Hot-stamped steel, cold-rolled steel sheet and method for producing hot-stamped steel
10544475 ยท 2020-01-28
Assignee
Inventors
- Yoshihiro Suwa (Amagasaki, JP)
- Toshiki Nonaka (Tokai, JP)
- Koichi Sato (Tokai, JP)
- Manabu Naruse (Tokoname, JP)
- Yasunori Iwasa (Spanish Fort, AL, US)
- Yoshifumi Kobayashi (Obu, JP)
Cpc classification
C22C38/005
CHEMISTRY; METALLURGY
C23C2/02
CHEMISTRY; METALLURGY
C22C38/002
CHEMISTRY; METALLURGY
C22C38/12
CHEMISTRY; METALLURGY
C23C2/28
CHEMISTRY; METALLURGY
International classification
C22C38/12
CHEMISTRY; METALLURGY
C23C2/28
CHEMISTRY; METALLURGY
Abstract
A hot-stamped steel according to the present invention has a predetermined chemical composition, satisfies (5[Si]+[Mn])/[C]>10 when [C] is the amount of C by mass %, [Si] is the amount of Si by mass %, and [Mn] is the amount of Mn by mass %, includes 40% to 95% ferrite and 5% to 60% martensite in area fraction, and optionally further includes 10% or less pearlite in area fraction, 5% or less retained austenite in volume fraction, and less than 40% bainite in area fraction. The total of the area fraction of ferrite and the area fraction of martensite is 60% or more, the hardness of martensite measured with a nanoindenter satisfies H2/H1<1.10 and HM<20, and TS which is product of tensile strength TS and hole expansion ratio is 50000 MPa.Math.% or more.
Claims
1. A hot-stamped steel comprising, by mass %: C: 0.030% to 0.150%; Si: 0.010% to 1.000%; Mn: 0.50% or more and less than 1.50%; P: 0.001% to 0.060%; S: 0.001% to 0.010%; N: 0.0005% to 0.0100%; Al: 0.010% to 0.050%, and optionally at least one of B: 0.0005% to 0.0020%; Mo: 0.01% to 0.50%; Cr: 0.01% to 0.50%; V: 0.001% to 0.100%; Ti: 0.001% to 0.100%; Nb: 0.001% to 0.050%; Ni: 0.01% to 1.00%; Cu: 0.01% to 1.00%; Ca: 0.0005% to 0.0050%; REM: 0.0005% to 0.0050%, and a balance of Fe and impurities, wherein when [C] is an amount of C by mass %, [Si] is an amount of Si by mass %, and [Mn] is an amount of Mn by mass %, a following expression (A) is satisfied, the structure of the hot-stamped steel sheet consists of a ferrite, a martensite, and optionally one or more of a pearlite, a retained austenite, and a bainite, an area fraction of the ferrite is 40% to 95% and an area fraction of the martensite is 5% to 60%, a total of the area fraction of the ferrite and the area fraction of the martensite is 60% or more, an area fraction of the pearlite is 10% or less, a volume fraction of the retained austenite is 5% or less, and an area fraction of the bainite is less than 40%, a hardness of the martensite measured with a nanoindenter satisfies a following expression (B) and a following expression (C), TS which is a product of a tensile strength TS and a hole expansion ratio is 50000 MPa.Math.% or more,
(5[Si]+[Mn])/[C]>10(A),
H2/H1<1.10(B),
HM<20(C), and the H1 is an average hardness of the martensite in a surface portion of a sheet thickness of the hot-stamped steel, the surface portion is an area having a width of 200 m in a thickness direction from an outermost layer, the H2 is an average hardness of the martensite in a central portion of the sheet thickness of the hot-stamped steel, the central portion is an area having a width of 200 m in the thickness direction at a center of the sheet thickness, and the HM is a variance of the average hardness of the martensite in the central portion of the sheet thickness of the hot-stamped steel.
2. The hot-stamped steel according to claim 1, wherein an area fraction of MnS existing in the hot-stamped steel and having an equivalent circle diameter of 0.1 m to 10 m is 0.01% or less, a following expression (D) is satisfied,
n2/n1 <1.5(D), and the n1 is an average number density per 10000 m.sup.2 of the MnS having an equivalent circle diameter of 0.1 m to 10 m in a portion of the sheet thickness of the hot-stamped steel, and the n2 is an average number density per 10000 m.sup.2 of the MnS having an equivalent circle diameter of 0.1 m to 10 m in the central portion of the sheet thickness of the hot-stamped steel.
3. The hot-stamped steel according to claim 1, wherein a hot-dip galvanized layer is formed on a surface thereof.
4. The hot-stamped steel according to claim 3, wherein the hot-dip galvanized layer is alloyed.
5. The hot-stamped steel according to claim 1, wherein an electrogalvanized layer is formed on a surface thereof.
6. The hot-stamped steel according to claim 1, wherein an aluminized layer is formed on a surface thereof.
Description
BRIEF DESCRIPTION OF THE DRAWINGS
(1)
(2)
(3)
(4)
(5)
(6)
(7)
(8)
(9)
(10)
EMBODIMENTS OF THE INVENTION
(11) As described above, it is important to establish an appropriate relationship among the amount of Si, the amount of Mn and the amount of C and provide an appropriate hardness to martensite in a predetermined position in a hot-stamped steel (or a cold-rolled steel sheet) in order to improve hole expansibility of the hot-stamped steel. Thus far, there have been no studies regarding the relationship between the hole expansibility or the hardness of the martensite in a hot-stamped steel.
(12) Herein, reasons for limiting a chemical composition of a hot-stamped steel according to an embodiment of the present invention (in some cases, also referred to as a hot-stamped steel according to the present embodiment) and steel used for manufacture thereof will be described. Hereinafter, % that is the units of the amount of an individual component indicates mass %.
(13) C: 0.030% to 0.150%
(14) C is an important element to strengthen the martensite and increase the strength of the steel. When the amount of C is less than 0.030%, it is not possible to sufficiently increase the strength of the steel. On the other hand, when the amount of C exceeds 0.150%, degradation of the ductility (elongation) of the steel becomes significant. Therefore, the range of the amount of C is set to 0.030% to 0.150%. In a case in which there is a demand for high hole expansibility, the amount of C is desirably set to 0.100% or less.
(15) Si: 0.010% to 1.000%
(16) Si is an important element for suppressing a formation of harmful carbide and obtaining a multi-phase structure mainly including a ferrite structure and a balance of the martensite. However, in a case in which the amount of Si exceeds 1.000%, the elongation or hole expansibility of the steel degrades, and a chemical conversion treatment property or plating adhesion after hot stamping also degrades. Therefore, the amount of Si is set to 1.000% or less. In addition, while Si is added for deoxidation, a deoxidation effect is not sufficient when the amount of Si is less than 0.010%. Therefore, the amount of Si is set to 0.010% or more.
(17) Al: 0.010% to 0.050%
(18) Al is an important element as a deoxidizing agent. To obtain the deoxidation effect, the amount of Al is set to 0.010% or more. On the other hand, even when Al is excessively added, the above-described effect is saturated, and conversely, the steel becomes brittle. Therefore, the amount of Al is set to be in a range of 0.010% to 0.050%.
(19) Mn: 0.50% or more and less than 1.50%
(20) Mn is an important element for increasing a hardenability of the steel and strengthening the steel. However, when the amount of Mn is less than 0.50%, it is not possible to sufficiently increase the strength of the steel. On the other hand, Mn is selectively oxidized on a surface in a similar manner with Si, and thereby chemical conversion treatment property or plating adhesion after hot stamping degrades. As a result of studies by the inventors, it was found that when the amount of Mn is 1.50% or more, plating adhesion degrades. Therefore, in the embodiment, the amount of Mn is set to less than 1.5%. It is more preferable that the upper limit of the amount of Mn be 1.45%. Therefore, the amount of Mn is set to be in a range of 0.50% to less than 1.50%. In a case in which there is a demand for high elongation, the amount of Mn is desirably set to 1.00% or less.
(21) P: 0.001% to 0.060%
(22) In a case in which the amount is large, P segregates at a grain boundary, and deteriorates the local ductility and weldability of the steel. Therefore, the amount of P is set to 0.060% or less. On the other hand, since an unnecessary decrease of P leads to an increase in the cost of refining, the amount of P is desirably set to 0.001% or more.
(23) S: 0.001% to 0.010%
(24) S is an element that forms MnS and significantly deteriorates the local ductility or weldability of the steel. Therefore, the upper limit of the amount of S is set to 0.010%. In addition, in order to reduce refining costs, the lower limit of the amount of S is desirably set to 0.001%.
(25) N: 0.0005% to 0.0100%
(26) N is an important element to precipitate AlN and the like and to refine crystal grains. However, when the amount of N exceeds 0.0100%, a solute N (a solute nitrogen) remains and the ductility of the steel is degraded. Therefore, the amount of N is set to 0.0100% or less. Due to a problem of refining costs, the lower limit of the amount of N is desirably set to 0.0005%.
(27) The hot-stamped steel according to the embodiment has a basic composition including the above-described elements, Fe and unavoidable impurities as a balance, but may further contain any one or more elements selected from Nb, Ti, V, Mo, Cr, Ca, REM (rare earth metal), Cu, Ni and B as elements that have thus far been used in amounts that are within the below-described ranges to improve the strength, to control a shape of a sulfide or an oxide, and the like. Even when the hot-stamped steel or cold-rolled steel sheet does not include Nb, Ti, V, Mo, Cr, Ca, REM, Cu, Ni, and B, various properties of the hot-stamped steel or cold-rolled steel sheet can be improved sufficiently. Therefore, the lower limits of the amounts of Nb, Ti, V, Mo, Cr, Ca, REM, Cu, Ni, and B are 0%.
