COLD ROLLED STEEL SHEET AND METHOD FOR PRODUCING COLD ROLLED STEEL SHEET Technical Field of the Invention [0001] The present invention relates to a cold rolled steel sheet having an excellent 10 formability before hot stamping and/or after hot stamping, and a method for producing the same. Priority is claimed on Japanese Patent Application No. 2012-004549, filed January 13,2012, and Japanese Patent Application No. 2012-004864, filed January 13, 2012, the content of which is incorporated herein by reference. 15 Related Art [0002] Recently, a steel shcet for a vehicle is required to be improved in terms of collision safety and to have a reduced weight. In such a situation, hot stamping (also 20 called hot pressing, hot stamping, diequenching, press quenching or the like) is drawing attention as a method for obtaining a high strength. The hot stamping refers to a forming method in which a steel sheet is heated at a high temperature of, for example, 700°C or more, then hot-formed so as to improve the formability of the steel sheet, and quenched by cooling after forming, thereby obtaining desired material qualities. As 25 described above, a steel sheet used for a body structure of a vehicle is required to have high press workability and a high strength. A steel sheet having aferrite and martensite structure, a steel sheet having a ferrite and bainite structure, a steel sheet containing retained austenite in a structure or the like is known as a steel sheet having both press worltability and high strength. Among these steel sheets, a multi-phase steel sheet 5 having martensite dispersed in a ferrite base has a low yield strength and a high tensile strength, and furthermore, has excellent elongation characteristics. However, the multi-phase steel sheet has a poor hole expansibility since stress concentrates at the interface between the ferrite and the martei~site,a nd cracking is likely to initiate from the interface. 10 [0003] For example, patent Documents 1 to 3 disclose the multi-phase steel sheet. In addition, Patent Documents 4 to 6 describe relationships between the hardness and formability of a steel sheet. [0004] 15 However, even with these techniques of the related art, it is difficult to obtain a steel sheet which satisfies the current requirements for a vehicle such as an additional reduction of weight and more complicated shapes of components. Prior Art Document 20 Patent Document [0005] [Patent Document I] Japanese Unexamined Patent Application, First PublicationNo. H6-128688 [Patent Document 21 Japanese Unexamined Patent Application, First 25 Publication No. 2000-3 19756 3 [Patent Document 31 Japanese Unexamined Patent Application, First Publication No. 2005-120436 1 [Patent Document 41 Japanese Unexamined Patent Application, First I I PublicationNo. 2005-256141 < 5 [Patent Document 51 Japanese Unexamined Patent Application, First Publication No. 2001 -355044 1 [Patent Document 61 Japanese Unexamined Patent ~ Application, First Publication No. H11-189842 10 Disclosure of the Invention Problems to be Solved by the Invention 1 [0006] ~ An object of the present invention is to provide a cold rolled steel sheet, a i :I hot-dip galvanized cold rolled steel sheet, a galvannealed cold rolled steel sheet, an 15 electrogalvanized cold rolled steel sheet, and an aluminized cold rolled steel sheet, which ! are capable of ensuring a strength before and after hot stamping and have a more favorable hole expansibility, and a method for producing the same. Meails for Solving the Problem 20 [0007] The present inventors carried out intensive studies regarding a cold rolled steel sheet, a hot-dip galvanized cold rolled steel sheet, a galvannealed cold rolled steel sheet, an electrogalvanized cold rolled steel sheet, and an aluminized cold rolled steel sheet that ensured a strength before hot stamping (before heating for carrying out quenching in a 25 hot stamping process) andlor after hot stanlping (after quenching in a hot stainping 4 process), and having an excellent formability (hole expansibility). As a result, it was found that, regarding the steel composition, when an appropriate relationship is established among the amount of Si, the amount of Mn and the amount of C, a fraction of a ferrite and a fraction of a martensite in the steel sheet are set to predetermined fractions, 5 and the hardness ratio (difference of a hardness) of the martensite between a surface part of a sheet thicltness and a central part of the sheet thicltness of the steel sheet and the hardness distribution of the martensite in the central part of the sheet thicltness are set in specific ranges, it is possible to industrially produce a cold rolled steel sheet capable of ensuring, in the steel sheet, a greater formability than ever, that is, a charactcristic of TS 10 x h 2 50000MPa.% that is a product of a tensile strength TS and a hole expansion ratio h. Furthermore, it was found that, when this cold rolled steel sheet is used for hot stamping, a steel sheet having excellent formability even after hot stamping is obtained. In addition, it was also clarified that the suppression of a segregation of MnS in the central part of the sheet thickness of the cold rolled steel sheet is also effective in improving the 15 formability (hole expansibility) of the steel sheet before hot stanlping andlor after hot ' . stamping. In addition, it was also found that, in cold-rolling, an adjustment of a fraction of a cold-rolling reduction to a total cold-rolling reduction (cumulative rolling reduction) from an uppermost stand to a third stand based on the uppermost stand within a specific range is effective in controlling a hardness of the martensite. Furthermore, the inventors 20 have found a variety of aspects of the present invention as described below. In addition, it was found that the effects are not impaired even when a hot-dip galvanized layer, a galvannealed layer, an electrogalva~~izelady er and an aluminizied layer are formed on the cold rolled steel sheet. [OOOS] 25 ( I ) That is, according to a first aspect of the present invention, a cold rolled steel 5 sheet includes, by mass%, C: 0.030% to 0.150%, Si: 0.010% to 1.000%, Mn: 1.50% to 2.70%, P: 0.001% to 0.060%, S: 0.001% to 0.010%, N: 0.0005% to 0.0100%,Al: 0.010% to 0.050%, and optionally one or more of B: 0.0005% to 0.0020%, Mo: 0.01% to 0.50%, Cr: 0.01% to 0.50%, V: 0.001% to 0.100%, Ti: 0.001% to 0.100%, Nb: 0.001% to 5 0.05076, Ni: 0.01% to 1.00%, Cu: 0.01% to 1.00%, Ca: 0.0005% to 0.0050%, REM: 0.0005% to 0.0050%, and a balance including Fe and unavoidable impurities, in which, when [C] represents an amount ofC by mass%, [Si] represents an amount of Si by mass%, and [Mn] represents an amount of Mn by mass%, a following expression (A) is satisfied, a metallographic structure before a hot stamping includes 40% to 90% of a 10 ferrite and 10% to 60% of a martensite in an area fraction, a total of an area fraction of the ferrite and an area fraction of the martensite is 60% or more, the metallographic structure may optionally further includes one or more of 10% or less of a perlite in an area fraction, 5% or less of a retained austenile in a volume ratio, and less than 40% of a bainite as a remainder in an area fraction, a hardness of the marlensite measured with a 15 nanoindenter satisfies a following expression (B) and a following expression(C) before the hot stamping, TS x h which is a product of a tensile strength TS and a hole expansion ratio h is 50000MPa.