381 14.6 43 17 18 69 19 20,159 24.854 X Conparative Sted
39 11 AM 1.4 25 5 5 - - 65 1,320 16 45 IS 16 69 19 21,120 21.120 X Conparative Sted
40 13 AN 1.4 3 - 2 - " 95 1,410 14 28 8 25 72 22 19,740 35,250 0 Invention Sted
Underline shows it does not meet the claimed range, the recommeded condition, or the target performance.
The each symbol of the Microstructure means as follows:
F:ferrite, Pipearlite, B:bainite, TM:tempered martensite, M:as-quenched martensite
(D means the calculated value of "a-(2.37t2-14t+65)"( and the value is good if it isO or more.
" -" means the microstructure was not observed.
42

[0113] [Table 9]
TABLE 9
Test No. Steel No. Prodction No. Thickness (mm) Volume Fraction of Microstructure (%) TS
(MPa) El
(%) Standard
Deviation
of
Macro
hardness variations
in
Micro
Hardness
(Number) (%) Crash Resistance Remarks

F P B Retained V M TM




a (deg) 00 TSxEl TSx* Evatu -ation

41 IS AO 1.4 - - 30 - - 22 1,380 10.1 32 16 23 48 -Jl 13,938 31.740 X Conparative Steel
42 16 AP 1.4 - - - - - 100 1,659 9 45 16 16 48 -J, 14,928 26.539 X Conparative Sted
43 18 AQ 1.4 80 - - - - 2Q 760 30 50 18 8 82 32 22,800 6.080 X Conparative Sted
44 22 AR 1.4 60 - - - - 40 960 19 35 16 8 75 25 18,240 7.680 X Conparative Sted
45 24 AS 1.4 20 - 12 - - 68 850 15 43 13 34 85 35 12.750 28.900 X Conparative Sted
46 27 AI 1.4 10 10 40 - - 40 1,290 10.2 44 15 6 71 21 13,158 7.740 X Conparative Sted
47 29 AU 1.4 5 - 20 5 10 60 1,290 15 35 15 12 68 18 19,350 15.480 X Conparative Sted
48 30 AV 1.4 - - - - - 100 960 9.4 22 8 42 81 31 9.024 40,320 X Conparative Sted
49 31 AW 1.4 - - - - - 100 1,380 8.4 25 7 33 64 14 11.592 45,540 X Conparative Sted
50 32 AX 1.4 - - - - - 100 1,350 8.8 24 8 50 66 16 11.880 67,500 X Conparative Sted
51 32 AY 1.4 - - - - - 100 1,949 9.5 25 12 16 51 1 18,516 31.184 X Conparative Sted
52 32 AZ 1.4 - - - - - 100 1,820 9.2 29 15 20 45 ^5 16,744 36,400 X Conparative Sted
53 34 A 1.4 - - - - - 100 1,220 8.9 22 5 46 84 34 10.858 56,120 X Conparative Sted
54 35 B 1.4 - - - - - 100 2,200 7.7 32 .12 12 38 -12 16,940 26.400 X Conparative Sted
55 36 C 1.4 - - - - - 100 2,321 9.0 31 11 11 43 J_ 20,885 25.527 X Conparative Sted
56 37 D 1.4 15 10 50 10 5 10 580 21 45 12 56 92 42 12.180 32.480 X Conparative Sted
57 38 E 1.4 - - - - - 100 1,560 9.2 34 11 11 43 -J_ 14,352 17.160 X Conparative Sted
58 39 F 1.4 - - - - - 100 2,244 8.4 31 10 11 44 -A 18,848 24.682 X Conparative Sted
59 40 G 1.4 - - - - - 100 1,965 7.9 33 10 12 51 1 15,520 23.575 X Conparative Sted
60 41 H 1.4 - - - - - 100 1,714 9.3 34 11 11 42 -A 15,937 18.850 X Conparative Sted
Underline shows it does not meet the claimed range, the recommeded condition, or the target perforrr
The each symbol of the Microstructure means as follows:
F:femte, P:pearlite, B:bainite, TM:tempered martensite, M:as-quenched martensite
® means the calculated value of "a-(2.37t2-14t+65)"( and the value is good if it is 0 or more.
" -" means the microstructure was not observed.
43

[0114] [Table 10]
TABLE 10

Test No. Steel No. Prodction No. Thickness (mm) Volume Fraction of Microstructure (%) TS
(MPa) El (%) Standard
Deviation
of
Macro
hardness Variations
in
Micro
Hardness
(Number) (%) Crash Resistance Remarks