(28) Nb, Ti and V are elements that precipitate fine carbonitride and strengthen the steel. In addition, Mo and Cr are elements that increase hardenability and strengthen the steel. To obtain these effects, the steel desirably contains Nb: 0.001% or more, Ti: 0.001% or more, V: 0.001% or more, Mo: 0.01% or more, and Cr: 0.01% or more. However, even when Nb: more than 0.050%, Ti: more than 0.100%, V: more than 0.100%, Mo: more than 0.50%, or Cr: more than 0.50% are contained, the strength-increasing effect is saturated, and there is a concern that the degradation of the elongation or the hole expansibility may be caused.
(29) The steel may further contain Ca in a range of 0.0005% to 0.0050%. Ca and rare earth metal (REM) control the shape of sulfides or oxides and improve the local ductility or the hole expansibility. To obtain this effect using the Ca, it is preferable to add 0.0005% or more Ca. However, since there is a concern that an excessive addition may deteriorate workability, the upper limit of the amount of Ca is set to 0.0050%. For the same reason, for the rare earth metal (REM) as well, it is preferable to set the lower limit of the amount to 0.0005% and the upper limit of the amount to 0.0050%.
(30) The steel may further contain Cu: 0.01% to 1.00%, Ni: 0.01% to 1.00% and B: 0.0005% to 0.0020%. These elements also can improve the hardenability and increase the strength of the steel. However, to obtain the effect, it is preferable to contain Cu: 0.01% or more, Ni: 0.01% or more and B: 0.0005% or more. In a case in which the amounts are equal to or less than the above-described values, the effect that strengthens the steel is small. On the other hand, even when Cu: more than 1.00%, Ni: more than 1.00% and B: more than 0.0020% are added, the strength-increasing effect is saturated, and there is a concern that the ductility may degrade.
(31) In a case in which the steel contains B, Mo, Cr, V, Ti, Nb, Ni, Cu, Ca and REM, one or more elements are contained. The balance of the steel is composed of Fe and unavoidable impurities. Elements other than the above-described elements (for example, Sn, As and the like) may be further contained as unavoidable impurities as long as the elements do not impair characteristics. Furthermore, when B, Mo, Cr, V, Ti, Nb, Ni, Cu, Ca and REM are contained in amounts that are less than the above-described lower limits, the elements are treated as unavoidable impurities.
(32) In addition, in the hot-stamped steel according to the embodiment, as shown in
(5[Si]+[Mn])/[C]>10(A)
(33) To satisfy a condition of TS50000 MPa.Math.%, the above expression (A) is preferably satisfied. When the value of (5[Si]+[Mn])/[C] is 10 or less, it is not possible to obtain a sufficient hole expansibility. This is because, when the amount of C is large, the hardness of a hard phase becomes too high, a hardness difference (ratio of the hardness) between the hard phase and a soft phase becomes great, and therefore the value deteriorates, and, when the amount of Si or the amount of Mn is small, TS becomes low. Regarding the value of (5[Si]+[Mn])/[C], since the value does not change even after hot stamping as described above, the expression is preferably satisfied when the cold-rolled steel sheet is produced.
(34) Generally, it is the martensite rather than the ferrite to dominate the formability (hole expansibility) in a dual-phase steel (DP steel). As a result of intensive studies by the inventors regarding the hardness of martensite, it was clarified that, when the hardness difference (the ratio of the hardness) of the martensite between a surface portion of a sheet thickness and a central portion of the sheet thickness, and the hardness distribution of the martensite in the central portion of the sheet thickness are in a predetermined state in a phase before quenching in the hot stamping, the state is almost maintained even after hot stamping as shown in
(35) In addition, regarding the hardness of the martensite measured with an nanoindenter manufactured by Hysitron Corporation, the inventors found that the fulfillments of the following expression (B) and the following expression (C) are advantageous to the hole expansibility of the hot-stamped steel. The fulfillments of the expression (H) and the expression (I) are also advantageous in the same manner. Here, H1 is the average hardness of the martensite in the surface portion of the sheet thickness that is within an area having a width of 200 m in a thickness direction from an outermost layer of the hot-stamped steel, H2 is the average hardness of the martensite in an area having a width of 100 m in the thickness direction from the central portion of the sheet thickness in the central portion of the sheet thickness in the hot-stamped steel, and HM is the variance of the hardness of the martensite in an area having a width of 100 m in the thickness direction from the central portion of the sheet thickness in the hot-stamped steel. In addition, H10 is the hardness of the martensite in the surface portion of the sheet thickness in the cold-rolled steel sheet before quenching in the hot stamping, H20 is the hardness of the martensite in the central portion of the sheet thickness, that is, in an area having a width of 200 m in the thickness direction in a center of the sheet thickness in the cold-rolled steel sheet before quenching in the hot stamping, and HM0 is the variance of the hardness of the martensite in the central portion of the sheet thickness in cold-rolled steel sheet before quenching in the hot stamping. The H1, H10, H2, H20, HM and HM0 are obtained from 300-point measurements for each. An area having a width of 100 m in the thickness direction from the central portion of the sheet thickness refers to an area having a center at the center of the sheet thickness and having a width of 200 m in the thickness direction.
H2/H1<1.10(B)
HM<20(C)
H20/H10<1.10(H)
HM0<20(I)
(36) In addition, here, the variance is a value obtained using the following expression (K) and indicating a distribution of the hardness of the martensite.
HM=(1/n)[n,i=1](x.sub.avex.sub.i).sup.2(K)
(37) x.sub.ave is the average value of the hardness, and x.sub.i is an ith hardness.
(38) A value of H2/H1 of 1.10 or more represents that the hardness of the martensite in the central portion of the sheet thickness is 1.10 or more times the hardness of the martensite in the surface portion of the sheet thickness, and, in this case, HM becomes 20 or more even after hot stamping as shown in
(39) In addition, the variance HM being 20 or more even after hot stamping indicates that a scattering of the hardness of the martensite is large, and portions in which the hardness is too high locally exist. In this case, TS becomes less than 50000 MPa.Math.% as shown in
(40) In the hot-stamped steel according to the embodiment, the area fraction of ferrite is 40% to 95%. When the area fraction of ferrite is less than 40%, a sufficient elongation or a sufficient hole expansibility cannot be obtained. On the other hand, when the area fraction of the ferrite exceeds 95%, the martensite becomes insufficient, and a sufficient strength cannot be obtained. Therefore, the area fraction of ferrite in the hot-stamped steel is set to 40% to 95%. In addition, the hot-stamped steel also includes martensite, the area fraction of martensite is 5% to 60%, and the total of the area fraction of ferrite and the area fraction of martensite is 60% or more. All or principal portions of the hot-stamped steel are occupied by ferrite and martensite, and furthermore, one or more of bainite and retained austenite may be included in the hot-stamped steel. However, when retained austenite remains in the hot-stamped steel, a secondary working brittleness and a delayed fracture characteristic are likely to degrade. Therefore, it is preferable that retained austenite is substantially not included; however, unavoidably, 5% or less of retained austenite in a volume fraction may be included. Since pearlite is a hard and brittle structure, it is preferable not to include pearlite in the hot-stamped steel; however, unavoidably, up to 10% of pearlite in an area fraction may be included. Furthermore, the amount of bainite may be 40% at most in an area fraction with respect to a region excluding ferrite and martensite. Here, ferrite, bainite and pearlite were observed through Nital etching, and martensite was observed through Le pera etching. In both cases, a portion of the sheet thickness was observed at a magnification of 1000 times. The volume fraction of retained austenite was measured with an X-ray diffraction apparatus after polishing the steel sheet up to the portion of the sheet thickness. The portion of the sheet thickness refers to a portion of the thickness of the steel sheet away from a surface of the steel sheet in a thickness direction of the steel sheet in the steel sheet.
(41) In the embodiment, the hardness of the martensite is specified by a hardness obtained using a nanoindenter under the following conditions. Magnification for observing indentation: 1000 Visual field for observation: height of 90 m and width of 120 m Indenter shape: Berkovich-type three-sided pyramid diamond indenter Compression load: 500 N (50 mgf) Loading time for indenter compression: 10 seconds Unloading time period for indenter compression: 10 seconds (the indenter is not kept at a position of the maximum load.)
(42) A relationship between compression depth and load is obtained under the above condition, and hardness is calculated from the relationship. The hardness can be calculated by a conventional method. The hardness is measured at 10 positions, the hardness of martensite is obtained by an arithmetic average for the 10 hardness values. The individual positions for measurement are not particularly limited as long as the positions are within martensite grains. However, the distance between positions for measurement must be 5 m or longer
(43) Since an indentation formed in an ordinary Vickers hardness test is larger than the martensite, according to the Vickers hardness test, while a macroscopic hardness of the martensite and peripheral structures thereof (ferrite and the like) can be obtained, it is not possible to obtain the hardness of the martensite itself. Since the formability (hole expansibility) is significantly affected by the hardness of the martensite itself, it is difficult to sufficiently evaluate the formability only with a Vickers hardness. On the contrary, in the embodiment, since the distribution state of hardness is given based on the hardness of the martensite in the hot-stamped steel measured with the nanoindenter, it is possible to obtain an extremely favorable formability.
(44) In addition, in the cold-rolled steel sheet before quenching in the hot stamping and the hot-stamped steel, as a result of observing MnS at a location of of the sheet thickness and in the central portion of the sheet thickness, it was found that it is preferable that the area fraction of the MnS having an equivalent circle diameter of 0.1 m to 10 m is 0.01% or less, and, as shown in
n2/n1<1.5(D)
n20/n0<1.5(J)
(45) These relationships are all identical to the steel sheet before quenching in the hot stamping, the steel sheet after hot stamping, and the hot-stamped steel.