% or more, (5 x [Si] + [Mn]) / [C] > 1 l (A), H2 /HI < 1.10 (B), 20 OHM < 20 (C), and the HI is an average hardness of the martensite in a surface part of a sheet thickness before the hot stamping, the H2 is an average hardness of the marlensite in a central part of the sheet thicltness which is an area having a width of 200 pm in a thickness direction at a center of the sheet thiclmess before the hot stamping, and the 25 GHM is a variance olthe hardness of the martensite in the central part of the sheet thickness before the hot stamping. [0009] (2) In the cold rolled steel sheet according to the above (I), an area fraction of MnS existing in the cold rolled steel sheet and having an equivalent circle diameter of 0.1 5 pm to 10 pm may be 0.01% or less, and a following expression (D) may be satisfied, n2 I n1 < 1.5 (D), and the nl is an average number density pcr 10000 pn2 of the MnS having the equivalent circle diameter of 0.1 pm to 10 pm in a 114 part of the sheet thickness before the hot stamping, and the 112 is an average number density per 10000 pm2 of the MnS 10 having the equivalent circle diameter of 0.1 pm to 10 pm in the central part of the sheet i thickness before the hot stamping. 100 lo] (3) In the hot stamped steel accord~ngto the above (1) or (2), a galvanizing may be formed on a surface thereof. 15 [OOl I ] (4) According to another aspect of the present invent~ont,h ere is provided a method for producing a cold rolled steel sheet including casting a molten stecl having a chemical composition according to the above (1) and obtaining a steel, heating the steel, hot-rolling the steel with a hot-rolling mill including a plurality of stands, coiling the 20 steel after the hot-rolling, pickling the steel after the coiling, cold-rolling the steel with a cold-rolling mill including a plurality of stands after the pickling under a condition satisfying a following expression (E), annealing in which the steel is annealed under 700°C to 850°C and cooled after the cold-rolling, temper-rolling the steel after the annealing, 25 1 . 5 x r l l r + 1 . 2 x r 2 / r + r 3 / r > l . O (El, and 7 the ri (i = 1,2,3) represents an individual target cold-rolling reduction at an ith stand (i = 1,2,3) based on an uppermost stand in the plurality of stands in the cold-rolling in unit %, and the r represents a total cold-rolling reduction in the cold-rolling in unit %. 5 [OO 121 (5) The method for producing the cold rolled steel sheet according to the above (4) may further include galvanizing the steel hctween the annealing and the temper-rolling. [OO 131 10 (6) In the method for producing the cold rolled steel sheet according to the above (4), when CT represents a coiling temperature in the coiling in unit OC, [C] represents the amount of C by mass%, [Mn] represents the amount of Mn by mass%, [Si] represents the amount of Si by mass%, and [Mo] represents the amount of Mo by mass% in the steel sheet, a following expression (F) may be satisfied, 15 560 - 474 x [C] - 90 x [Mn] - 20 x [Cr] - 20 x [Mo] < CT < 830 - 270 x [C] - 90 x [Mn] - 70 x [Cr] - 80 x [Mo] (F). [00 141 (7) In the method for producing the cold rolled steel sheet according to the above (6), when T represents a heating temperature in the heating in unit OC, t represents 20 an in-furnace time in the heating in unit minute, [Mn] represents the amount of MII by mass%, and [S] represents an amount of S by mass% in the steel sheet, a following expression (G) may be satisfied, T x ln(t) l(l.7 [Mn] + [S]) > 1500 (G). [OO 1 51 25 (8) That is, according to a first aspect of the present invention, there is provided 8 a cold rolled steel sheet including, by mass%, C: 0.030% to 0.150%, Si: 0.010% to 1.000%, Mn: 1.50% to 2.70%, P: 0.001% to 0.060%, S: 0.001% to 0.010%, N: 0.0005% to 0.0100%, AI: 0.010% to 0.050%, and optionally one or more of B: 0.0005% to 0.0020%, Mo: 0.01% to 0.50%, Cr: 0.01% to 0.50%, V: 0.001% to 0.100%, Ti: 0.001% 5 to 0.100%, Nb: 0.001% to 0.050%, Ni: 0.01% to 1.00%, Cu: 0.01% to 1.00%, Ca: 0.0005% to 0.0050%, REM: 0.0005% to 0.0050%, and a balance including Fe and unavoidable impurities, in which, when [C] represents an amount of C by mass%, [Si] represents an amount of Si by mass%, and [Mn] represents an amount of Mn by mass%, a following expression (13) is satisfied, a metallographic structure after a hot stamping 10 includes 40% to 90% of a ferrite and 10% to 60% of amattensite in an area fraction, a total of an area fraction of the ferrite and an area fraction of the martensite is 60% or more, the metallographic structure may optionally further includes one or more of 10% or less of a perlite in an area fraction, 5% or less of a retained austenite in a volume ratio, and less than 40% of a bainite as a remainder in an area fraction, a hardness of the 15 martensite measured with a nanoindenter satisfies a following expression (I) and a following expression(J) after the hot stamping, TS x h which is a product of a tensile strength TS and a hole expansion ratio h is 50000MPa.% or more, (5 x [Si] + [Mn]) / [C] > 11 (H), H21 /HI1 < I.lO(I), 20 oHM1 < 20 (J), and the H11 is an average hardness of the marlensite in a surface part of a sheet thickness after the hot sta~npingt,h e H21 is an average hardness of the mattensite in a central pa~otf the sheet thickness which is an area having a width of 200 pm in a thiclu~essd irection at a center of the sheet thickness afler the hot stamping, and the 25 oWM1 is a variance ofthe average hardness of the marlensite in the central part of the 9 sheet thickness after the hot stamping. 100 161 (9) In the cold rolled steel sheet for the hot stamping according to the above (8), an area fraction of MnS existing in the cold rolled steel sheet and having an equivalent 5 circle diameter of 0.1 pm to 10 pm may be 0.01% or less, and a following expression (K) may be satisfied, n21 / 1111 < 1.5 (K), and the 1111 is an average number density per 10000 pm2 of the MnS having ihe equivalent circle diameter of 0.1 prn to 10 pm in a 114 part of the sheet thickness after the 10 hot stamping, and the 1121 is an average number density per 10000 pm2 of the MnS having the equivalent circle diameter of 0.1 pm to 10 pin in the central part of the sheet thickness after the hot stamping. 1001 71 (10) In the cold rolled steel sheet for the hot stamping according to the above (8) 15 or (9), a hot dip galvanizing may be formed on a surface thereof. [0018] (11) In the cold rolled steel sheet for the hot stamping according to thc above (lo), a galvannealing may be formed on a surface of the hot dip galvanizing. [0019] 20 (12) In the cold rolled steel sheet for the hot stamping according to the above (8) or (9), an clectrogalvanizing may be formed on a surface thereof. [0020] (1 3) In the cold rolled steel sheet for the hot stamping according to the above (8) or (9), an aluminizing may be formed on a surface thereof. 25 [002 11 10 (14) According to another aspect of the present invention, there is provided a method for producing a cold rolled steel sheet including casting a molten steel having a chemical composition according to the above (8) and obtaining a steel, heating the steel, hot-rolling the steel with a hot-rolling mill including a plurality of stands, coiling the 5 steel after the hot-rolling, pickling the steel aAer the coilmg, cold-rolling the steel with a 2 cold-rolling mill including a plurality of stands after the pickling under a condition satisfying a following expression (L), annealing in which the steel is annealed under 700°C to 850°C and cooled after the cold-rolling, and temper-rolling the steel after the annealing, 10 1.5 x r l / r + 1 . 