F p B Retained V M TM




a (deg) i» TSxEl TSxA Evalu -ation

61 42 J 1.4 - - - - - 100 1,768 9.4 34 13 10 44 -16 16,617 17,677 X Conparative Steel
62 43 K 1.4 - - - - - 100 1,458 8.8 33 11 11 46 -14 12,828 16,035 X Conparative Steel
63 44 L 1.4 - - 4 - - 96 1,590 8.6 36 11 10 44 -16 13,672 15,897 X Conparative Steel
64 45 M 1.4 - - - - - 100 1,599 8.6 3Z 13 9 48 -12 13,751 14,391 X Conparative Steel
65 46 N 1.4 - - - - - 100 1,699 8.4 34 14 9 48 -12 14,275 15,295 X Conparative Steel
66 4Z O 1.4 - - - - - 100 1,649 9.5 34 11 10 51 ;9 15,663 16,488 X Conparative Steel
67 48 P 1.4 - - - - - 100 1,850 9.7 34 11 10 45 -15 17,947 18,502 X Conparative Steel
68 49 Q 1.4 3 - 5 - " 92 1,629 10.2 2Z 14 9 42 -18 16,615 14,661 X Conparative Steel
69 50 R 1.4 2 - 4 - 1 93 1,417 9.8 33 12 12 46 -14 13,883 17,000 X Conparative Steel
70 51 S 1.4 - - - - " 100 2,096 8.9 31 13 13 47 -13 18,652 27,244 X Conparative Steel
71 52 T 1.4 - - - - - 100 2,095 9.6 39 15 9 44 -16 20,109 18,852 X Conparative Steel
72 53 U 1.4 - - - - - 100 1,707 7.4 32 13 15 42 -18 12,634 25,609 X Conparative Steel
73 54 V 1.4 - - - - - 100 1,655 7.8 31 11 16 41 -19 12,910 26,481 X Conparative Steel
74 55 w 1.4 - - - - - 100 1,498 6.9 31 11 17 44 -16 10,337 25,468 X Conparative Steel
75 56 X 1.4 - - - - - 100 1,430 6.4 22 12 19 46 -14 9,152 27,170 X Conparative Steel
76 57 X 1.4 - - - - - 100 1,612 9.1 36 11 13 45 -15 14,669 20,956 X Conparative Steel
77 58 X 1.4 - - - - - 100 1,933 8.7 35 12 12 44 -16 16,817 23,196 X Conparative Steel
78 59 X 1.4 - - - - - 100 1,572 9.1 37 12 10 44 ;16 14,307 15,722 X Conparative Steel
79 60 X 1.4 - - - - - 100 1,464 8.8 40 13 4 48 -12 12,886 5.857 X Conparative Steel
80 61 X 1.4 - - - - " 100 1,859 7.9 40 14 5 49 -11 14,688 9,296 X Conparative Steel
81 62 X 1.4 - - - - - 100 2,100 8.3 31 14 11 43 -17 17,430 23,100 X Conparative Steel
82 63 X 1.4 - - - - " 100 2,100 9.3 32 13 12 42 -18 19,530 25,200 X Conparative Steel
83 64 F 1.4 - - - - - 100 1,720 9.8 25 6 28 60 10 16,857 48,164 o Invention Steel
84 1 AY 1.4 - - - - 2 98 1,889 8.2 34 9 17 52 2 15,492 32,117 X Conparative Steel
Underline shows it does not meet the claimed range, the recommeded condition, or the target performance.
The each symbol of the Microstructure means as follows:
F:ferrite, P:pearlite, B:bainite, TM:tempered martensite, M:as-quenched martensite
® means the calculated value of "a-(2.37t2-14t+65)"( and the value is good if it is 0 or more.
" -" means the microstructure was not observed.
44

[0115] [Table 11]

o o ,_, ,_,
u ID
< CO CO CO CO CD CO CO CO CO CO CO CO CO CO CO rv CO CO
■ ' ■ ' • ■ ■ ■ ■ ■ ■ 0.010 ' ■ ■ ■ ' •


3 ' ' ■ • 1 ■ ■ 1 1 1 1 • 0.00 ■ ■ ■ ' ■

ID
N 1 ■ 1 1 ■ ■ ■ ■ ' ■ 1 1 0.01 ■ • ■ • ■ "