(46) When the area fraction of the MnS having an equivalent circle diameter of 0.1 m to 10 m is more than 0.01% after hot stamping, the hole expansibility is likely to degrade. The lower limit of the area fraction of the MnS is not particularly specified, however, 0.0001% or more of the MnS is present due to a below-described measurement method, a limitation of a magnification and a visual field, and an original amount of Mn or the S. In addition, a value of an n2/n1 (or an n20/n10) of 1.5 or more indicates that a number density of the MnS having an equivalent circle diameter of 0.1 m to 10 m in the central portion of the sheet thickness of the hot-stamped steel (or the cold-rolled steel sheet before hot stamping) is 1.5 or more times the number density of the MnS having an equivalent circle diameter of 0.1 m or more in the portion of the sheet thickness of the hot-stamped steel (or the cold-rolled steel sheet before hot stamping). In this case, the formability is likely to degrade due to a segregation of the MnS in the central portion of the sheet thickness of the hot-stamped steel (or the cold-rolled steel sheet before hot stamping). In the embodiment, the equivalent circle diameter and number density of the MnS having an equivalent circle diameter of 0.1 m to 10 m were measured with a field emission scanning electron microscope (Fe-SEM) manufactured by JEOL Ltd. At a measurement, a magnification was 1000 times, and a measurement area of the visual field was set to 0.120.09 mm.sup.2 (=10800 m.sup.210000 m.sup.2). Ten visual fields were observed in the portion of the sheet thickness, and ten visual fields were observed in the central portion of the sheet thickness. The area fraction of the MnS having an equivalent circle diameter of 0.1 m to 10 m was computed with particle analysis software. In the hot-stamped steel according to the embodiment, the form (shape and number) of the MnS formed before hot stamping is the same before and after hot stamping.
(47) When the hot stamping is carried out on the cold-rolled steel sheet having the above-described configuration, it is possible to obtain a hot-stamped steel having a tensile strength of 400 MPa to 1000 MPa, and hole expansibility is significantly improved in the hot-stamped steel having a tensile strength of approximately 400 MPa to 800 MPa.
(48) Furthermore, a hot-dip galvanized layer, a galvannealed layer, an electrogalvanized layer or an aluminized layer may be formed on a surface of the hot-stamped steel according to the embodiment. It is preferable to form the above-described plating in terms of rust prevention. A formation of the above-described platings does not impair the effects of the embodiment. The above-described platings can be carried out with a well-known method.
(49) A cold-rolled steel sheet according to another embodiment of the present invention includes, by mass %, C: 0.030% to 0.150%; Si: 0.010% to 1.000%; Mn: 0.50% or more and less than 1.50%; P: 0.001% to 0.060%; S: 0.001% to 0.010%; N: 0.0005% to 0.0100%; Al: 0.010% to 0.050%, and optionally at least one of B: 0.0005% to 0.0020%; Mo: 0.01% to 0.50%; Cr: 0.01% to 0.50%; V: 0.001% to 0.100%; Ti: 0.001% to 0.100%; Nb: 0.001% to 0.050%; Ni: 0.01% to 1.00%; Cu: 0.01% to 1.00%; Ca: 0.0005% to 0.0050%; REM: 0.0005% to 0.0050%, and a balance of Fe and impurities, in which, when [C] is the amount of C by mass %, [Si] is the amount of Si by mass %, and [Mn] is the amount of Mn by mass %, the following expression (A) is satisfied, the area fraction of ferrite is 40% to 95% and the area fraction of martensite is 5% to 60%, the total of the area fraction of ferrite and the area fraction of martensite is 60% or more, the cold-rolled steel sheet optionally further can include one or more of pearlite, retained austenite, and bainite, the area fraction of pearlite is 10% or less, the volume fraction of retained austenite is 5% or less, and the area fraction of bainite is less than 40%, the hardness of the martensite measured with a nanoindenter satisfies the following expression (H) and the following expression (I), TS which is a product of tensile strength TS and hole expansion ratio is 50000 MPa.Math.% or more.
(5[Si]+[Mn])/[C]>10(A)
H20/H10<1.10(H)
HM0<20(I)
(50) The H10 is the average hardness of the martensite in a surface portion of a sheet thickness, the H20 is the average hardness of the martensite in a central portion of the sheet thickness, the central portion is an area having a width of 200 m in the thickness direction at a center of the sheet thickness, and the HM0 is the variance of the average hardness of the martensite in the central portion of the sheet thickness.
(51) The above hot-stamped steel is obtained by hot-stamping the cold-rolled steel sheet according to the embodiment as described below. Even when the cold-rolled steel sheet is hot stamped, the chemical composition of the cold-rolled steel sheet does not change. In addition, as described above, when the hardness ratio of the martensite between the surface portion of the sheet thickness, and the central portion of the sheet thickness and the hardness distribution of the martensite in the central portion of the sheet thickness are in the above predetermined state in a phase before quenching in the hot stamping, the state is almost maintained even after hot stamping (see also
(52) In the cold-rolled steel sheet according to the embodiment, the area fraction of MnS existing in the cold-rolled steel sheet and having an equivalent circle diameter of 0.1 m to 10 m may be 0.01% or less, and the following expression (J) may be satisfied
n20/n10<1.5(J)
(53) The n10 is the average number density per 10000 m.sup.2 of the MnS having an equivalent circle diameter of 0.1 m to 10 m in a portion of the sheet thickness, and the n20 is the average number density per 10000 m.sup.2 of the MnS having an equivalent circle diameter of 0.1 m to 10 m in the central portion of the sheet thickness.
(54) As described above, the ratio of n20 to n10 having the cold-rolled steel sheet before hot stamping is almost maintained even after hot-stamping the cold-rolled steel sheet (see also
(55) A hot-dip galvanized layer may be formed on a surface of the cold-rolled steel sheet according to the embodiment in a similar manner with the above-described hot-stamped steel. In addition, the hot-dip galvanized layer may be alloyed in the cold-rolled steel sheet according to the embodiment. Furthermore, an electrogalvanized layer or aluminized layer may be formed on the surface of the cold-rolled steel sheet according to the embodiment.
(56) Hereinafter, a method for producing the cold-rolled steel sheet (a cold-rolled steel sheet, a galvanized cold-rolled steel sheet, a galvannealed cold-rolled steel sheet, an electrogalvanized cold-rolled steel sheet and an aluminized cold-rolled steel sheet) and a method for producing the hot-stamped steel for which the cold-rolled steel sheet is used according to the embodiments will be described.
(57) When producing the cold-rolled steel sheet and the hot-stamped steel for which the cold-rolled steel sheet is used according to the embodiments, as an ordinary condition, a molten steel from a converter is continuously cast, thereby producing a steel. In the continuous casting, when a casting rate is fast, precipitates of Ti and the like become too fine, and, when the casting rate is slow, productivity deteriorates, and consequently, the above-described precipitates coarsen and the number of grains (for example, ferrite, martensite and the like) in the microstructure decreases, the grains coarsen in the microstructure, and thus, there is a case other characteristics such as a delayed fracture cannot be controlled. Therefore, the casting rate is desirably 1.0 m/minute to 2.5 m/minute.
(58) The steel after the casting can be subjected to hot-rolling as it is. Alternatively, in a case in which the steel after cooling has been cooled to less than 1100 C., it is possible to reheat the steel after cooling to 1100 C. to 1300 C. in a tunnel furnace or the like and subject the steel to hot-rolling. When the heating temperature is less than 1100 C., it is difficult to ensure a finishing temperature in the hot-rolling, which causes a degradation of the elongation. In addition, in the hot-stamped steel for which a cold-rolled steel sheet to which Ti and Nb are added is used, since the dissolution of the precipitates becomes insufficient during the heating, which causes a decrease in strength. On the other hand, when the heating temperature is more than 1300 C., the amount of scale formed increases, and there is a case in which it is not possible to make surface property of the hot-stamped steel favorable.
(59) In addition, to decrease the area fraction of the MnS having an equivalent circle diameter of 0.1 m to 10 m, when the amount of Mn and the amount of S in the steel are respectively represented by [Mn] and [S] by mass %, it is preferable for a temperature T ( C.) of a heating furnace before carrying out hot-rolling, an in-furnace time t (minutes), [Mn] and [S] to satisfy a following expression (G) as shown in
Tln(t)/(1.7[Mn]+[S])>1500(G)
(60) When Tln(t)/(1.7[Mn]+[S]) is equal to or less than 1500, the area fraction of the MnS having an equivalent circle diameter of 0.1 m to 10 m becomes large, and there is a case in which a difference between the number density of the MnS having an equivalent circle diameter of 0.1 m to 10 m in the portion of the sheet thickness and the number density of the MnS having an equivalent circle diameter of 0.1 m to 10 m in the central portion of the sheet thickness becomes large. The temperature of the heating furnace before carrying out hot-rolling refers to an extraction temperature at an outlet side of the heating furnace, and the in-furnace time refers to a time elapsed from a placement of the steel into the hot heating furnace to an extraction of the steel from the heating furnace. Since the MnS does not change even after hot stamping as described above, it is preferable to satisfy the expression (G) in a heating step before hot-rolling.
(61) Next, the hot-rolling is carried out according to a conventional method. At this time, it is desirable to carry out hot-rolling on the steel at the finishing temperature (the hot-rolling end temperature) which is set to be in a range of an Ar.sub.3 temperature to 970 C. When the finishing temperature is less than the Ar.sub.3 temperature, the hot-rolling includes a (+) two-phase region rolling (two-phase region rolling of the ferrite+the martensite), and there is a concern that the elongation may degrade. On the other hand, when the finishing temperature exceeds 970 C., the austenite grain size coarsens, and the fraction of the ferrite becomes small, and thus, there is a concern that the elongation may degrade. A hot-rolling facility may have a plurality of stands.
(62) Here, the Ar.sub.3 temperature was estimated from an inflection point of a length of a test specimen after carrying out a formastor test.