2 x r 2 / r + r 3 / r > l (L), and the ri (i = 1,2,3) represents an individual target cold-rolling reduction at an ith stand (i = 1,2,3) based on an uppermost stand in the plurality of stands in the cold-rolling in unit %, and the r represents a total cold-rolling reduction in the cold-rolling in unit %. 15 [0022] (15) In the method for producing the cold rolled steel sheet ihr the hot stamping according to the above (14), when CT represents a coiling temperature in the coiling in unit "C, LC] represents the amount of C by mass%, [Mn] represents the amount of Mn by mass%, [Si] represents the amount of Si by mass%, and wo] represents the amount of 20 Mo by mass% in the steel sheet, a following expression (M) may be satisfied, 560 - 474 x [C] - 90 x [Mn] - 20 x [Cr] - 20 x [Mo] < CT < 830 - 270 x [C] - 90 x [Mn] - 70 x [Cr] - 80 x [Mo] (M). 100231 (1 6) In the method for producing the cold rolled steel sheet for the hot stamping 25 according to the above (15), when T represents a beating temperature in the heating in 11 unit "C, t represents an in-furnace time in the heating in unit minute, [Mn] represents the amount of Mn by mass%, and [S] represents an amount of S by mass% in the steel sheet, a following expression (N) may be satisfied, T x In(t) / (1.7 x [Mn] + [SJ) > 1500 (N) . 5 [0024] (1 7) The producing method according to any one of the above (14) to (16) may further include galvanizing the steel between the amlealing and the temper-rolling. [0025] (18) The producing method according to the above (17) may hrthe~i.n clude 10 alloying the steel between the galvanizing and the temper-rolling. [0026] (19) The producing method according to any one of the above (14) to (16) may further include elechogalvanizing the sleel after the temper-rolling. [0027] 15 (20) The producing method according to any one of the above (14) to (16) may further include aluminizing the steel between the annealing and the temper-rolling. The hot stamped steel obtained by using tlle steel sheet any one of (I) to (20) has an excellent formability. Effects of the Invention 20 [002S] According to the present invention, since an appropriate relationship is established among the amount of C, the amount of Mn and the amount of Si, and the hardness of the martensite measured with a llanoindenter is set to an appropriate value, it is possible to obtain a more favorable hole expansibility before hot stamping and/or after 25 hot stamping in the hot stamped steel Brief Description of the Drawings [0029] FIG. 1 is a graph illustrating the relationship between (5 x [Si] + [Mn]) / [C] and 5 TS x h before hot stamping and after hot stamping. FIG. 2A is a graph illustrating a foundation of an expression (B) and is a graph illustrating the relationship between H2 / HI and a OHM before hot stamping and the relationship between 821 / H11 and 01-1M1 after hot stamping. FIG 2B is a graph illustrating a foundation of an expression (C) and is a graph 10 illustrating the relationship between the OHM and TS x h before hot stamping and the relationship between oHM1 and TS x h after hot stamping. FIG. 3 is a graph illustrating the relationship between n2 / nl and TS x h before hot stamping and the relationship between n21/ n l l and TS x h after hot stamping, and illustrating a foundation of an expression (D). 15 FIG. 4 is a graph illustrating the relationship between 1.5 x rl / r + 1.2 x r2 / r + r3 /rand H2 / H1 before hot stamping and the relationship between 1.5 x rl / r + 1.2 x r2 / 2 + r3 / r and H21 / HI 1 after hot stamping, and illustrating a foundation of an expression (E). FIG. 5A is a graph illustrating the relationship between an expression (F) and a 20 fraction of a martensite. FLG. 5B is a graph illustrating the relationship between the expression (F) and a fraction of a pearlite. FIG. 6 is a graph illustrating the relationship between T x lii(t) / (1.7 x [Mn] + [S]) and TS x h, and illustrating a foundation of an expression (G). 25 FIG. 7 is a perspective view of a hot stamped steel used in an exanlple. 13 FIG. 8A is a flowchart illustrating a method for producing the cold rolled steel sheet according to a11 embodiment of the present invention. FIG. 8B is a flowchart illustrating a method for producing the cold rolled steel sheet after hot stamping according to another embodiment of the present invention 5 Embodiments of the Invention [0030] 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 10 appropriate hardness to a martensite in a predetermined position in a steel sheet in order to improve formability (hole expansibility). Thus far, there have been no studies regarding the relationship between the formability and the hardness of the martensite in a steel sheet before hot stamping or after hot stamping. [003 11 15 Herein, reasons for limiting a chemical composition of a cold rolled steel sheet before hot stamping according to an embodiment of the present invention (in some cases, also referred to as a colt1 rolled steel sheet before hot stamping according to the present embodiment), a cold rolled steel sheet after hot stamping according to an embodiment of the present invention (in some cases, also referred to as a cold rolled steel sheet after hot 20 stamping according to the present embodiment), and steel used for manufacture thereof will be described. Hereinafter, "%" that is a unit of an amount of an individual component indicates "mass%. [0032] C: 0.030% to 0.150% 25 C 1s an important element to stre~lgthenth e martensite and increase the strength 14 of the steel. When the amount of C is less than 0.030%, it is not possible to sufficiently illcrease the strength of the steel. On the other hand, when the amount of C exceeds 0.150%, degradation of the ductility (elongation) of ihe steel becomes significant. Therefore, the range ofthe amount of C is set to 0.030% to 0.150%. In a case in which 5 there is a demand for high hole expansibility, the amount of C is desirably set to 0.100% or less. [0033] Si: 0.010% to 1.000% Si is an important element for suppressing a formation of a harmful carbide and 10 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 also degrades. 'Therefore, the amount of Si is set to 1.000% or less. In addition, while the Si is added for deoxidation, a deoxidation effect is not sufiicient 15 when the amount of Si is less than 0 010%. Therefore, the amount of Si is set to 0.010% or more. Al: 0.010% to 0.050% Al is an important element as a deoxidizing agent. To obtain the deoxidation 20 effect, the amount ofAl is set to 0.010% or more. On the other hand, even when the Al is excessively added, the above-described effect is saturated, and conversely, the steel becomes brittle. Therefore, the amount ofAl is set in a range of 0.010% to 0.050%. [0035] Mn: 1.50% to 2.70% 25 Mn is an important element for increasing a hardenability of the steel and 15 strengthening the steel. However, when the amount of Mn is less than 1.50%, it is not possible to sufficiently increase the strength of the steel. On the other hand, when the amount of Mn exceeds 2.70%, since the hardenability increases more than necessary, an increase in the strength of the steel is caused, and consequently, the elongation or hole 5 expansibility of the steel degrades. Therefore, the amount of Mn is set in a range of 1.50% to 2.70%. In a case in which there is a demand for high elongation, the amount of Mn is desirably set to 2.00% or less. [0036] P: 0.001% to 0.060% 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 increasing in the cost of refining, the amount of P is desirably set to 0.001 % or more. [0037] S: 0.001% to 0.010% S is an element that forms MnS and significantly deteriorates the local ductility or weldability of the stccl. Therefore, the upper limit of the amount of S is set to 0.010%. In addition, in order to reduce refining costs, a lower limit of the amount of S is desirably set to 0.001%. 