> ' • 1 1 ■ ■ • • • • ' 1 ■ 0.00 ■ ■ ' ■


U ' 1 ■ 1 ■ ■ 1 1 1 • ' ' ' 0.00 ■ 1 •

^j-
1 ' ■ • 1 ■ ■ ' 1 ■ ' 0.00 1 ' ' ■ ' ■

^
< 1 ' ■ • 1 ■ ■ ■ ' 0.02 ' • 1 1 ' 1 ' ■

in
to ' • 1 0.01 ■ ■ 1 • • • • 1 ■ 1 1 ■ ' ■

fM
c 1 ' 1 1 • 0.01 1 1 ' ' ■ ' ' ■ ' ■ ' •

o
i/i 1= ' 1 1 1 ■ ■ ' 1 0.01 ' 1 ' ' ' ' ■ ' , ■

CO
mpuriti g 1 ' ■ ' 1 1 ■ ' 1 ' ' ' 1 1 ' ■ 0.00 ■


: Fe and 3 ■ • ■ • ■ ■ 0.091 ■ • • ' ■ ■ ' • ■ ■ 0.200 ■

rg
a lance 2 ' ' 1 1 ' ' 0.3 1 ' ' 1 1 ' 1 1 0.7 ' 1 '

0
O
LU ? d

£0
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45

TABLE 12
No. Chemical composition(mass% the balance: Fe and impurities)

C Si Mn P S N 0 Al B Tl Nb V Mo Cr Co Ni Cu w Ta Sn Sb As Mg Ca

121 0.19 0.27 1.30 0.0030 0.0068 0.0006 0.0012 - 0.0016 0.01 - - - - - - - - - - - - - -
122 0.18 1.91 1.50 0.0027 0.0016 0.0023 0.0014 0.10 0.0008 - 0.013 - - - - - - - - - - - - -
123 0.21 0.38 0.70 0.0036 0.0164 0.0007 0.0156 0.67 0.0012 - - - - 0.23 - - - - - - - - - -
124 0.18 0.44 0.60 0.0016 0.0115 0.0015 0.0015 0.03 0.0016 0.05 - - - - - 0.32 - - - - - - - -
125 0.19 0.20 1.70 0.0014 0.0171 0.0055 0.0022 0.08 0.0010 - 0.038 0.22 - - - - - - - - - - - -
126 0.34 0.10 1.30 0.0006 0.0015 0.0113 0.0137 0.23 0.0019 - - - - - 0.12 - - - - - - - - -
127 0.20 1.44 2.80 0.0027 0.0180 0.0034 0.0035 0.06 0.0019 - 0.018 - - - - - - - - - - - - -
128 0.21 0.34 4.10 0.0079 0.0029 0.0011 0.0030 0.17 0.0008 0.01 - - 0.15 - - - - - - • - - - -
129 0.19 0.33 4.10 0.0013 0.0044 0.0045 0.0028 0.15 0.0007 - 0.043 - - - - - - 0.020 - - - - - -
130 0.20 0.82 1.60 0.0040 0.0012 0.0035 0.0015 0.74 0.0068 - 0.015 0.05 - - - - - - - - 0.020 - - -
131 0.38 0.47 1.40 0.0052 0.0004 0.0033 0.0181 - 0.0030 0.01 - - - - - - - - - - - - - -
132 0.28 0.65 3.70 0.0034 0.0028 0.0141 0.0040 0.06 0.0091 - - - - - - - - - - - - - - -
133 0.35 0.53 3.20 0.0024 0.0103 0.0033 0.0035 0.08 0.0016 - - 0.41 - - - - - - - - - - - -
134 0.28 1.87 4.70 0.0005 0.0031 0.0027 0.0004 0.86 0.0036 - 0.016 - - - - - - - - • - - - -
135 0.18 0.20 3.60 0.0031 0.0130 0.0027 0.0121 0.85 0.0011 - - 0.14 - - - - - - - - - - - -
136 0.23 0.80 2.10 0.0032 0.0036 0.0039 0.0087 0.06 - - - - - - - - - - - - - - - -
137 0.22 1.00 2.30 0.0033 0.0035 0.0084 0.0071 0.05 - - - - - - - • - - - - - - - -
138 0.24 1.20 2.20 0.0029 0.0033 0.0057 0.0010 0.03 - - - - - - - - - - - - - - - -
139 0.20 0.90 2.80 0.0027 0.0022 0.0027 0.0023 0.08 - - - - - - - - - - - - - - - -
140 0.21 1.20 3.10 0.0033 0.0025 0.0021 0.0044 0.03 - - - - - - - - - - - - - - -

TABLE 13
No. Chemical composition(mass% the balance; Fe and impurities)