(63) After the hot-rolling, the steel is cooled at an average cooling rate of 20 C./second to 500 C./second, and is coiled at a predetermined coiling temperature CT. In a case in which the average cooling rate is less than 20 C./second, the pearlite that causes the degradation of the ductility is likely to be formed. On the other hand, the upper limit of the cooling rate is not particularly specified and is set to approximately 500 C./second in consideration of a facility specification, but is not limited thereto.
(64) After coiling the steel, pickling is carried out, and cold-rolling is carried out. At this time, to obtain a range satisfying the above-described expression (C) as shown in
1.5r1/r+1.2r2/r+r3/r>1.00(E)
(65) Here, the ri is an individual target cold-rolling reduction (%) at an ith stand (i=1, 2, 3) from an uppermost stand in the cold-rolling, and the r is a total target cold-rolling reduction (%) in the cold-rolling. The total cold-rolling reduction is a so-called cumulative reduction, and on a basis of the sheet thickness at an inlet of a first stand, is a percentage of the cumulative reduction (the difference between the sheet thickness at the inlet before a first pass and the sheet thickness at an outlet after a final pass) with respect to the above-described basis.
(66) When the steel is cold-rolled under the conditions in which the expression (E) is satisfied, it is possible to sufficiently divide pearlite in the cold-rolling even when a large pearlite exists before the cold-rolling. As a result, it is possible to eliminate pearlite or limit the area fraction of pearlite to a minimum through the annealing carried out after cold-rolling, and therefore it becomes easy to obtain a structure in which the expression (B) and the expression (C) (or the expression (H) and the expression (I)) are satisfied. On the other hand, in a case in which the expression (E) is not satisfied, the cold-rolling reductions in upper stream stands are not sufficient, the large pearlite is likely to remain, and it is not possible to form a desired martensite in the following annealing. Therefore, it is not possible to obtain a structure in which the expression (B) and the expression (C) (or the expression (H) and the expression (I)) are satisfied. That is, in the case in which the expression (E) is not satisfied, it is not possible to obtain a feature of H2/H1<1.10 (or H20/H10<1.10), and a feature of HM<20 (or HM0<20). In addition, the inventors found that, when the expression (E) is satisfied, an obtained form of the martensite structure after the annealing is maintained in almost the same state even after hot stamping is carried out, and therefore the hot-stamped steel according to the embodiment becomes advantageous in terms of the elongation or the hole expansibility even after hot stamping. In a case in which the hot-stamped steel according to the embodiment is heated up to the two-phase region in the hot stamping, a hard phase including martensite before quenching in the hot stamping turns into an austenite structure, and ferrite before quenching in the hot stamping remains as it is. Carbon (C) in austenite does not move to the peripheral ferrite. After that, when cooled, austenite turns into a hard phase including martensite. That is, when the expression (E) is satisfied, the expression (H) is satisfied before hot stamping and the expression (B) is satisfied after hot stamping, and thereby the hot-stamped steel becomes excellent in terms of the formability.
(67) r, r1, r2 and r3 are the target cold-rolling reductions. Generally, the cold-rolling is carried out while controlling the target cold-rolling reduction and an actual cold-rolling reduction to become substantially the same value. It is not preferable to carry out the cold-rolling in a state in which the actual cold-rolling reduction is unnecessarily made to be different from the target cold-rolling reduction. However, in a case in which there is a large difference between a target rolling reduction and an actual rolling reduction, it is possible to consider that the embodiment is carried out when the actual cold-rolling reductions satisfy the expression (E). Furthermore, the actual cold-rolling reduction is preferably within 10% of the target cold-rolling reduction.
(68) In addition, it is more preferable that the actual cold-rolling reductions satisfy the following expression.
1.201.5r1/r+1.2r2/r+r3/r>1.00(E)
(69) When 1.5r1/r+1.2r2/r+r3/r exceeds 1.20, a heavy load is applied to a cold rolling mill, productivity is degraded. Tensile strength of the steel sheet according to the above-described embodiment is a range of 400 MPa to 1000 MPa, and is much larger than the tensile strength of typical cold-rolled steel sheets. It is necessary to apply a rolling load of 1800 ton or more per a stand in order to carry out the cold-rolling under a condition that 1.5r1/r+1.2r2/r+r3/r exceeds 1.20 in the steel sheet having such tensile strength. It is difficult to apply such heavy rolling load in consideration of rigidity of stands and/or rolling facility capability. Furthermore, when such heavy rolling load is applied, there is a concern that production efficiency is degraded.
(70) After cold-rolling, a recrystallization is caused in the steel sheet by annealing the steel. The annealing forms a desired martensite. Furthermore, regarding an annealing temperature, it is preferable to carry out the annealing by heating the steel sheet to 700 C. to 850 C., and cool the steel sheet to a room temperature or a temperature at which a surface treatment such as the galvanizing is carried out. When the annealing is carried out in the above-described range, it is possible to stably ensure a predetermined area fraction of the ferrite and a predetermined area fraction of the martensite, to stably set the total of the area fraction of the ferrite and the area fraction of the martensite to 60% or more, and to contribute to an improvement of TS. A holding time at 700 C. to 850 C. is preferably 1 second or more as long as the productivity is not impaired (for example, 300 second) to reliably obtain a predetermined structure. The temperature-increase rate is preferable in a range of 1 C./second to an upper limit of a facility capacity, and the cooling rate is preferable in a range of 1 C./second to the upper limit of the facility capacity. In a temper-rolling step, temper-rolling is carried out with a conventional method. The elongation ratio of the temper-rolling is, generally, approximately 0.2% to 5%, and is preferable within a range in which a yield point elongation is avoided and the shape of the steel sheet can be corrected.
(71) As a still more preferable condition of the embodiment, when the amount of C (mass %), the amount of Mn (mass %), the amount of Cr (mass %) and the amount of Mo (mass %) of the steel are represented by [C], [Mn], [Cr] and [Mo], respectively, regarding the coiling temperature CT, it is preferable to satisfy the following expression (F).
560474[C]90[Mn]20[Cr]20[Mo]<CT <830270[C]90[Mn]70[Cr]80[Mo](F)
(72) As shown in
(73) When the expression (F) is satisfied, the ferrite and the hard phase have an ideal distribution form before hot stamping as described above. In this case, when a two-phase region heating is carried out in the hot stamping, the distribution form is maintained as described above. If it is possible to more reliably ensure a microstructure having the above-described feature by satisfying the expression (F), the microstructure is maintained even after hot stamping, and the hot-stamped steel becomes excellent in terms of formability.
(74) Furthermore, to improve the rust-preventing capability, it is also preferable to include a galvanizing step in which a galvanized layer is formed on the steel between an annealing step and the temper-rolling step, and to form the galvanized layer on a surface of the cold-rolled steel sheet. Furthermore, it is also preferable that the method for producing according to the embodiment include an alloying step in which an alloying treatment is performed after galvanizing the steel. In a case in which the alloying treatment is performed, a treatment in which a galvannealed surface is brought into contact with a substance oxidizing the galvannealed surface such as water vapor, thereby thickening of an oxidized film may be further carried out on the surface.
(75) It is also preferable to include, for example, an electrogalvanizing step in which an electrogalvanized layer is formed on the steel after the temper-rolling step as well as the galvanizing step and the galvannealing step and to form an electrogalvanized layer on the surface of the cold-rolled steel sheet. In addition, it is also preferable to include, instead of the galvanizing step, an aluminizing step in which an aluminized layer is formed on the steel between the annealing step and the temper-rolling step. The aluminizing is generally hot-dip aluminizing which is preferable.
(76) After a series of the above-described treatments, the steel is heated to a temperature range of 700 C. to 1000 C., and is hot stamped in the temperature range. In the hot stamping step, the hot stamping is desirably carried out, for example, under the following conditions. First, the steel sheet is heated up to 700 C. to 1000 C. at the temperature-increase rate of 5 C./second to 500 C./second, and the hot stamping (a hot stamping step) is carried out after the holding time of 1 second to 120 seconds. To improve the formability, the heating temperature is preferably an Ac.sub.3 temperature or less. Subsequently, the steel sheet is cooled, for example, to the room temperature to 300 C. at the cooling rate of 10 C./second to 1000 C./second (quenching in the hot stamping). The Ac.sub.3 temperature was calculated from the inflection point of the length of the test specimen after carrying out the formastor test and measuring the infection point.
(77) When the heating temperature in the hot stamping step is less than 700 C., the quenching is not sufficient, and consequently, the strength cannot be ensured, which is not preferable. When the heating temperature is more than 1000 C., the steel sheet becomes too soft, and, in a case in which a plating, particularly zinc plating, is formed on the surface of the steel sheet, there is a concern that the zinc may be evaporated and burned, which is not preferable. Therefore, the heating temperature in the hot stamping is preferably 700 C. to 1000 C. When the temperature-increase rate is less than 5 C./second, since it is difficult to control heating in the hot stamping, and the productivity significantly degrades, it is preferable to carry out the heating at the temperature-increase rate of 5 C./second or more. On the other hand, the upper limit of the temperature-increase rate of 500 C./second depends on a current heating capability, but is not necessary to limit thereto. At a cooling rate of less than 10 C./second, since the rate control of the cooling after the hot stamping step is difficult, and the productivity also significantly degrades, it is preferable to carry out the cooling at the cooling rate of 10 C./second or more. The upper limit of the cooling rate of 1000 C./second depends on a current cooling capability, but is not necessary to limit thereto. A reason for setting a time until the hot stamping after an increase in the temperature to 1 second or more is a current process control capability (a lower limit of a facility capability), and a reason for setting the time until the hot stamping after the increase in the temperature to 120 seconds or less is to avoid an evaporation of the zinc or the like in a case in which the galvanized layer or the like is formed on the surface of the steel sheet. The reason for setting the cooling temperature to the room temperature to 300 C. is to sufficiently ensure the martensite and ensure the strength of the hot-stamped steel.