20 [0038] N: 0.0005% to 0.0100% N is an important element to precipitate AIN and the like and miniaturize crystal grains. However, when the amount of N exceeds 0.0100%, aN solid solution (nitrogen solid solution) remains and the ductility of the steel is degraded. Therefore, the amount 25 of N is set to 0.0100% or less. Due to a problem of refining costs, the lower limit of the 16 amount ofN is desirably set to 0.0005%. [0039] The cold rolled steel sheet according to the embodiment has a basic composition including the above-described components, Fe as a balance and unavoidable impurities, 5 but may further contain any one or more elements of 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 equal to or less than the below-described upper limits to improve the strength, to control a shape of a sulfide or an oxide, and the like. Since these chemical elements are not necessarily added to the steel sheet, the lower limits thereof are 0%. [0040] Nb, Ti and V are elements that precipitate a fine carbonitride and strengthen the steel. In addition, Mo and Cr are elements that increase hardenability and strengthen the steel. To obtain these effects, it is desirable to contain 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. 15 However, even when Nb: more than 0.050%, Ti: more than 0.100%, V: more than 0.100%, Mo: more than 0.50%, and Cr: more than 0.50% are contained, the strength-increasing effcct is saturated, and there is a concern that the degradation of the elongation or the hole expansibility may be caused. [0041] 20 The steel may further contain Ca in a range of 0.0005% to 0.0050%. Ca controls the shape of the sulfide or the oxide and improves the local ductility or hole expansibility. To obtain this effect using Ca, it is preferable to add 0.0005% or more of Ca. However, since there is a concern that an excessive addition may deteriorate worltability, the upper limit of the amount of Ca is set to 0.0050%. For the same reason, 25 for the rare earth metal (REM) as well, it is preferable to set the lower limit of the amount 17 to 0.0005% and an upper limit of the amount to 0.0050%. 100421 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, 10 and there is a concern that the ductility may degrade. [0043] 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, 15 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-describetl lower limits, the elements are treated as unavoidable impurities. [0044] 20 In addition, in the cold rolled steel sheet according to the embodiment, as illustrated in FIG. 1, when the amount of C (mass%), the amount of Si (mass%) and the amount of Mn (mass%) are represented by [C], [Si] and [Mn] respectively, it is important to satisfi a following expression (A) ( (H) as well). (5 x [Si]+ [Mn])/ [C]> 11 (A) 25 When the above expression (A) is satisfied before hot stamping andlor after hot 18 stamping, it is possible to satisfy a condition of TS x h ? 50000Wa%. When the value of (5 x [Si] + [Mnj) / [Cj is 11 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, the hardness difference (ratio of tl~eha rdness) between the hard 5 phase and a soit phase becomes great, and therefore the h value deteriorates, and, when the amount of Si or the amount of Mn is small, TS becomes low. [0045] 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 10 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 part of a sheet thiclcness and a central part of the sheet thickness, and the hardness distribution of the martensite in the central part of the sheet thickness are in a predeterniined state in a phase of before hot stamping, the state is almost maintained even after quenching in a hot 15 stamping process as illustrated in FIGS. 2A and 2B, and the forniability such as elongation or hole expansibility becomes favorable. This is considered to be because the hardness distribution of the martensite formed beihre hot stamping still 11;rs a significant effect even after hot stan~pinga, ud alloy elements concentrated in the central part of the sheet thickness still hold a state of being concentrated in the central part of the 20 sheet thickness even after hot stamping. That is, in the steel sheet before hot stamping, in a case in which the hardness ratio between the martensite in the surface part of the sheet thickness and the martensite in the central part of the sheet thickness is great, or a variance of the hardness of the martcnsite is great, the same tendency is exhibited even after hot sta~nping. As illustrated in FIGS. 2A and 2B, the hardness ratio between the 25 surface part of the sheet thickness and the central part of the sheet thickness in the cold 19 rolled steel sheet according to the embodiment before hot stamping, and the hardness ratio between the surface part of the sheet thickness and the central part of the sheet thickness in the steel sheet obtained by hot stamping the cold rolled steel sheet according to the embodiment, are almost the same. In addition, similarly, the variance of the hardness of the martensite in the central part of the sheet thickness in the cold rolled steel sheet according to the embodiment before hot stamping, and the variance of the hardness of the martensite in the central part of the sheet thickness in the steel sheet obtained by hot stamping the cold rolled steel sheet according to the embodiment, are almost the same. Therefore, the formability of the steel sheet obtained by hot stamping the cold rolled steel sheet according to the embodiment is similarly excellent to the formability of the cold rolled steel sheet according to the embodiment before hot stamping. [0046] In addition, regarding the hardness of the martensite measured with an nanoindenter manufactured by Hysitron Corporation at a magnification of 1000 times, it is found in the present invention that a following expression (B) and a following expression (C) ((I) and (J) as well) being satisfied before hot stamping and/or after hot stamping are advantageous to the formability of the steel sheet. Here, "111" is the average hardness ofthe martensite in the surface part of the sheet thickness that is within an area having a width of 200 pm in a thickness direction from an outermost layer of the steel sheet in the thickness direction in the steel sheet behre hot stamping, "H2" is the average hardness of the martensite in an area having a width of 1100 pm in the thicltness direction from the central part of the sheet thickness in the central part of the sheet thickness in the steel sheet before hot slamping, and "OHM is the variance of the hardness of the martensite in an area having a width of &I00 pm in the thickness direction from the central part of the sheet thiclmess before hot stamping. In addition, 20 "H11" is the hardness of the martensite in the surface part of the sheet thickness in the cold rolled steel sheet for hot stamping after hot stamping, "H21" is the hardness ofthe martensite in the central part of the sheet thickness, that is, in an area having a width of ,I 200 pm in the thiclcness direction in a center of the sheet thickness afier hot