C Si Mn P S N 0 Al B Ti Nb V Mo Cr Co Ni Cu w Ta Sn Sb As Mg Ca

141 0.19 1.50 1.90 0.0039 0.0035 0.0088 0.0068 0.04 - - - - - - - - - - - - - - - -
142 0.24 0.80 2.00 0.0032 0.0038 0.0056 0.0045 0.02 - - - - - - - - - - - - - - - -
143 0.22 0.50 2.20 0.0039 0.0037 0.0078 0.0090 0.03 - - - - - - - - - - - - - - - -
144 0.23 0.60 2.50 0.0033 0.0021 0.0072 0.0042 0.07 - - - - - - - - - - - - - - - -
145 0.19 0.30 2.80 0.0028 0.0039 0.0059 0.0056 0.06 - - - - - - - - - - - - - - - -
146 0.24 0.40 1.70 0.0034 0.0039 0.0071 0.0061 0.06 - - - - - - - - - - - - - - - -
147 0.22 0.20 1.60 0.0019 0.0038 0.0046 0.0061 0.03 - - - - - - - - - - - - - - - -
148 0.23 0.90 1.90 0.0027 0.0030 0.0027 0.0047 0.04 - - - - - - - - - - - - - - - -
149 0.23 1.40 1.50 0.0020 0.0027 0.0029 0.0012 0.08 - - - - - - - - - - - - - - - -
150 0.24 1.60 2.20 0.0023 0.0020 0.0083 0.0087 0.01 - - - - - - - - - - - - - - - -
151 0.25 0.80 2.10 0.0026 0.0023 0.0033 0.0062 - - - - - - -. - - - - - - - - - -
152 0.26 0.90 1.90 0.0025 0.0024 0.0012 0.0057 0.08 - - - - - - - - - - - - - - - -
153 0.15 0.50 2.40 0.0011 0.0024 0.0014 0.0011 0.14 0.0079 - - - - - - - - - - - - - - -
154 0.50 0.50 2.80 0.0021 0.0007 0.0072 0.0028 0.10 0.0002 - - - - - - - - - - - - - - -
155 0.22 3.50 2.60 0.0155 0.0003 0.0173 0.0013 0.12 0.0011 - - - - - - - - - - - - - - -
156 0.22 0.50 0.25 0.0024 0.0162 0.0012 0.0047 - 0.0014 - - - - - - - - - - - - - - -
152 0.22 0.50 6,50 0.0013 0.0176 0.0049 0.0025 0.67 0.0079 - - - - - - - - - - - - - - -
Underline shows that it does not meet the claimed range.

TABLE 14
No. Cold Rolling First Heat Treatment Second Heat Treatment

Hot Rolling
Oxygen Partial Pressure
(xl0'21atm) Heat Temp.
CO Held Time
(sec) First-stage Cooling Colling Rate
CC/s) Stop Temp.
CC) Oxygen Partial Pressure
(xl021atm) Heat Temp.
CC) Held Time
(sec) First-stage Cooling Colling Rate
CC/s) Stop Temp.
CC) Holding Temp.
CC) Hold Tim
(se

Heat
Temp.
CO Rnish
Temp.
(t) Coiling
Temp.
CO Rolling
Reduction
(%)


Colling Rate CC/s) Stop
Temp.
CC)




Colling Rate CC/s) Stop
Temp.
CC)

a 1230 860 340 61 631 870 250 - - 90 160 399 860 300 - 40 160 310 30
b 1140 960 370 37 41,072 970 430 - - 130 98 5,555 920 30 8.5 660 20 180 300 20
c 1240 890 130 33 156 880 60 - - 130 105 2,379 900 310 - - 90 160 30 27
d 1230 880 460 66 8,399 930 260 - - 90 82 1,540 890 30 - - 80 150 110 70
e 1280 850 410 82 5,555 920 50 - - 120 116 8,399 930 220 - - 40 120 310 41
f 1140 890 360 34 21 850 310 - - 40 253 8,399 930 130 - - 60 130 170 70
g 1300 870 230 66 0.01 870 170 - - 130 126 27,888 960 100 - - 130 210 370 20
h 1210 850 310 31 250 870 50 - - 60 97 989 880 160 - - 70 100 240 39
i 1300 960 520 90 18,816 950 400 - - 100 207 8,399 930 40 - - 110 50 340 46
j 1160 880 410 60 8,399 930 170 - - 140 230 1,540 890 290 - - 110 so 380 35
k 1270 850 340 63 5,555 920 30 - - 100 83 8,399 930 10 - - 50 100 50 38
1 1260 940 490 62 96 850 290 - - 140 153 399 860 160 - - 60 40 160 47
m 1170 1000 230 87 5,555 920 440 - - 30 54 250 850 20 - - 110 70 440 50
n 1220 980 250 56 3,648 910 20 - - 140 101 1,540 890 20 - - 130 210 270 17
0 1230 860 280 69 5,555 920 410 - - 40 158 989 880 350 - - 80 80 190 29
P 1190 880 380 42 5,555 920 380 - - 110 183 399 860 100 5.2 680 50 50 130 48
q 1190 910 170 82 59 900 70 5 680 120 244 5,555 920 90 - - 60 90 280 14
r 1190 910 170 82 59 830 70 1 720 30 253 989 880 280 - 110 80 250 10
s 1130 960 500 75 21 890 170 - - 130 258 1,540 890 100 - - 90 no 110 10
t 1140 930 360 57 3,648 910 90 - 130 114 1,540 890 280 - 60 160 190 30