(78)
(79) In the hot-stamped steel of the embodiment, the expression (B) and the expression (C) are satisfied even after hot stamping is carried out under the above-described condition. In addition, consequently, it is possible to satisfy the condition of TS50000 MPa.Math.% even after hot stamping is carried out.
(80) As described above, when the above-described conditions are satisfied, it is possible to manufacture the hot-stamped steel in which the hardness distribution or the structure is maintained even after hot stamping, and consequently the strength is ensured and a more favorable hole expansibility can be obtained.
EXAMPLES
(81) Steel having a composition described in Table 1-1 and Table 1-2 was continuously cast at a casting rate of 1.0 m/minute to 2.5 m/minute, a slab was heated in a heating furnace under a conditions shown in Table 5-1 and Table 5-2 with a conventional method as it is or after cooling the slab once, and hot-rolling was carried out at a finishing temperature of 910 C. to 930 C., thereby producing a hot rolled steel sheet. After that, the hot rolled steel sheet was coiled at a coiling temperature CT described in Table 5-1 and Table 5-2. After that, pickling was carried out so as to remove a scale on a surface of the steel sheet, and a sheet thickness was made to be 1.2 mm to 1.4 mm through cold-rolling. At this time, the cold-rolling was carried out so that the value of the expression (E) became a value described in Table 5-1 and Table 5-2.
(82) After cold-rolling, annealing was carried out in a continuous annealing furnace at an annealing temperature described in Table 2-1 and Table 2-2. On a part of the steel sheets, a galvanized layer was further formed in the middle of cooling after a soaking in the continuous annealing furnace, and then an alloying treatment was further performed on a part of the part of the steel sheets, thereby forming a galvannealed layer. In addition, an electrogalvanized layer or an aluminized layer was formed on another part of the steel sheets. Furthermore, temper-rolling was carried out at an elongation ratio of 1% according to a conventional method. In this state, a sample was taken to evaluate material qualities and the like before quenching in the hot stamping, and a material quality test or the like was carried out. After that, to obtain a hot-stamped steel having a form as shown in
(%)={(dd)/d}100(L)
(83) d: a hole diameter when a crack penetrates the sheet thickness
(84) d: an initial hole diameter
(85) Furthermore, regarding plating types in Table 3-1 and Table 3-2, CR represents a non-plated cold-rolled steel sheet, GI represents that the galvanized layer is formed, GA represents that the galvannealed layer is formed, EG represents that the electrogalvanized layer is formed, and Al represents that the aluminized layer is formed.
(86) Furthermore, determinations G and B in the tables have the following meanings.
(87) G: a target condition expression is satisfied.
(88) B: the target condition expression is not satisfied.
(89) The chemical conversion treatment property after hot stamping was evaluated as a surface property after hot stamping in a hot-stamped steel produced from a non-plated cold-rolled steel sheet. The plating adhesion of hot-stamped steel was evaluated as a surface property after hot stamping when zinc, aluminum, or the like was plated on a cold-rolled steel sheet from which a hot-stamped steel was produced.
(90) The chemical conversion treatment property was evaluated through the following procedure. First, a chemical conversion treatment was applied to each sample under a condition that the bath temperature was 43 C. and the time period for chemical conversion treatment was 120 seconds using a commercial chemical conversion treatment agent (Palbond PB-L3020 system manufactured by Nihon Parkerizing Co. Ltd.). Second, the crystal uniformity of a conversion coating was evaluated by SEM observation on the surface of each sample to which the chemical conversion treatment is applied. The crystal uniformity of a conversion coating was classified by the following valuation standards. Good (G) was given to a sample without lack of hiding in crystals of the conversion coating, bad (B) was given to a sample with a lack of hiding in an area of crystals of the conversion coating, and very bad (VB) was given to a sample with a conspicuous lack of hiding in crystals of the conversion coating.
(91) The plating adhesion was evaluated through the following procedure. First, a sheet specimen for testing having a height of 100 mm, a width of 200 mm, and a thickness of 2 mm was taken from a plated cold-rolled steel sheet. The plating adhesion was evaluated by applying a V bending and straightening test to the sheet specimen. In the V bending and straightening test, the above sheet specimen was bent using a die for the V bending test (a bending angle of 60), and then the sheet specimen after the V bending was straightened again by a press working. A cellophane tape (CELLOTAPE CT405AP-24 manufactured by Nichiban Co. Ltd.) was stuck on a portion (deformed portion) which was located in the inside of a bent portion during V bending in the straightened sheet specimen, and then the cellophane tape was taken off by hand. Next, the width of a detached plating layer which is stuck on the cellophane tape was measured. In the Examples, good (G) was given to a sheet specimen in which the width was 5 mm or less, bad (B) was given to a sheet specimen in which the width was more than 5 mm and 10 mm or less, and very bad (VB) was given to a sheet specimen in which the width was more than 10 mm.