stamping, i 5 and "oHM1" is the variance of the hardness of the martensite in the central par1 of the sheet thickness after hot stamping. The HI, H11, H2, H21, OHM and oNMl are obtained respectively from 300-point measurements for each. An area having a width of *lo0 pm in the thickness direction from the central part of the sheet thickness refers to an area having a center at the center of the sheet thickness and having a dimension of 200 10 pm in the thickness direction. H2/H1<1.10 (B) I I i o m < 20 iC) H21 /HI1 1500 (G) When T x ln(t) / (1.7 x [Mn] + [S]) is equal to or less than 1500, the area fraction of the MnS having the equivalent circle diameter of 0.1 pm to 10 pm becomes 15 large, and there is a case in which a diKerence between the number density of the MIIS having the equivalent circle diameter of 0.1 pm to 10 pm in the 114 part ofthe sheet thickness and the number density of the MnS having the equivalent circle diameter of 0.1 pm to 10 pm in the central part of the sheet thickness becomes large. The temperature of the heating fumace before carrying out hot-rolling refers to an extraction temperature 20 at an outlet side of the heating furnace, and the in-furnace time refers to a time elapsed from an insertion of the slab into the hot heating fumace to an extraction of the slab from the heating furnace. Since the MIIS does not change even after hot stamping as described above, it is preferable to satisfy the expression (G) or the expression (N) in a heating process before hot-rolling. 25 [0060] 28 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 slab at the finishing temperature (the hot-rolling end temperature) which is set in a range of an Ar3 temperature to 97OoC. When the finishing temperature is less than the AT3 temperature, the hot-rolling becomes 5 a (a + y) 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 teluperature exceeds 970°C, an austenite grain size coarsens, and the fraction of the ferrite becomes small, and thus, there is a concern that the elongation may degrade. Allot-rolling Facility may have a plurality of stands. 10 Here, the AT, temperature was estimated from an inflection point of a length of a test specimen after carrying out a formastor test. [0061] After the hot-rolling, the steel is cooled at an average cooling rate of 20 "Clsecond to 500 'Clsecond, and is coiled at a predetermined coiling temperature CT. 15 In a case in which the average cooling rate is less than 20 "Clsecond, the pearlite that causes the degradation of the ductility is likely to he formed. On the other hand, an upper limit of the cooling rate is not particularly specified and is set to approximately 500 "Clsecond in consideration of a facility specification, but is not limited thereto. [0062] 20 After the coiling, pickling is carried out, and cold-rolling is carried out. At this time, to obtain a range satisfying the above-described expression (C) as illustrated in FIG. 4, the cold-rolling is carried out under a condition in which a following expression (E) ((I,) as well) is satisfied. When conditions for annealing, cooling and the like described below are further satisfied afier the above-described rolling, TS x h > 50000 MPa.% is 25 ensured before hot stamping andlor afier hot stamping. The cold-rolling is desirably 29 carried out with a tandem rolling mill in which a plurality of rolling mills are linearly disposed, and the steel sheet is continuously rolled in a single direction, thereby obtaining a predetermined thickness. 1.5 x r l / r + 1 . 2 x r 2 / r + r 3 l r > 1 . 0 (El 5 Here, the "ri" represents an individual target cold-rolling reduction (%) at an i"' stand (i = 1,2,3) from an uppermost stand in the cold-rolling, and the "r" represents a total target cold-rolling reduction (Oh) in the cold-rolling. The total cold-rolling r 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 (a difference between the 10 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. 100631 When the cold-rolling is carried out under the conditions in which the expression (E) is satisfied, it 1s possible to sufficiently divide the pearlite in the 15 cold-rolling even when a large pearlite exists before the cold-rolling. As a result, it is possible to burn the pearlite or suppress the area fraction of the pearlite to a minimum through the annealing carried out after cold-rolling, and therefore it becomes easy to obtain a structure in which an expression (B) and an expression (C) are satisfied. On the other hand, in a case in which the expression (E) is not satisfied, the cold-rolling 20 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. 111 addition, the inventors found that, when the expression (E) is satisfied, an obtained form of the martensite structure after the annealing is ~naintainedin almost the same state even after hot stamping is carried out, and therefore the cold rolled steel sheet according to the 25 embodiment becomes advantageous in terms of the elongation or the hole expansibility 30 even after hot stamping. In a case in which the hot stamped steel for which the cold rolled steel sheet for hot stamping according to the embodiment is used is heated up to the two-phase region in the hot stamping, a hard phase including the martensite hefore hot stamping turns into an austenite structure, and the ferrite before hot stamping remains 5 as it is. Carbon (C) in the austenite does not move to the peripheral ferrite. Mer that, when cooled, the austenite turns into a hard phase including the marlensite. That is, when the expression (E) is satisfied and the above-described I32 / Hl is in a predetermined range, the H2 / H1 is maintained even after hot stamping and the formability becomes excellent after hot stamping. 10 [0064] In the embodiment, r, rl, 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 15 reduction is uiinecessarily 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 embodin~etil is carried out when the actual cold-rolling reduction satisfies the expression (E). Furthermore, the actual cold-rolling reduction is preferably within *lo% of the target cold-rolling 20 reduction. ! [0065] 1 I After cold-rolling, a recrystallization is caused in the steel sheet by carrying out the annealing. In addition, in a case that hot-dip galvaniziug or gaivannealing is formed to improve the rust-preventing capability, a hot-dip galvanizing, or a hot-dip galvanizing 25 and alloying treatment is performed on the steel sheet, and then, the steel sheet is cooled 3 1 with a conventional method. The annealing and the cooling 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 5 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 a 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 x h. Other annealing temperature conditions are not particularly specified, but a 10 holding time at 700°C to 850°C is preferably I second or more as long as the productivity is not impaired to reliably obtain a predetermined structure, and it is also preferable to appropriately determine a temperature-increase rate in a range of 1 "Cisecond to an upper limit of a facility capacity, and to appropriately determine the cooling rate in a range of 1 "Clsecond to the upper limit of the facility capacity. In a 15 temper-rolling process, temper-rolling is carried out with a conventional method. An .. 