 high-strength hot-dip galvanized steel sheet and method for its production
专利摘要:
abstract a base steel sheet has a hot-dip galvanized layer formed on a surface thereof, in which, in a steel sheet structure in a range of 1/8 thickness to 3/8 thickness centered around 1/4 thickness of a sheet thickness from a surface, a volume fraction of a retained austenite phase is 5% or less, and a total volume fraction of a bainite phase, a bainitic ferrite phase, a fresh martensite phase and a tempered martensite phase is 40% or more, an average effective crystal grain diameter is 5.0 µm or less, a maximum effective crystal grain diameter is 20 µm or less, and a decarburized layer with a thickness of 0.01 µm to 10.0 µm is formed on a surface layer portion, in which a density of oxides dispersed in the decarburized layer is 1.0 × 1012 to 1.0 × 1016 oxides / m2, and an average grain diameter of the oxides is 500 nm or less. _______________________ translation of the summary patent summary of invention: "high strength hot dip galvanized steel sheet excellent in impact resistance property and method for its production, and high bonded hot dip galvanized steel sheet resistance and method for its production ". a base steel sheet has a hot-dip galvanized layer formed on its surface, in which, in a structure of the steel sheet in a range of 1/8 of the thickness to 3/8 of the thickness centered around 1/4 of the thickness of the steel sheet from the surface ,. the volume fraction of the retained austenite phase is 5% or less, and the total volume fraction of a bainite phase, a bainite ferrite phase, a new martensite phase, and a tempered martensite phase is 40% or more , the effective crystal grain diameter is 5.0 µm or less, the maximum effective crystal grain diameter is 20 µm or less, and a decarburized layer with a thickness of 0.01 µm to 10.0 µm is formed in a portion of the surface layer, in which the density of the oxides dispersed in the decolorized layer is 1.0 × 1012 to 1.0 × 1016 oxides / m2, and the average grain diameter of the oxides is 500 nm or less . 公开号:BR112014007677B1 申请号:R112014007677 申请日:2012-09-28 公开日:2020-04-22 发明作者:Minami Akinobu；Murasato Akinobu；Ban Hiroyuki；Kawata Hiroyuki；Hiramatsu Kaoru；Maruyama Naoki；Yasui Takeshi；Kuwayama Takuya 申请人:Nippon Steel & Sumitomo Metal Corp；Nippon Steel Corp； IPC主号:
专利说明:
(54) Title: STEEL PLATE GALVANIZED BY HOT IMMERSION OF HIGH RESISTANCE AND METHOD FOR ITS PRODUCTION (51) Int.CI .: C22C 38/00; 1/21 B21B; B21B 3/00; C21D 9/46; C22C 18/04; (...) (30) Unionist Priority: 09/30/2011 JP 2011-218774. (73) Holder (s): NIPPON STEEL CORPORATION. (72) Inventor (s): HIROYUKI KAWATA; NAOKI MARUYAMA; AKINOBU MURASATO; AKINOBU MINAMI; TAKESHI YASUI; TAKUYA KUWAYAMA; HIROYUKI BAN; KAORU HIRAMATSU. (86) PCT Application: PCT JP2012075098 of 28/09/2012 (87) PCT Publication: WO 2013/047755 of 04/04/2013 (85) Date of the Beginning of the National Phase: 28/03/2014 (57) Summary: ABSTRACT The base steel sheet has a hot-dip galvanized layer formed on a surface thereof, in which, in a steel sheet structure in a range of 1/8 thickness to 3/8 thickness centered around 1/4 thickness of a sheet thickness from a surface, a volume fraction of a retained austenite phase is 5% or less, and a total volume fraction of a bainite phase, a bainitic ferrite phase, a fresh martensite phase and a tempered martensite phase is 40% or more, an average effective crystal grain diameter is 5.0 pm or less, a maximum effective crystal grain diameter is 20 pm or less, and a decarburized layer with a thickness of 0.01 pm to 10.0 pm is formed on a surface layer portion, in which a density of oxides dispersed in the decarburized layer is 1.0 x 1012 to 1.0 x 1016 oxides / m2, and an average grain diameter of the oxides is 500 nm or less._ ____________ TRANSLATION OF SUMMARY SUMMARY Patent of Invention: STEEL SHEET GALVANIZED BY IMER-SÃO HOT OF EXCELLENT HIGH RESISTANCE IN PROPERTY OF IMPACT RESISTANCE AND METHOD FOR ITS PRODUCTION, AND GALVANIZED STEEL SHEET BY HOT IMMERSION FOR HIGH LINK FOR HIGH RESISTANCE HARD LINING YOUR PRODUCTION. A base steel sheet has a galvanized layer (...). 