TABLE 15
No. Cold Rolling Rrst Heat Treatment Second Heat Treatment

Hot Rolling
Oxygen Partial Pressure
(xl0'21atm) Heat Temp.
CO Held Time
(sec) First-stage Cooling Colling Rate
(t/s) Stop Temp.
co Oxygen Partial Pressure
(xl0'21atm) Heat Temp.
eo Held Time
(sec) First-stage Cooling Colling Rate
(t/s) Stop Temp.
(t) Holding Temp.
m Hold Tim
(sec

Heat
Temp.
CO Finish
Temp.
(T) Coiling Temp.
co Rolling
Reduction
(%)


Colling Rate CC/s) Stop
Temp.
(t)




Colling Rate (t/s) Stop Temp.

u 1260 990 260 79 989 880 400 - - 130 273 41,072 970 130 - - 110 190 340 33
V 1110 860 400 83 21 920 380 - - 120 134 3,648 910 350 - - 50 250 260 23
w 1150 990 290 53 21 840 140 - - 80 271 1,540 890 270 - - 120 180 340 90
X 1300 930 410 38 18,816 950 420 - - 100 174 0.01 860 260 - - 100 130 320 15
y 1300 870 500 83 989 880 150 - - 60 209 3,648 910 140 - - 100 140 400 17
z 1190 930 370 45 21 800 100 - - 20 127 250 850 160 - - 100 190 100 20
aa 1300 910 530 81 12,613 940 470 - - 60 216 2,949 905 20 - 80 120 430 200
ab 1210 870 120 60 59 840 260 - 100 233 631 870 120 - - 110 30 440 44
ac 1160 960 220 81 21 840 260 - - 120 121 989 880 210 - - 80 70 320 45
ad 1140 940 490 80 41,072 970 30 - - 120 143 8,399 930 330 - - 70 170 270 60
ae 1000 980 140 70 631 870 320 - - 50 109 41,072 970 60 - - 130 160 40 20
af 1220 800 420 85 3,648 910 90 - - 60 68 60,117 980 110 - - 30 100 340 26
as 1220 920 600 55 250 860 IS - - 150 255 989 880 290 - - 80 110 280 38
ah 1180 970 470 15 41,072 970 1Q - 90 168 18,816 950 140 - - 110 90 120 90
al 1120 900 510 98 21 850 450 - - 80 238 41,072 970 190 - - 120 100 330 50
aj 1130 990 160 72 0.01 860 290 - - 40 57 0.01 870 30 - 70 170 200 70
ak 1270 910 530 31 279 750 120 - - 40 222 2,379 900 150 - - 70 200 170 48
al 1200 900 210 80 250 870 fi - - 30 118 989 880 20 - - 80 170 80 22
am 1190 940 330 57 3,648 910 480 0.01 650 50 243 2,379 900 180 - - 50 60 380 10
an 1150 970 110 52 3,648 910 290 1 600 90 180 60,117 980 250 - - 100 90 400 15
Underline shows that it does not meet the recommeded condition.

[0120] [Table 16]
50

TABLE 17
Substrate layer Soft Layer
Test No. Steel No. Prodction No. Thickness t (mm) Soft Layer Volume Fraction of Microstructure (%) TS (MPa) El (%) Macro Hardness Variations
in
Micro
Hardness
(Number) Hardness Hv,„« /
Hv„,« (%) Crash