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 llrc shape of the steel sheet can be corrected. [0066] 20 As a still more preferable condition of the present invention, when the amount of C (mass%), the amount of Mn (mass%), the amount of Si (mass%) and the amount of Mo (mass%) of the steel are represented by [C], [Mn], [Si] and [Mo] respectively, regarding the coiling temperature CT, it is preferable to satisfy a following expression (F) ((M) as well). 25 560 - 474 x [C] - 90 x [MI] - 20 x [Cr] - 20 x [Mo] < CT < 830 - 270 x [C] - 90 32 x [Mn] - 70 x [Cr] - 80 x [Mo] (F) [0067] As illustrated in FIG. 5A, when the coiling temperature CT is less than "560 - 474 x [C] - 90 x [Mn] - 20 x [Cr] - 20 x [Mo]", the martensite is excessively formed, the steel sheet becomes too hard, and there is a case in which the following cold-rolling becomes difficult. On the other hand, as illustrated in FIG. 5B, when the coiling temperature CT exceeds "830 - 270 x [C] - 90 x [Mn] - 70 x [Cr] - 80 x [Mo]", a banded structure of the ferrite and the pearlite is likely to be formed, and furthermore, a fraction of the pearlite in the central part of the sheet thickness is likely to increase. 'Therefore, a uniformity of a distribution of the martensite formed in the following annealing degrades, and it becomes difficult to satisfy the above-described expression (C). In addition, there is a case in which it becomes difficult for the martensite to be formed in a sufficient amount. [0068] When the expression (F) is satisfied, the ferrite and the hard phase have an ideal distribution form as described above In this case, when a two-phase region heating is carried out in thc hot stamping, the distribution form is maintained as described above. If it is possible to more reliably ensure the above-described metallographic structure by satisfying the expression (F), the metallographic structure is maintained even after hot stamping, and the formability becomes excellent after hot stamping. LO0691 Furthermore, to improve a rust-preventing capability, it is also preferable to include a hot-dip galvanizing process iu which a hot-dip galvanizing is formed between an annealing process and the temper-rolling process, and to form the hot-dip galvanizing on a surface of the cold rolled steel sheet. Furthermorc, it is also preferable lo include 33 an alloying process in which an alloying treatment is performed after the hot-dip galvanizing. 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 a sheet surface such as water vapor, thereby thickening an oxidized film may be further carried 5 out on the surface. [0070] It is also preferable to include, for example, an electrogalvanizing process in which an electrogalvanizing is formed after the temper-rolling process as well as the hot-dip galvanizing and the galvannealing and to form an electrogalvanizing on the 10 surface of the cold rolled steel sheet. In addition, it is also preferable to include, instead of the hot-dip galvanizing, an aluminizing process in which an aluminizing is formed between the annealing process and the temper-rolling process, and to form the alumi~iizingo n the surface ofthe cold rolled steel sheet. The aluminizing is generally hot dip aluminizing, which is preferable. 15 [007 11 After a series of the above-described treatments, the hot stamping is carried out as necessary. In the hot stamping process, the hot stamping is desirably carried out, for example, under the following condition. First, the steel sheet is heated up to 700°C to 1000°C at the temperature-increase rate of 5 "Clsecond to 500 'Clsecond, and ihe hot 20 stamping (a hot stamping process) is carried out after the holding time of 1 second to 120 seconds. To improve the formability, the heating temperature is preferably an Ac1 temperature or less. The Ac) temperature was estimated from the inflection point of the length of the test specimen after carrying out the formastor test. Subsequently, the steel sheet is cooled, for example, to the room temperature to 300°C at the cooling rate of 10 25 "Clsecond to 1000 "Clsecond (quenching in the hot stamping). 34 [0072] When the heating temperature in the. hot stamping process is less than 70OoC, 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 5 becomes too soft, and, in a case in which a plating, particularly zinc plating, is formed on the surface of the steel sheet, and the 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 1 OOO°C. 'when the temperature-increase rate is less than 5 "Clsecond, since it is difficult to control heating in the hot stamping, and the 10 productivity significantly degrades, it is preferable to carry out the heating at the temperature-increase rate of 5 "Clsecond or more. On the other hand, an upper limit of the temperature-lncrease rate of 500 'Clsecond depends on a current heating capability, but is not necessary to limit thereto. When the cooling rate is less than 10 "Clsecond, since the rate control of the cooling after hot stamping is difficult, and the productivity 15 also significantly degrades, it is preferable to carry out the cooling at the cooling rate of'. 10 "Clsecond or more. An upper limit of the cooling rate of 1000 "Clsecond depends on a current cooling capability, but is not necessary to limit thereto. Areason 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 20 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 galvanizing or the like is formed on the surface of the steel sheet. A reason for setting the cooling temperature to the room temperature to 300°C is to sufficiently ensure the marlensite and ensure the strength after hot stamping. 25 FIG. 8A and FIG. 8B are flowcharts illustrating the method for producing the 3 5 cold rolled steel sheet according to the embodiment of the present invention. Reference signs S1 to S13 in the drawing respectively correspond to individual process described above. [0073] 5 In the cold rolled steel sheet 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 TS x h > 50000MPa.% even after hot stamping is carried out [0074] 10 As described above, when the above-described conditions are satisfied, it is possible to manufacture the steel sheet 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 before hot stamping andlor after hot stamping can be obtained. 15 Examples [0075] Steel having a composition described in Table 1 was continuously cast at a casting rate of 1.0 dminute to 2.5 ndminute, a slab was heated in a heating furnace under a conditions shown in Table 2 with an conventional method as it is or after cooling 20 the steel 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 1. After that, pickling was carried out so as to remove a scale on a surface of the steel sheet, and a sheet thicliness was made to be 1.2 mnl to 1.4 mm through cold-rolling. At this time, the cold-rolling 25 was carried out so that the value of the expression (E) or the expression (L) became a 36 value described in Table 5. After cold-rolling, annealing was carried out in a continuous amlealing furnace at an annealing temperature described in Table 2. On a part of the steel sheets, a galvanizing was further formed in the middle of cooling after a soaking in the continuous annealing furnace, and then an alloying treatment was further performed 5 on the part of the steel sheets, thereby for~ninga galvannealing. In addition, an electrogalvanizing or an aluminizing was formed on the part of the steel sheets. Furthermore, temper-rolling was carried out at a11 elongation ratio of 1% according lo an conventional method. In this state, a sample was taken to evaluate material qualities and the like before hot stamping, and a material quality test or ihe like was carried out. 10 After that, to obtain a hot stamped steel having a form as illustrated in FIG. 7, hot stamping in which a temperature was increased at a temperature-increase rate of LO "C/second to 100 "C/second, the steel sheet was held at 780°C for 10 seconds, and the steel sheet was cooled at a cooling rate of 100 "C/second to 20OoC or less, was carried out. A sample was cut from a location of FIG. 7 in an obtained hot stamped steel, the 15 material quality test and the like were carried out, and the tensile strength (TS), the elongation (El), the hole expansion ratio (1) and the l~kwe ere obtained. The results are described in Table 2, 'l'rlble 3 (continuation ofTable 2), Table 4 and Table 5 (continuation of Table 4). The hole expansion ratios h in the tables were obtained from a ibllowing expression (P). 