(92) TABLE-US-00001 TABLE 1-1 STEEL TYPE REFERENCE SYMBOL C Si Mn P S N Al Cr Mo A EXAMPLE 0.045 0.143 0.55 0.002 0.007 0.0033 0.031 0 0 B 0.061 0.224 0.63 0.025 0.005 0.0054 0.025 0 0 C 0.149 0.970 1.45 0.006 0.009 0.0055 0.035 0.22 0 D 0.075 0.520 0.69 0.007 0.006 0.0025 0.020 0 0.25 E 0.082 0.072 0.51 0.006 0.009 0.0032 0.045 0.40 0 F 0.098 0.212 1.15 0.007 0.009 0.0075 0.035 0 0 G 0.102 0.372 0.82 0.013 0.008 0.0035 0.037 0 0 H 0.085 0.473 0.53 0.056 0.001 0.0029 0.041 0.39 0.15 I 0.095 0.720 0.72 0.008 0.002 0.0055 0.032 0 0 J 0.071 0.777 0.82 0.006 0.008 0.0014 0.015 0 0.45 K 0.091 0.165 1.21 0.006 0.009 0.0035 0.041 0 0 L 0.102 0.632 1.11 0.015 0.007 0.0041 0.032 0 0.37 M 0.105 0.301 1.22 0.012 0.009 0.0015 0.035 0 0 N 0.105 0.253 1.44 0.008 0.005 0.0032 0.042 0 0.35 O 0.144 0.945 0.89 0.008 0.006 0.0043 0.036 0 0.21 P 0.095 0.243 1.45 0.009 0.007 0.0025 0.039 0.49 0 Q 0.115 0.342 1.03 0.015 0.004 0.0038 0.037 0 0.15 R 0.121 0.175 0.78 0.008 0.003 0.0038 0.036 0 0 S 0.129 0.571 0.93 0.016 0.006 0.0024 0.039 0 0.19 T 0.141 0.150 1.40 0.018 0.003 0.0029 0.031 0 0.21 U 0.129 0.105 1.35 0.018 0.007 0.0064 0.019 0 0.29 W 0.143 0.652 1.17 0.012 0.006 0.0019 0.038 0 0 X 0.141 0.922 1.02 0.015 0.004 0.0066 0.026 0.25 0.16 Y 0.131 0.155 1.47 0.008 0.006 0.0065 0.043 0.37 0 Z 0.149 0.105 1.32 0.009 0.003 0.0061 0.031 0 0.25 STEEL TYPE REFERENCE EXPRESSION SYMBOL V Ti Nb Ni Cu Ca B REM (A) A 0 0 0 0 0 0 0 0 28.1 B 0 0 0 0.5 0 0 0 0 28.7 C 0 0 0 0 0 0 0 0 42.3 D 0 0 0 0 0 0 0 0 43.9 E 0 0 0 0 0 0 0 0 10.6 F 0 0 0 0 0.7 0.005 0 0 22.6 G 0 0 0 0 0 0 0 0 26.3 H 0 0 0 0 0 0.004 0 0 34.1 I 0.05 0 0 0 0 0 0 0 45.5 J 0 0 0 0 0 0 0 0 66.3 K 0 0 0 0 0 0 0 0 22.4 L 0 0.07 0 0 0 0 0 0 41.9 M 0 0 0 0 0 0 0 0 26.0 N 0 0 0 0 0 0 0.0019 0 25.8 O 0 0 0 0 0 0 0 0 39.0 P 0 0 0 0 0 0 0 0 28.1 Q 0 0 0.03 0 0 0 0.0011 0 23.8 R 0 0 0.03 0 0 0 0 0 13.7 S 0 0 0 0 0 0 0 0 29.3 T 0 0.03 0 0 0 0 0 0 15.2 U 0 0 0 0 0 0 0.0009 0 14.5 W 0 0 0 0 0 0.003 0 0 31.0 X 0 0.07 0 0 0 0 0.0015 0.0025 39.9 Y 0 0 0 0 0 0 0.0013 0 17.1 Z 0.04 0 0 0 0 0 0 0 12.4
(93) TABLE-US-00002 TABLE 1-2 STEEL TYPE REFERENCE SYMBOL C Si Mn P S N Al Cr Mo AA COMPARATIVE 0.079 0.205 0.89 0.012 0.006 0.0021 0.029 0 0 EXAMPLE AB COMPARATIVE 0.092 0.219 0.96 0.010 0.004 0.0029 0.041 0 0 EXAMPLE AC COMPARATIVE 0.105 0.103 1.22 0.008 0.002 0.0041 0.039 0 0 EXAMPLE AD COMPARATIVE 0.076 0.355 0.98 0.013 0.005 0.0039 0.033 0 0 EXAMPLE AE COMPARATIVE 0.142 0.246 0.69 0.009 0.003 0.0030 0.031 0 0 EXAMPLE AF COMPARATIVE 0.129 0.363 1.28 0.007 0.003 0.0040 0.042 0 0 EXAMPLE AG COMPARATIVE 0.118 0.563 1.13 0.008 0.004 0.0039 0.041 0 0 EXAMPLE AH COMPARATIVE 0.027 0.323 1.49 0.006 0.002 0.0031 0.032 0 0 EXAMPLE AI COMPARATIVE 0.231 0.602 1.39 0.004 0.005 0.0013 0.040 0 0 EXAMPLE AJ COMPARATIVE 0.093 0.004 1.01 0.006 0.008 0.0039 0.036 0 0.23 EXAMPLE AK COMPARATIVE 0.098 1.493 0.71 0.007 0.003 0.0041 0.036 0.38 0.33 EXAMPLE AL COMPARATIVE 0.125 0.780 0.21 0.011 0.003 0.0035 0.032 0 0 EXAMPLE AM COMPARATIVE 0.136 0.040 2.75 0.008 0.003 0.0044 0.039 0 0 EXAMPLE AN COMPARATIVE 0.103 0.265 1.12 0.095 0.004 0.0025 0.042 0.36 0.12 EXAMPLE AO COMPARATIVE 0.072 0.223 1.41 0.002 0.025 0.0052 0.036 0 0 EXAMPLE AP COMPARATIVE 0.051 0.281 1.03 0.012 0.007 0.1630 0.032 0 0 EXAMPLE AQ COMPARATIVE 0.141 0.011 1.39 0.019 0.008 0.0045 0.003 0 0.23 EXAMPLE AR COMPARATIVE 0.149 0.150 1.23 0.005 0.003 0.0035 0.065 0 0.37 EXAMPLE AS COMPARATIVE 0.133 0.030 1.10 0.012 0.004 0.0020 0.035 0 0 EXAMPLE AT COMPARATIVE 0.135 0.170 1.24 0.010 0.004 0.0023 0.035 0 0 EXAMPLE AU COMPARATIVE 0.139 0.331 1.43 0.013 0.002 0.0044 0.030 0 0 EXAMPLE AV COMPARATIVE 0.137 0.192 1.50 0.011 0.002 0.0041 0.033 0 0 EXAMPLE AW COMPARATIVE 0.136 0.040 2.75 0.008 0.003 0.0044 0.039 0 0 EXAMPLE AX COMPARATIVE 0.137 0.192 1.50 0.011 0.002 0.0041 0.033 0 0 EXAMPLE STEEL TYPE REFERENCE EXPRESSION SYMBOL V Ti Nb Ni Cu Ca B REM (A) AA 0 0 0 0 0 0 0 0 24.2 AB 0 0 0 0 0 0 0 0 22.3 AC 0 0 0 0 0 0 0 0 16.5 AD 0 0 0 0 0 0 0 0 36.3 AE 0 0 0 0 0 0 0 0 13.5 AF 0 0 0 0 0 0 0 0 24.0 AG 0 0 0 0 0 0 0 0 33.4 AH 0 0 0 0 0 0 0 0.0050 115.0 AI 0 0 0 0 0 0 0 0 19.0 AJ 0 0 0 0 0 0 0.0011 0 11.1 AK 0 0 0 0 0 0 0.0013 0 83.4 AL 0 0 0 0 0 0 0 0 32.6 AM 0 0 0 0 0 0 0 0 21.7 AN 0 0 0.03 0 0 0 0 0 23.7 AO 0 0 0 0.4 0 0 0 0 35.1 AP 0 0 0.04 0 0 0.003 0 0 47.7 AQ 0 0 0 0 0 0 0 0 10.2 AR 0 0 0 0 0 0 0 0 13.3 AS 0 0 0 0 0 0 0.001 0 9.4 AT 0 0 0.02 0 0 0 0 0 15.5 AU 0 0 0.00 0 0 0 0 0 22.2 AV 0 0 0 0 0 0 0 0 18.0 AW 0 0 0 0 0 0 0 0 21.7 AX 0 0 0 0 0 0 0 0 18.0
(94) TABLE-US-00003 TABLE 2-1 AFTER ANNEALING AND TEMPER-ROLLING AND BEFORE HOT STAMPING STEEL FERRITE MARTENSITE TYPE TEST ANNEALING AREA AREA REFERENCE REFERENCE TEMPERATURE TS EL FRACTION FRACTION SYMBOL SYMBOL ( C.) (Mpa) (%) (%) TS EL TS (%) (%) A 1 790 445 35.5 121 15798 53845 92 7 B 2 800 468 36.2 115 16942 53820 87 6 C 3 750 502 31.2 132 15662 66264 82 10 D 4 790 542 33.1 105 17940 56910 84 8 E 5 795 542 34.8 98 18862 53116 78 7 F 6 790 585 26.5 86 15503 50310 78 6 G 7 745 552 27.2 92 15014 50784 65 8 H 8 792 622 29.1 87 18100 54114 88 6 I 9 782 598 28.3 93 16923 55614 82 9 J 10 771 565 29.2 105 16498 59325 75 9 K 11 811 635 27.1 79 17209 50165 78 10 L 12 752 672 30.6 89 20563 59808 87 7 M 13 782 612 31.4 82 19217 50184 56 27 N 14 821 631 29.6 87 18678 54897 58 27 O 15 769 629 28.7 89 18052 55981 78 13 P 16 781 692 27.1 77 18753 53284 71 24 Q 17 781 678 25.8 78 17492 52884 56 32 R 18 782 672 21.5 89 14448 59808 63 27 S 19 771 729 23.1 79 16840 57591 55 32 T 20 785 745 28.5 71 21233 52895 44 41 U 21 813 761 21.6 68 16438 51748 44 39 W 22 831 796 19.2 65 15283 51740 46 37 X 23 815 862 18.2 61 15888 52582 47 40 Y 24 802 911 19.2 59 17491 53749 45 38 Z 25 841 1021 13.5 55 13784 56155 43 41 PEARLITE AFTER ANNEALING AND TEMPER-ROLLING AND BEFORE HOT STAMPING AREA FERRITE + RESIDUAL FRACTION STEEL MARTENSITE AUSTENITE BAINITE PEARLITE BEFORE TYPE AREA VOLUME AREA AREA COLD REFERENCE FRACTION FRACTION FRACTION FRACTION ROLLING SYMBOL (%) (%) (%) (%) (%) A 99 1 0 0 25 B 93 3 4 0 25 C 92 2 5 1 34 D 92 3 5 0 26 E 85 4 11 0 42 F 84 2 7 7 62 G 73 4 15 8 72 H 94 3 3 0 35 I 91 4 5 0 42 J 84 3 7 6 29 K 88 2 6 4 34 L 94 0 5 1 15 M 83 2 6 9 8 N 85 5 4 6 42 O 91 4 3 2 33 P 95 2 2 1 25 Q 88 3 5 7 28 R 90 3 7 0 53 S 87 4 9 0 46 T 85 3 12 0 23 U 83 5 9 3 23 W 83 4 10 3 18 X 87 2 6 5 51 Y 83 2 15 0 43 Z 84 4 12 0 15
(95) TABLE-US-00004 TABLE 2-2 AFTER ANNEALING AND TEMPER-ROLLING AND BEFORE HOT STAMPING STEEL FERRITE MARTENSITE TYPE TEST ANNEALING AREA AREA REFERENCE REFERENCE TEMPERATURE TS EL FRACTION FRACTION SYMBOL SYMBOL ( C.) (Mpa) (%) (%) TS EL TS (%) (%) AA 26 804 582 27.2 76 15830 44232 62 8 AB 27 797 606 27.5 68 16665 41208 58 13 AC 28 769 581 27.6 79 16036 45899 51 9 AD 29 756 611 21.3 66 13014 40326 31 15 AE 30 792 598 24.1 75 14412 44850 52 9 AF 31 742 643 27.2 71 17490 45653 59 21 AG 32 772 602 29.1 62 17518 37324 72 17 AH 33 761 372 40.8 117 15178 43524 96 0 AI 34 789 1493 9.1 29 13586 43297 9 77 AJ 35 768 682 21.6 66 14731 45012 69 17 AK 36 802 602 30.3 59 18241 35518 76 20 AL 37 789 362 42.1 127 15240 45974 86 2 AM 38 766 832 15.7 42 13062 34944 35 42 AN 39 802 802 19.6 46 15719 36892 56 32 AO 40 816 598 24.1 38 14412 22724 69 19 AP 41 779 496 33.2 72 16467 35712 79 12 AQ 42 840 829 20.2 32 16746 26528 28 61 AR 43 776 968 14.2 39 13746 37752 27 63 AS 45 778 912 16.2 45 14774 41040 46 32 AT 46 671 713 15.9 51 11337 36363 30 10 AU 47 889 1023 11.3 32 11560 32736 2 56 AV 48 832 956 18.1 55 17304 52580 44 39 AW 38 766 832 15.7 42 13062 34944 35 42 AX 48 832 956 18.1 55 17304 52580 44 39 PEARLITE AFTER ANNEALING AND TEMPER-ROLLING AND BEFORE HOT STAMPING AREA FERRITE + RESIDUAL FRACTION STEEL MARTENSITE AUSTENITE BAINITE PEARLITE BEFORE TYPE AREA VOLUME AREA AREA COLD REFERENCE FRACTION FRACTION FRACTION FRACTION ROLLING SYMBOL (%) (%) (%) (%) (%) AA 70 2 13 15 25 AB 71 1 14 14 31 AC 60 3 17 20 17 AD 46 1 29 24 42 AE 61 2 7 30 28 AF 80 2 8 11 41 AG 89 2 8 11 21 AH 96 1 3 0 3 AI 86 3 1 10 9 AJ 86 2 4 8 26 AK 96 2 2 0 7 AL 88 1 0 11 15 AM 77 3 13 7 14 AN 88 3 9 0 16 AO 88 4 5 3 16 AP 91 2 6 1 11 AQ 89 0 11 0 22 AR 90 0 0 10 11 AS 78 0 18 4 13 AT 40 1 16 43 40 AU 58 1 33 8 7 AV 83 2 13 2 45 AW 77 3 13 7 14 AX 83 2 13 2 45