8 -P yt F P B Retained V M TM

III Standard Deviation
Average Value Standard Deviation

a (deg) a> T

101 101 a 1.4 60 8.6 " - 4 1 - 95 1432 9.8 450 26 8 356 28 0.79 36 96 31 14
102 102 b 1.4 150 10.7 4 - 1 - - 95 1169 11.3 385 25 7 274 28 0.71 45 98 33 13
103 103 c 1.4 79 5.6 - - 2 - - 98 1517 9.6 477 22 8 392 25 0.82 37 90 25 14
104 104 d 1.4 137 9.8 - - 4 - - 96 1575 9.2 499 23 9 391 27 0.78 34 85 20 14
105 105 e 1.4 121 8.6 - - - - - 100 1286 10.2 405 21 8 259 24 0.64 44 96 31 13
106 106 f 1.4 94 6.7 - - - - - 100 1534 8.9 487 25 8 327 24 0.67 31 89 24 13
107 107 g 1.4 147 10.5 - - 2 - - 98 1256 10.4 401 23 7 199 26 0.50 39 114 49 13
108 108 h 1.4 41 3.0 - - 4 - - 96 1439 9.1 445 26 6 359 29 0.81 39 96 31 13
109 109 i 1.4 182 13.0 - - 3 2 - 95 1198 10.9 392 28 5 239 28 0.61 46 120 55 13
110 110 J 1.4 151 10.8 - - 1 - - 99 1102 12.6 338 27 7 257 30 0.76 43 131 66 13
111 111 k 1.0 100 10.0 - - 3 2 - 95 1671 9.4 527 26 8 358 29 0.68 28 78 10 15
112 112 1 1.4 34 2.4 - - 4 - - 96 1881 8.2 590 24 9 428 26 0.73 25 70 5 15
113 113 m 1.4 132 9.4 - - 4 1 - 95 1185 12.3 376 26 9 282 29 0.75 37 113 48 14
114 114 n 1.4 36 2.6 - - 3 - 1 96 1456 9.5 457 28 8 327 28 0.72 23 95 30 13
115 115 0 1.4 170 12.2 - - 3 - - 97 1709 8.2 548 23 8 381 26 0.70 25 76 11 13
116 116 P 1.4 134 9.6 3 1 - - - 96 1639 9.6 517 23 6 438 26 0.85 28 81 16 15
117 117 q 1.4 64 4.6 - - - - - 100 1294 10.3 408 21 9 285 24 0.70 42 110 45 13
118 118 r 1.4 48 3.4 - - - - - 100 1402 9.5 440 20 8 354 23 0.80 39 100 35 13
119 119 s 1.2 37 3.1 - - - - - 100 1515 8.6 475 21 7 391 22 0.82 37 90 23 13
120 120 t 1.4 100 7.2 - - 1 - - 99 1561 8.8 494 23 7 365 26 0.74 29 86 21 13
Underline shows it does not meet the claimed range, the recommeded condition, or the target performance.
The each symbol of the Microstructure means as follows:
F:ferrite, P:pearlite, B:bainite, TM:tempered martensite, M:as-quenched martensite ©means the calculated value of "a-(2.37t2-14t+65)M, and the value is good if it is 0 or more. " -" means the microstructure was not observed.

cn to

TABLE 18
Substrate layer Soft Layer
Test No. c o
■a ■ u o
sz
o- 1? Soft Layer Volume Fraction of Mfcrostructure (%) TS (MPa) El (%) Macro Hardness Variations
in
Micro
Hardness
(Number) Hardness Hv„„ / (%) Crash