20 h (%) = {(d' - d) / d) x 100 (PI d': a hole diameter when a crack penetrates the sheet thicltness d: an initial hole diameter Furthermore, regarding plating types in Table 2, CR represents a non-plated, that is, a cold rolled steel sheet, GI represents that the hot-dip galvanizing is fonned on the 25 cold rolled steel sheet, GA represents that the galvanllealing is formed on the cold rolled 37 steel sheet, EG represents that the electrogalvanizing is formed on the cold rolled steel sheet. Furthermore, dcterminations G and B in the tables have the following meanings. G: a target condition expression is satisfied. 5 B: the target condition expression is not satisfied. In addition, since the expression (H), the expression (I), the expression (J), the expression (K), the expression (L), the expression (M), and the expression (N) are substantially the same as the expression (A),the expression (B), the expression (C), the expression (D), the expression (E), the expressio~(tF ), the expression (G), respectively, in 10 headings of the respective tables, the expression (A),the expression (B), the expression (C), the expression (D), the expression (E), the expression (F), and the expression (G), are described as representatives. [0076] [Table 11 15 [0077] [Table 21 [00781 20 [Table 31 [0079] [Table 41 25 [OOSO] [Table 51 [OOS 1] [Table 61 [0082] [Table 71 [0083] [Table 81 [0084] [Table 91 15 [0085] Based on the above-described examples, as long as the conditions of the present invention are satisfied, it is possible to obtain an excellent cold rolled steel sheet, an excellent hot-dip galvanized cold rolled steel sheet, an excellent galvanllealed cold rolled steel sheet, all of which satisfy TS x h 2 50000 MPa%, before hot stamping andlor after 20 hot stamping. Industrial Applicability [0086] Since the cold rolled steel sheet, the hot-dip galvanized cold rolled steel sheet, 25 and the galvannealed cold rolled sleel sheet, which are obtained in the present invention 39 and satisfy TS x h 2 50000 MPa% before hot stamping and after hot stamping, the hot stamped steel has 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 5 Brief Description of the Reference Symbols [0087] S 1 : MELTING PROCESS S2: CASTING PROCESS 10 S3: HEATING PROCESS S4: HOT-ROLLING PROCESS S5: COILING PROCESS S6: PlCKLlNG PROCESS S7: COLD-ROLLING PROCESS 15 S8: ANNEALING PROCESS S9: TEMPER-ROLLING PROCESS S10: GALVAhIIZING PROCESS S 1 1 : KLOYING PROCESS S 12: ALUMINIZING PROCESS 20 S 13: ELECTROGALVANIZING PROCESS Table 1 Table 2 Steel type reference symbol Test reference symbol Anneal~ng temperature ?C) Pearlite area fraction before cold rolling (%) After annealing and temper-rolling and before hot stamping Bainite area fraction (s;l) TS (Mpa) Pearlite area fraction (%) Ferrite area fraction (%I EL (%) Martensite area fraction (%) TS EL Ferrite + mariensite area faction (%) Residual austenite fraacretiao n (%) Table 3 Table 4 Table 5 r After hot stamping Table 6 c Left c Leff side of .: type side of . expression .G reference expression E m (6) c symbol (8) % after hot 2 0 stamping Left side of expression (C) 1 Left side of 1 4 ex~ression .G stamping Area fraction of MnS of 0.1 m or more before hot stamping (96) -0.010 0.008 0.006 0.007 0.009 0.002 0.003 0.004 0.006 0.007 0,008 0.006 0.006 0.009 0.004 0.006 0.003 0.002 0.005 0.004 0.005 Area fraction of MnS of 0.1 ll m or more after hot stamping (%) o.010 0.008 0.006 0.007 0.009 0.002 0.003 0.004 0.006 0.007 0.007 0.006 0.006 0.008 0.004 0.006 0.003 0.002 0.005 ., 0.005 0.005 9 LI 9 CLAIMS 1. A cold rolled steel sheet comprising, by mass%: C: 0.030% to 0.150%; 5 Si: 0.01 0% to 1.000%; Mn: 1.50% to 2.70%; P: 0.001% to 0.060%; S: 0.001% to 0.010%; N: 0.0005% to 0.0100%; 10 Al: 0.010% to 0.050%, and optionally one or more of B: 0.0005% to 0.0020%; Mo: 0.01% to 0.50%; Cr: 0.01% to 0.50%; 15 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%; 20 Ca: 0.0005% to 0.0050%; REM: 0.0005% to 0.0050%, and a balance including Fe and unavoidable impurities, wherein when [C] represents an amount of C by mass%, [Si] represents an atnoun1 of Si by mass%, and [Mn] represents an amount of MII by mass%, a following expression (A) 25 is satisfied, a metallographic structure before a hot stamping includes 40% to 90% of a ferrite and 10% to 60% of a martensite in an area fraction, a total of an area fraction of the ferrite and an area fraction of the martensite is 60% or more, 5 the metallographic structure optionally further includes one or more of 10% or less of a perlite in an area fraction, 5% or less of a retained austenite in a volume ratio, and less than 40% ofa bainite as a remainder in an area fraction, a hardness of the martensite measured with a nanoindenter satisfies a following expression (B) and a following expression(C) before the hot stamping, 10 TS x h which is a product of a tensile strength TS and a hole expansion ratio h is 50000MPa-% or more, (5 x [Si] + [Mn]) / [C] > 11 (A), H2 / H1 I 1.10 (B), and oI3M < 20 (c), 15 where the H1 is an average hardness of the martensite in a surface part of a sheet thickness before the hot stamping, the H2 is an average hardness of the martensite in a central part of the sheet thickness which is an area having a width of 200 pni in a thickness direction at a center of the sheet thickness before the hot stamping, and the OHM is a variance of the hardness of the martensite in the central part of the sheet 20 thickness before the hot stamping. 2. The cold rolled steel sheet according to claim 1, wherein an area fraction of MnS existing in the cold rolled steel sheet and having an equivalent circle diameter of 0.1 pm to 10 pm is 0.01% or less, 25 a following expression (D) is satisfied, n2/n1<1.5 (D), where the nl is an average number density per 10000 pln2 of the MnS having the equivalent circle diameter of 0.1 pm to 10 pm in a 114 part of the sheet thickness before the hot stamping, and the n2 is an average number density per 10000 pm2 of the 5 MnS having the equivalent circle diameter of 0.1 pm to 10 pm in the central part of the sheet thickness before the hot stamping. 3. The cold rolled steel sheet according to claim 1 or 2, whereln a galvanizing is formed on a surface thereof. 10 1 4. Amethod for producing a cold rolled steel sheet, the method comprising: casting a molten steel having a chemical composition according to claim 1 and obtaining a steel; heating the steel; 15 hot-rolling the steel with a hot-rolling mill including a plurality of stands; coiling the steel after the hot-rolling; pickling the stccl after the coiling; cold-rolling the steel with a cold-rolling mill including a plurality of stands after the pickling under a condition satisfying a following expression (E); 20 annealing in which the steel is annealed under 700°C to 850°C and cooled after the cold-rolling; temper-rolling the steel after the annealing; 1.5 x r l / r i - 1 . 