(96) TABLE-US-00005 TABLE 3-1 AFTER HOT STAMPING FERRITE + STEEL FERRITE MARTENSITE MARTENSITE TYPE AREA AREA AREA REFERENCE TS EL FRACTION FRACTION FRACTION SYMBOL (Mpa) (%) (%) TS EL TS (%) (%) (%) A 462 40.2 135 18572 62370 92 6 98 B 447 41.2 125 18416 55875 85 7 92 C 512 36.2 115 18534 58880 83 10 93 D 553 32.7 115 18083 63595 82 7 89 E 589 32.9 99 19378 58311 81 6 87 F 589 32.1 87 18907 51243 82 7 89 G 561 30.9 90 17335 50490 66 10 76 H 632 30.0 89 18960 56248 86 8 94 I 698 28.3 75 19753 52350 65 7 72 J 755 25.9 87 19555 65685 59 12 71 K 721 24.5 72 17665 51912 52 22 74 L 752 24.2 78 18198 58656 53 23 76 M 789 20.9 69 16490 54441 57 35 92 N 768 19.8 72 15206 55296 59 27 86 O 802 21.2 65 17002 52130 41 35 76 P 835 18.8 75 15698 62625 45 23 68 Q 872 22.5 61 19620 53192 41 39 80 R 852 21.5 69 18318 58788 47 31 78 S 912 20.1 56 18331 51072 56 32 88 T 965 18.5 62 17853 59830 41 41 82 U 989 17.0 55 16813 54395 49 37 86 W 1025 15.9 53 16298 54325 46 38 84 X 1049 17.2 49 18043 51401 46 37 83 Y 1102 14.5 51 15979 56202 43 40 83 Z 1189 13.1 55 15576 65395 45 48 93 AFTER HOT STAMPING RESIDUAL STEEL AUSTENITE BAINITE PEARLITE TYPE VOLUME AREA AREA PLATING REFERENCE FRACTION FRACTION FRACTION TYPE SYMBOL (%) (%) (%) *.sup.) A 1 0 1 GA B 3 4 1 GI C 1 5 1 GA D 3 8 0 GA E 1 12 0 CR F 2 4 5 GA G 2 14 8 GI H 4 0 2 EG I 4 23 1 GA J 1 25 3 Al K 1 19 6 GA L 2 21 1 CR M 2 6 0 CR N 5 4 5 GA O 4 11 9 GI P 1 31 0 EG Q 4 10 6 Al R 4 13 5 CR S 4 2 6 CR T 3 12 3 GA U 1 13 0 GA W 4 12 0 GA X 3 11 3 GA Y 1 16 0 GI Z 2 5 0 GA
(97) TABLE-US-00006 TABLE 3-2 AFTER HOT STAMPING FERRITE + STEEL FERRITE MARTENSITE MARTENSITE TYPE AREA AREA AREA REFERENCE TS EL FRACTION FRACTION FRACTION SYMBOL (Mpa) (%) (%) TS EL TS (%) (%) (%) AA 756 19.2 63 14515 47628 37 39 76 AB 821 18.3 57 15024 46797 39 42 81 AC 891 17.6 51 15682 45441 32 41 73 AD 922 16.8 41 15490 37802 29 38 67 AE 1021 15.8 31 16132 31651 49 31 80 AF 1152 13.8 38 15898 43776 37 42 79 AG 723 19.1 61 13809 44103 72 16 88 AH 412 42.1 109 17345 44908 97 0 97 AI 1513 8.3 27 12558 40851 6 88 94 AJ 821 16.9 52 13875 42692 57 25 82 AK 912 18.9 43 17237 39216 65 32 97 AL 398 41.2 113 16398 44974 86 2 88 AM 1023 14.2 43 14527 43989 45 43 88 AN 923 17.6 46 16245 42458 57 31 88 AO 736 19.2 41 14131 30176 63 26 89 AP 543 31.0 68 16833 36924 78 14 92 AQ 1128 14.3 34 16130 38352 29 63 92 AR 1062 12.9 35 13700 37170 29 65 94 AS 1109 13.8 41 15304 45469 46 32 78 AT 1021 11.9 38 12150 38798 30 28 58 AU 1236 9.9 34 12236 42024 7 69 76 AV 1151 13.1 46 15078 52946 41 44 85 AW 1023 14.2 43 14527 43989 45 43 88 AX 1151 13.1 46 15078 52946 41 44 85 AFTER HOT STAMPING RESIDUAL STEEL AUSTENITE BAINITE PEARLITE TYPE VOLUME AREA AREA PLATING REFERENCE FRACTION FRACTION FRACTION TYPE SYMBOL (%) (%) (%) *.sup.) AA 2 11 11 GA AB 1 6 12 CR AC 2 10 15 GA AD 1 14 18 EG AE 2 7 11 GI AF 2 1 18 Al AG 2 8 12 GI AH 0 3 0 EG AI 3 2 1 Al AJ 2 13 3 GA AK 2 1 0 GA AL 0 1 11 GA AM 3 8 1 GA AN 3 9 0 GI AO 4 7 0 CR AP 1 6 1 GA AQ 0 6 2 GA AR 0 0 6 GA AS 3 14 5 GA AT 1 11 30 GI AU 4 18 2 GI AV 4 10 1 GI AW 3 8 1 CR AX 4 10 1 CR
(98) TABLE-US-00007 TABLE 4-1 STEEL LEFT SIDE OF LEFT SIDE OF LEFT SIDE OF TYPE EXPRESSION EXPRESSION EXPRESSION REFERENCE (B) BEFORE DETERMI- (B) AFTER DETERMI- (C) BEFORE DETERMI- SYMBOL HOT STAMPING NATION HOT STAMPING NATION HOT STAMPING NATION A 1.01 G 1.02 G 13 G B 1.04 G 1.02 G 17 G C 1.05 G 1.07 G 5 G D 1.08 G 1.07 G 17 G E 1.07 G 1.05 G 18 G F 1.08 G 1.09 G 12 G G 1.08 G 1.09 G 15 G H 1.02 G 1.03 G 7 G I 1.05 G 1.04 G 8 G J 1.05 G 1.01 G 15 G K 1.03 G 1.04 G 19 G L 1.03 G 1.02 G 14 G M 1.08 G 1.06 G 14 G N 1.06 G 1.08 G 12 G O 1.07 G 1.08 G 13 G P 1.04 G 1.05 G 11 G Q 1.04 G 1.06 G 12 G R 1.02 G 1.04 G 15 G S 1.06 G 1.05 G 16 G T 1.09 G 1.08 G 10 G U 1.07 G 1.08 G 6 G W 1.09 G 1.08 G 7 G X 1.06 G 1.08 G 17 G Y 1.04 G 1.05 G 12 G Z 1.06 G 1.05 G 10 G STEEL LEFT SIDE OF AREA FRACTION OF AREA FRACTION OF TYPE EXPRESSION MnS OF 0.1 m MnS OF 0.1 m REFERENCE (C) AFTER DETERMI- OR MORE BEFORE OR MORE AFTER SYMBOL HOT STAMPING NATION HOT STAMPING HOT STAMPING A 15 G 0.004 0.004 B 16 G 0.006 0.005 C 3 G 0.016 0.014 D 15 G 0.006 0.006 E 17 G 0.006 0.007 F 13 G 0.015 0.015 G 12 G 0.008 0.007 H 9 G 0.006 0.005 I 9 G 0.005 0.006 J 14 G 0.005 0.006 K 18 G 0.005 0.006 L 13 G 0.006 0.007 M 15 G 0.012 0.011 N 13 G 0.003 0.003 O 12 G 0.003 0.004 P 10 G 0.006 0.005 Q 12 G 0.005 0.006 R 15 G 0.006 0.007 S 18 G 0.008 0.008 T 15 G 0.003 0.004 U 5 G 0.014 0.013 W 9 G 0.006 0.007 X 16 G 0.006 0.006 Y 11 G 0.006 0.004 Z 9 G 0.006 0.007
(99) TABLE-US-00008 TABLE 4-2 STEEL LEFT SIDE OF LEFT SIDE OF LEFT SIDE OF TYPE EXPRESSION EXPRESSION EXPRESSION REFERENCE (B) BEFORE DETERMI- (B) AFTER DETERMI- (C) BEFORE DETERMI- SYMBOL HOT STAMPING NATION HOT STAMPING NATION HOT STAMPING NATION AA 1.13 B 1.15 B 23 B AB 1.15 B 1.16 B 22 B AC 1.13 B 1.15 B 21 B AD 1.19 B 1.18 B 26 B AE 1.13 B 1.13 B 22 B AF 1.11 B 1.10 B 19 G AG 1.16 B 1.17 B 25 B AH B B B AI 1.23 B 1.19 B 22 B AJ 1.23 B 1.22 B 21 B AK 1.19 B 1.18 B 23 B AL B B B AM 1.41 B 1.39 B 31 B AN 1.26 B 1.22 B 26 B AO 1.29 B 1.31 B 28 B AP 1.06 G 1.05 G 11 G AQ 1.19 B 1.21 B 23 B AR 1.09 G 1.07 G 17 G AS 1.23 B 1.21 B 23 B AT 1.28 B 1.26 B 27 B AU 1.06 G 1.07 G 18 G AV 1.06 G 1.07 G 18 G AW 1.41 B 1.39 B 31 B AX 1.06 G 1.07 G 18 G STEEL LEFT SIDE OF AREA FRACTION OF AREA FRACTION OF TYPE EXPRESSION MnS OF 0.1 m MnS OF 0.1 m REFERENCE (C) AFTER DETERMI- OR MORE BEFORE OR MORE AFTER SYMBOL HOT STAMPING NATION HOT STAMPING HOT STAMPING AA 22 B 0.011 0.013 AB 21 B 0.008 0.007 AC 20 B 0.050 0.006 AD 25 B 0.006 0.007 AE 21 B 0.009 0.009 AF 18 G 0.003 0.003 AG 24 B 0.003 0.003 AH B 0.004 0.004 AI 23 B 0.006 0.006 AJ 23 B 0.007 0.008 AK 22 B 0.007 0.006 AL B 0.006 0.006 AM 30 B 0.006 0.007 AN 29 B 0.008 0.009 AO 33 B 0.005 0.004 AP 12 G 0.005 0.007 AQ 25 B 0.003 0.003 AR 17 G 0.002 0.002 AS 23 B 0.006 0.007 AT 28 B 0.005 0.006 AU 19 G 0.006 0.005 AV 19 G 0.006 0.005 AW 30 B 0.006 0.007 AX 19 G 0.006 0.005 HARDNESS WAS NOT MEASURED BECAUSE THE AREA FRACTION OF MARTENSITE IS SIGNIFICANTLY SMALL.