1? f3 yt F P B Retained V M TM

Average Value HVo,,, Standard Deviation
Average Value Hv,,., Standard Deviation

a (deg) ® T

121 121 U 1.4 122 8.7 - - 2 - - 98 1136 11.6 364 23 9 216 26 0.59 34 127 62 13
122 122 V 1.4 101 7.2 - - 2 2 1 95 1304 10.8 413 26 8 307 29 0.74 26 109 44 14
123 123 W 1.4 57 4.1 - - 2 2 1 95 1239 10.5 388 27 7 285 27 0.73 36 115 50 13
124 124 X 1.4 122 8.7 - - 3 - - 97 1137 11.6 373 23 7 207 26 0.56 42 127 62 13
125 125 y 1.4 90 6.5 - - - - - 100 • 1165 12.6 333 21 8 215 24 0.65 40 123 58 14
126 126 z 1.4 80 5.7 " - 3 - 2 95 1891 8.1 592 28 8 467 26 0.79 20 76 11 15
127 127 aa 1.4 177 12.6 - - 3 2 - 95 1132 11.6 309 27 7 197 30 0.64 39 127 62 13
128 128 ab 1.4 32 2.3 - - 4 - - 96 1145 12.3 317 26 9 242 29 0.76 31 126 61 14
129 129 ac 1.4 43 3.1 - - 3 2 - 95 1236 11.7 388 26 8 314 24 0.81 34 116 51 14
130 130 ad 1.4 102 7.3 - - 3 1 - 96 1265 11.6 409 25 8 282 28 0.69 37 113 48 14
131 131 2£ 1.4 171 12.2 - - 4 - - 96 1999 8.2 650 24 IS 336 25 0.52 16 68 3 16
132 132 af It cannot be tested due to shape defect of hot rolled plate.
133 133 ag 1.4 48 3.4 - - 5 - - 95 1720 8.3 542 25 16 338 28 0.62 18 75 10 14
134 134 ah It cannot be tested due to shape defect of cold rolled plate.
135 135 ai It cannot be tested due to exvessive cold rolling load.
136 136 aj 1.4 70 5.0 - - - - - 100 1498 9.2 465 22 8 421 28 0.91 28 62 r3 13
137 137 ak 1.4 64 4.6 - - 5 - - 95 1492 9.1 470 24 12 359 24 0.76 20 92 27 13
138 138 ai 1.4 21 1.5 - - 3 1 1 95 1614 8.8 505 25 11 414 24 0.82 20 82 17 14
139 139 am 1.4 161 11.5 - - - - - 100 1090 12.6 349 22 13 243 22 0.70 30 132 67 13
140 140 an 1.4 220 15,7 - - - - - 100 942 15.1 325 21 11 169 27 0.52 45 63 -Jl 14
Underline shows it does not meet the claimed range, the recommeded condition, or the target performance.
The each symbol of the Microstructure means as follows:
F:ferrite, Pipearlite, Bibainite, TM:tempered martensite, M:as-quenched martensite
® means the calculated value of "a-(2.37t2-14t+65)", and the value is good if it is 0 or more.
" -" means the microstructure was not observed.

cn
CO

TABLE 19
Substrate layer Soft Layer
Test No. Steel No. Prodction No. Thickness t (mm) Soft Layer Volume Fraction of Mkrostructure {%) TS (MPa) El (%) Macro Hardness Variations
in
Micro
Hardness
(Number) Hardness Hv„„
1 HvM™ A
(%) Crash

Thickness tj(mm) Wt F P B Retained Y M TM

Average Value
Hv„v= Standard Deviation
Average Value Hv„v, Standard Deviation

a (deg) ® T

141 141 ao 1.4 303 21.6 - - 2 - - 98 1350 9.7 439 24 12 320 29 0.73 23 105 40 13
142 142 ae 1.4 123 8.8 - - - - - 100 1293 10.6 412 23 13 272 25 0.66 25 110 45 13
143 143 aq 1.4 8 0.6 - - 3 1 - 96 1504 8.8 470 22 7 278 28 0.59 29 64 ^1 13
144 144 SI 1.4 101 7.2 90 10 - - - 0 430 55.0 395 45 20 194 36 0.49 56 239 174 23
145 145 aj 1.4 50 3.6 - - 4 - - 96 1513 9.9 473 24 22 446 28 0.94 19 56 ^2 14
146 146 at 1.4 80 5.7 34 - - - - 66 1057 25.7 493 40 21 472 29 0.96 23 62 z3 27
147 147 an 1.4 90 6.4 39 - - - - 61 1021 28.3 458 39 IS 430 28 0.94 26 63 £ 28
148 148 ay 1.4 80 5.7 10 - 40 3 - 47 960 17.1 480 38 8 354 26 0.74 34 148 83 16
149 149 aw 1.4 100 7.1 - - 60 5 - 35 1122 14.1 352 32 9 207 29 0.59 22 128 63 15
150 150 ax 1.4 82 5.9 - - - - - 100 990 10.6 282 18 16 95 30 0.34 32 144 79 10
151 151 ay 1.4 150 10.7 - - - - - 100 1530 8.9 372 22 8 274 27 0.74 46 89 24 13
152 152 az 1.4 55 3.9 - - - - - 100 1610 8.4 521 23 9 392 29 0.75 44 83 18 13
153 152 ba 1.4 60 4.3 - - - - - 100 1666 8.0 522 28 16 392 27 0.75 19 79 14 13
154 153 bb 1.4 140 10.0 - - - - - 100 1468 8.0 958 26 8 334 25 0.35 24 94 29 11
155 154 be 1.4 154 11.0 - - 3 2 - 95 2920 9.4 958 25 9 334 24 0.35 8 35 -30 27
156 155 bd 1.4 60 4.3 - - 2 - - 98 1591 8.1 498 23 9 458 26 0.92 18 53 J2 12
157 156 be 1.4 60 4.3 - - - - - 100 1591 8.0 498 22 8 458 27 0.92 19 54 -11 12
158 157 bf 1.4 60 4.3 - - - - - 100 1591 8.0 498 22 9 458 29 0,92 18 53 J2 12
Underline shows it does not meet the claimed range, the recommeded condition, or the target performance.
The each symbol of the Microstructure means as follows:
F:ferrite, P:pearlite, Bibainite, TM:tempered martensite, M:as-quenched martensite
® means the calculated value of "a-(2.37t2-14t+65)", and the value is good if it is 0 or more.
" -" means the microstructure was not observed.