2 x r 2 / r + r 3 / r > l . O (E), and the ri (i = 1,2,3) represents an individual target cold-rolling reduction at an ith 25 stand (i = 1,2,3) based on an uppermost stand in the plurality of stands in the cold-rolling in unit %, and the r represents a total cold-rolling reduction in the cold-rolling in unit %. 5. The method for producing the cold rolled steel sheet according to claim 4, 5 further comprising: galvanizing the steel between the annealing and the temper-rolling 6. The method for producing the cold rolled steel sheet according to claim 4, wherein 10 when CT represents a coiling temperature in the coiling in unit OC, [C] represents the amount of C by mass%, [Mn] represents the amount of MII by mass%, [Si] represents the amount of Si by mass%, and [Mo] represents the amount of Mo by mass%, a following expression (F) is satisfied, 560 - 474 x [C] - 90 x [Mn] - 20 x [Cr] - 20 x [MOT < CT < 830 - 270 x [C] - 90 15 x [Mn] - 70 x [Cr] - 80 x [Mo] (F). 7. The metllod for producing the cold rolled steel sheet accordrng to claim 6, wherein when T represents a heating temperature in the heating in unit OC, t represents an 20 in-furnace time in the heating in unit minute, [Mn] represents the amount of Mn by mass%, and [S] represents an amount of S by mass%, a following expression (G) is satisfied. T x ln(t) 1 (1.7 x [Mn] + [S]) > 1500 (G) 25 8. A cold rolled steel sheet for a hot stamping comprising, by mass%: C: 0.030% to 0.150%; Si: 0.010% to 1.000%; Mn: 1.50% to 2.70%; P: 0.001 %to 0.060%; 5 S: 0.001% to 0.010%; N: 0.0005% to 0.0100%; Al: 0.010% to 0.050%, and optionally one or more of B: 0.0005% to 0.0020%; 10 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%; 15 Ni: 0.01%to 1.00%; Cu: 0.01% to 1.00%; Ca: 0.0005% to 0.0050%; REM: 0.0005% to 0.0050%, and a balance including Fe and unavoidable impurities, wherein 20 when [C] represents an anlount of C by mass%, [Si] represents an amount oSSi by mass%, and [Mn] represents an amount of Mn by mass%, a following expression (H) is satisfied, a metallograpliic structure after the hot stamping includes 40% to 90% of a ferrite and 10% to 60% of a martcnsite in an area fraction, 2.5 a total of an area fraction of the Serrite and an area fraction of the martensite is 60% or more, the metallographic structure optionally further includes one or more of 10% or less of a perlite in an area fraction, 5% or less of a retained austenite in a volume ratio, and less than 40% of a bainite as a remainder in an area fraction, 5 a hardness of the martensite measured with a nanoindenter satisfies a following expression (I) and a following expression(J) after the hot stamping, I I TS x h which is a product of a tensile strength TS and a hole expansion ratio h is I 50000MPa.% or more, (5 x [Si] + [Mn]) / [C] > 11 (HI, 10 H2l /HI1 < l.lO(I), ~ 01-lMl < 20 (J), and the HI 1 is an average hardness of the martensite in a surface part of a sheet thickness after the hot stamping, the H21 is an average hardness of the martensite in a central part of the sheet thickness which is an area having a width of 200 pm in a 15 thickness direction at a center of the sheet thickness after the hot stamping, and the oHM1 is a variance of the hardness of the martensite in the central part of the sheet thickness after the hot stamping. 9. The cold rolled steel sheet for the hot stamping according to claim 8, 20 wherein an area fraction of MnS existing in the cold rolled steel sheet and having an equivalent circle diameter of 0.1 p to 10 pm is 0.01% or less, a following expression (K) is satisfied, n21 In11 11.5 (K), and 25 the n l l is an average number density per 10000 pn2 of the MIIS having the equivalent circle diameter of 0.1 pm to 10 pm in a 114 part of the sheet thickness after the hot stamping, and the n21 is an average number density per 10000 pm2 of the Mils having the equivalent circle diameter of 0.1 pm to 10 pm in the central part of the sheet thickness after the hot stamping. 5 10. The cold rolled steel sheet for the hot stamping according to claim 8 or 9, wherein a hot dip galvanizing is formed on a surface thereof. 11. The cold rolled steel sheet for the hot stamping according to claim 10, 10 wherein a galvannealing is formed on a surface of the cold rolled steel sheet in which the 1 hot dip galvanizing is formed on the surface thereof. 12. The cold rolled steel sheet for the hot stamping according to claim 8 or 9, wherein an electrogalvanizing is formed on a surface thereof. 15 13. The cold rolled steel sheet for the hot stamping according to claim 8 or 9, wherein an aluminizing is formed on a surface thereof. 14. A method for producing a cold rolled steel sheet for a hot stamping, the 20 method comprising: casting a molten steel having a chemical composition according to claim 8 and obtaining a steel; heating the steel; hot-rolling the steel with a hot-rolling mill including a plurality of stands; 25 coiling the steel after thc hot-rolling; pickling the steel after the coiling; cold-rolling the steel with a cold-rolling mill including a plurality of stands after the pickling under a condition satisfying a following expression (L); annealing in which the steel is annealed under 700°C to 850°C and cooled after 5 the cold-rolling; temper-rolling the steel after the annealing, 1.5 x r l / r + 1 . 2 x r 2 / r + r 3 / r > 1 (L), and the ri (i = 1,2, 3) represents an individual target cold-rolling reduction at an ith stand (i = 1,2,3) based on an uppermost stand in the plurality of stands in the 10 cold-rolling in unit %, and the r represents a total cold-rolling reduction in the cold-rolling in unit %. 15. The method for producing the cold rolled steel sheet for the hot stamping ~ according to claim 14, wherein ! 15 when CT represents a coiling temperature in the coiling in unit OC, [C] represents the amount of C by mass%, [Mn] represents the amount of Mn by mass%, [Si] represents the amount of Si by mass%, and [Mo] represents the amount of Mo by mass% in the steel sheet, a following expression (M) is satisfied, 20 x [Mn] - 70 x [Cr] - 80 x [Mo] (M). 16. The method for producing the cold rolled steel sheet for the hot stamping accord~ngto claim 15, wherein when T represents a heating temperature in the heating in unit OC, t represents an 25 in-furnace time in the heating in unit minute, MI] represents the amount of Mn by mass% in the steel sheet, and [S] represents an amount of S by mass%, a following expression (N) is satisfied. T x in(t) / (1.7 x [Mi] + [S]) > 1500 (N) 5 17. The method for producing the cold rolled steel sheet for the hot stamping according to any one of claims 14 to 16, further comprising: galvanizing the steel between the annealing and the temper-rolling. 18. The method for producing the cold rolled steel sheet for the hol slamping 10 according to claim 17, hrtlier comprising: alloying the steel between the galvanizing aid the temper-rolling. 19. The method for producing the cold rolled steel sheet for the hot stamping according to any one of claims 14 to 16, further comprising: 15 electrogalvatiizing the steel after the temper-rolling. 20. The methotl for producing the cold rolled steel sheet for the liol stamping according to any one of clainls 14 to 16, further comprising: aluminizing the steel between the annealing and the temper-rolling. Dated this 01/07/2014 [RANJNA mIITA-DUTT] OF REMFRY & SAGAR ATTORNEY FOR THE APPLICANT[S]