(100) TABLE-US-00009 TABLE 5-1 BEFORE HOT STAMPING AFTER HOT STAMPING STEEL LEFT LEFT SURFACE LEFT TYPE SIDE OF SIDE OF PROPERTY SIDE OF REFERENCE EXPRESSION DETERMI- EXPRESSION DETERMI- AFTER HOT EXPRESSION DETERMI- SYMBOL n1 n2 (D) NATION n1 n2 (D) NATION STAMPING (E) NATION A 10 12 1.2 G 8 11 1.4 G 1.32 G B 6 7 1.2 G 6 5 0.8 G 1.13 VG C 3 5 1.7 B 3 5 1.7 B 1.23 G D 7 6 0.9 G 6 6 1.0 G 1.29 G E 2 2 1.0 G 2 2 1.0 G 1.51 G F 2 2 1.0 G 2 2 1.0 G 1.23 G G 1 1 1.0 G 1 1 1.0 G 1.43 G H 5 6 1.2 G 5 5 1.0 G 1.10 VG I 3 4 1.3 G 4 4 1.0 G 1.38 G J 4 4 1.0 G 4 5 1.3 G 1.34 G K 6 7 1.2 G 7 9 1.3 G 1.22 G L 5 7 1.4 G 5 6 1.2 G 1.42 G M 11 20 1.8 B 11 19 1.7 B 1.24 G N 5 6 1.2 G 6 7 1.2 G 1.33 G O 3 3 1.0 G 3 3 1.0 G 1.36 G P 5 6 1.2 G 5 5 1.0 G 1.52 G Q 8 9 1.1 G 7 8 1.1 G 1.61 G R 16 18 1.1 G 15 18 1.2 G 1.40 G S 11 12 1.1 G 10 12 1.2 G 1.28 G T 6 7 1.2 G 6 6 1.0 G 1.20 VG U 7 15 2.1 B 7 14 2.0 B 1.41 G W 16 20 1.3 G 15 19 1.3 G 1.07 VG X 22 26 1.2 G 22 23 1.0 G 1.26 G Y 22 29 1.3 G 21 28 1.3 G 1.24 G Z 27 32 1.2 G 26 32 1.2 G 1.55 G IN-FURNACE STEEL LEFT RIGHT TIME OF LEFT TYPE SIDE OF SIDE OF TEMPERATURE HEATING SIDE OF REFERENCE EXPRESSION EXPRESSION DETERMI- OF HEATING FURNACE EXPRESSION DETERMI- SYMBOL (F) CT (F) NATION FURNACE (MINUTES) (G) NATION A 489 580 768 G 1180 65 5229 G B 474 650 757 G 1250 72 4968 G C 354 510 644 G 1154 68 1968 G D 457 580 728 G 1260 72 4570 G E 467 615 734 G 1215 116 6593 G F 410 721 700 B 1322 135 3302 G G 438 741 729 B 1173 123 4026 G H 461 585 720 G 1205 95 6084 G I 450 542 740 G 1189 87 4331 G J 444 562 701 G 1221 89 3909 G K 408 715 697 B 1202 95 2649 G L 404 482 673 G 1212 165 3267 G M 400 463 692 G 1105 25 1708 G N 374 502 644 G 1295 195 2784 G O 407 631 694 G 1240 135 4004 G P 375 527 640 G 1298 201 2785 G Q 410 526 694 G 1192 120 3252 G R 432 543 727 G 1250 179 4879 G S 411 554 696 G 1232 122 3729 G T 363 523 649 G 1232 162 2630 G U 372 621 650 G 1113 20 1448 B W 387 521 686 G 1260 125 3049 G X 393 682 670 B 1180 141 3360 G Y 358 482 636 G 1280 162 2600 G Z 366 451 651 G 1260 181 2915 G
(101) TABLE-US-00010 TABLE 5-2 BEFORE HOT STAMPING AFTER HOT STAMPING STEEL LEFT LEFT SURFACE LEFT TYPE SIDE OF SIDE OF PROPERTY SIDE OF REFERENCE EXPRESSION DETERMI- EXPRESSION DETERMI- AFTER HOT EXPRESSION DETERMI- SYMBOL n1 n2 (D) NATION n1 n2 (D) NATION STAMPING (E) NATION AA 12 13 1.1 G 12 14 1.2 G 0.86 B AB 10 12 1.2 G 10 13 1.3 G 0.81 B AC 15 18 1.2 G 16 19 1.2 G 0.69 B AD 6 8 1.3 G 6 7 1.2 G 0.64 B AE 12 16 1.3 G 12 15 1.3 G 0.72 B AF 18 22 1.2 G 17 22 1.3 G 0.98 B AG 6 7 1.2 G 5 7 1.4 G 0.77 B AH 4 5 1.3 G 4 4 1.0 G 1.18 VG AI 12 15 1.3 G 12 14 1.2 G 1.16 VG AJ 17 21 1.2 G 15 21 1.4 G 1.26 G AK 12 14 1.2 G 12 13 1.1 G 1.25 G AL 2 2 1.0 G 2 2 1.0 G 1.16 VG AM 16 22 1.4 G 15 21 1.4 G X 1.26 G AN 10 12 1.2 G 10 11 1.1 G 1.19 VG AO 11 12 1.1 G 10 11 1.1 G 1.08 VG AP 7 9 1.3 G 7 8 1.1 G 1.17 VG AQ 13 14 1.1 G 14 16 1.1 G 1.08 VG AR 21 26 1.2 G 22 25 1.1 G 1.36 G AS 18 19 1.1 G 18 18 1.0 G 1.16 VG AT 15 17 1.1 G 16 16 1.0 G 1.17 VG AU 17 19 1.1 G 16 18 1.1 G 1.39 G AV 17 19 1.1 G 16 18 1.1 G 1.42 G AW 16 22 1.4 G 15 21 1.4 G X 1.25 G AX 17 19 1.1 G 16 18 1.1 G 1.43 G IN-FURNACE STEEL LEFT RIGHT TIME OF LEFT TYPE SIDE OF SIDE OF TEMPERATURE HEATING SIDE OF REFERENCE EXPRESSION EXPRESSION DETERMI- OF HEATING FURNACE EXPRESSION DETERMI- SYMBOL (F) CT (F) NATION FURNACE (MINUTES) (G) NATION AA 442 582 729 G 1210 128 3865 G AB 430 535 719 G 1236 116 3591 G AC 400 426 692 G 1210 125 2814 G AD 436 623 721 G 1210 145 3604 G AE 431 611 730 G 1152 152 4921 G AF 384 396 680 G 1198 86 2449 G AG 402 557 696 G 1209 147 3134 G AH 413 462 689 G 1209 135 2339 G AI 325 476 643 G 1260 165 2717 G AJ 420 543 696 G 1230 98 3269 G AK 435 558 687 G 1211 156 5054 G AL 481 721 777 G 1180 161 16656 G AM 248 539 546 G 1291 332 1602 G AN 401 560 667 G 1219 135 3134 G AO 396 523 673 G 1266 173 2694 G AP 443 551 724 G 1230 125 3378 G AQ 363 402 648 G 1250 140 2605 G AR 371 432 649 G 1241 192 3115 G AS 398 630 695 G 1263 191 3540 G AT 384 669 682 G 1203 203 3026 G AU 365 456 664 G 1248 192 2697 G AV 360 456 658 G 1248 192 2571 G AW 248 539 546 G 1291 332 1602 G AX 360 456 658 G 1248 192 2571 G
(102) Based on the above-described examples and comparative examples, it is found that, as long as the conditions of the present invention are satisfied, it is possible to obtain a cold-rolled steel sheet, a galvanized cold-rolled steel sheet, a galvannealed cold-rolled steel sheet, a electrogalvanized cold-rolled steel sheet, or a alluminized cold-rolled steel sheet all of which satisfy TS; 50000 MPa.Math.% even after hot stamping, and a hot-stamped steel manufactured from the obtained cold-rolled steel sheet.
INDUSTRIAL APPLICABILITY
(103) Since the cold-rolled steel sheet and the hot-stamped steel which are obtained in the present invention can satisfy TS50000 MPa.Math.% after hot stamping, the cold-rolled steel sheet and the hot-stamped steel have a high press workability and a high strength, and satisfies the current requirements for a vehicle such as an additional reduction of the weight and a more complicated shape of a component.
(104) TABLE-US-00011 Brief Description of the Reference Symbols S1: MELTING STEP S2: CASTING STEP S3: HEATING STEP S4: HOT-ROLLING STEP S5: COILING STEP S6: PICKLING STEP S7: COLD-ROLLING STEP S8: ANNEALING STEP S9: TEMPER-ROLLING STEP S10: GALVANIZING STEP S11: ALLOYING STEP S12: ALUMINIZING STEP S13: ELECTROGALVANIZING STEP