[0124]
As shown in Tables 7 to 10, steel sheets according to Test Nos. 1 to 30, which satisfied the definition according to the present invention, had high strength and excellent crash resistance. In contrast, steel sheets according to Test Nos. 31 to 82, which did not satisfy any one or more of the macro hardness, the micro hardness, and the tensile strength according to the present invention, were poor in crash resistance. [0125]
As shown in Tables 17 to 20, steel sheets according to Test Nos. 101 to 130, 151, and 152, which satisfied the definition according to the present invention, had high strength and excellent crash resistance. In contrast, steel sheets according to Test Nos. 131 to 150 and 153 to 158, which did not satisfy any one or more of the steel micro-structure, the chemical composition, the macro hardness, and the micro hardness of a substrate layer and the thickness and the tensile strength, and the hardness of a soft layer according to the present invention, were poor at least in crash resistance.
INDUSTRIAL APPLICABILITY [0126]
According to the present invention, a steel sheet that establishes compatibility between high strength (specifically a tensile strength of 1100 MPa or more) and excellent crash resistance is obtained.
REFERENCE SIGNS LIST [0127]
10 steel sheet
10a surface of steel sheet
t sheet thickness
A region for measurement of macro hardness
B region for measurement of micro hardness

WE CLAIMS

A steel sheet having a tensile strength of 1100 MPa or more, wherein the steel sheet has a micro-structure containing, in volume fraction, tempered martensite: 95% or more, and one or more kinds of ferrite, pearlite, bainite, as-quenched martensite, and retained austenite: less than 5% in total,
wherein in a cross section parallel to a sheet-thickness direction of the steel sheet, when a sheet thickness is denoted by t,
in a 300-um-square region centered about a t/2 point, a standard deviation of Vickers hardnesses that are measured under a load of 9.8 N at 30 points is 30 or less,
wherein when a 100-(j,m-square region centered about a t/2 point is divided into 10x10, 100 subregions, and at a center of each of the subregions, a nano hardness is measured under a maximum load of 1 mN, out of the subregions, the number of subregions each of which makes a difference in nano hardness of 3 GPa or more from any one of eight surrounding subregions is 10 or less, and
wherein the steel sheet has a chemical composition comprising, in mass%: C: 0.18% or more to 0.40% or less, Si: 0.01% or more to 2.50% or less, Mn: 0.60% or more to 5.00% or less, P: 0.0200% or less, S: 0.0200% or less, N: 0.0200% or less, O: 0.0200% or less, Al: 0% or more to 1.00% or less, Cr: 0% or more to 2.00% or less, Mo: 0% or more to 0.50% or less, Ti: 0% or more to 0.10% or less, Nb: 0% or more to 0.100% or less, B: 0% or more to 0.0100% or less, V: 0% or more to 0.50% or less, Cu: 0% or more to 0.500% or less,
55

W: 0% or more to 0.100% or less, Ta: 0% or more to 0.100% or less, Ni: 0% or more to 1.00% or less, Co: 0% or more to 1.00% or less, Sn: 0% or more to 0.050% or less, Sb: 0% or more to 0.050% or less, As: 0% or more to 0.050% or less, Mg: 0% or more to 0.050% or less, Ca: 0% or more to 0.050% or less, Y: 0% or more to 0.050% or less, Zr: 0% or more to 0.050%) or less, La: 0% or more to 0.050% or less, Ce: 0% or more to 0.050% or less, and the balance: Fe and impurities.
2. A steel sheet that includes a substrate layer including the steel sheet
according to claim 1 and a soft layer formed on at least one of surfaces of the substrate
layer,
wherein a thickness of the soft layer is more than 10 um to 0.15t or less per side,
wherein at a 10-u.m point from a surface of the soft layer, a standard deviation of Vickers hardnesses that are measured under a load of 4.9 N at 150 points is 30 or less, and
wherein an average Vickers hardness Hvi of the soft layer is 0.9 times or less an average Vickers hardness Hvo at a t/2 point.
3. The steel sheet according to claim 1 or 2 may include a galvanized layer, a
galvannealed layer, or an electrogalvanized layer on its surface.