1/110 Descriptive Report of the Invention Patent for GALVANIZED STEEL SHEET BY HOT IMMERSION OF HIGH RESISTANCE AND METHOD FOR ITS PRODUCTION. TECHNICAL FIELD [001] The present invention relates to a high-strength hot-dip galvanized steel sheet with excellent impact-resistance properties and a method for its production, and to a hot-dip galvanized steel sheet high strength alloy and a method for its production, and the present invention relates particularly to a high strength hot dip galvanized steel sheet, a high strength hot dip galvanized steel sheet excellent in property resistance to impact at low temperature, and its production method. BACKGROUND TECHNIQUE [002] In recent years, the demand to also improve the impact resistance property of a high strength coated steel sheet used for automobiles and the like has grown. As techniques related to highly resistant coated steel sheets excellent in impact resistance properties, the techniques described in Patent Literature 1 to Patent Literature 11, for example, have been proposed. [003] Patent Literature 1 describes a hot-rolled steel sheet of high strength excellent in folding workability and toughness anisotropy that contains, in mass%, C: 0.08 to 0.15%, Si : 0.3 to 1.5%, Mn: 1.5 to 2.5%, P: <0.01%, S: <0.01%, Al: 0.01 to 0.05%, Ti: 0.03 to 0.15%, N: <0.004%, B: 0.0003 to 0.001%, O: 0.005%, and a balance composed of Fe and the inevitable impurities, and has a ratio between the amount of absorption of Eab-L energy in a Charpy test specified in JISZ2242 (amount of Petition 870190015116, of 02/14/2019, p. 6/125 2/110 energy absorption in the Charpy test (conducted at -40 ° C) of the specimen whose longitudinal direction is the L direction) and Eab-C (Eab-L / Eab-C (amount of energy absorption in the Charpy test (conducted at 40 ° C) of the specimen in which the longitudinal direction is the C direction)) (not less than 0.9 nor more than 1.3). [004] In addition, Patent Literature 2 describes a technique for producing a high-strength hot-rolled steel sheet with a tensile strength of 980 MPa or more, having a steel composition containing C: 0.08 to 0.20%, Si: less than 0.2%, Mn: greater than 1.0% and equal to or less than 3.0%, N: 0.01% or less, V: greater than 0.1% and equal to or less than 0.5%, Ti: 0.05% or more and less than 0.25%, and Nb: 0.005 to 0.10%, having a steel structure in which the ferrite area ratio is 60% or more, and the martensite area ratio is 5% or less, having an average ferrite grain diameter of 5 pm or less, having a d correction of 0.05% or less, and having a numerical density total inclusions and precipitates each having an average grain diameter of 5 pm or more than 300 pieces / mm 2 or less. [005] In addition, Patent Literature 3 describes a product of high strength excellent in toughness at low temperature and with low anisotropy, having a random x-ray intensity ratio of the {110} plane in a position at 1/4 of the steel sheet thickness from the steel sheet surface from 1.2 to 4.0, and having a random x-ray intensity ratio of the plane {211} at a position 1/2 the thickness of the steel sheet steel from the surface of the steel sheet 1.2 to 4.0. [006] Patent Literature 4 describes a high-strength hot-rolled steel sheet having a composition in which, in% by mass, C is limited to 0.05% or more and less than 0.20%, Mn is limited to be 0.5% or more and less than 1.5%, Al sol. is limited to Petition 870190015116, of 02/14/2019, p. 7/125 3/110 is 0.002% or more and less than 0.05%, Si is limited to less than 0.1%, Cr is limited to less than 0.1%, Ti is limited to be 0.01% or less, Nb is limited to less than 0.005%, V is limited to be 0.01% or less, N is limited to less than 0.005%, and the balance is made up of Fe and the inevitable impurities, having a structure in a position in which the depth from the surface of the steel sheet is 1/4 the thickness of a steel sheet from the surface containing a ferrite phase as the main phase, and a martensite phase of 10 to 30% by volume , in which the average diameter of the crystal grain of the ferrite phase is 1.1 to 3.0 pm, and the average grain diameter of the martensite phase is 3.0 pm or less. [007] In addition, Patent Literature 5 describes a method of producing a high-strength hot-rolled steel sheet having a microscopic structure in which the ferrite volume ratio is 80% or more, and the average diameter of the ferrite grain is less than 10 pm, in which a steel containing C: 0.05 to 0.30% by weight, Si: 2.0% by weight or less, Mn: 1.0 to 2.5% by weight , and Al: 0.05% by weight or less, containing one or two elements between Ti: 0.05 to 0.3% by weight, and Nb: 0.10% by weight or less, and containing a balance composed of Fe and the inevitable impurities, is heated to a temperature of 950 to 1100 ° C, a reduction in which the lamination reduction per unit time becomes 20% or more is then carried out so that the finishing temperature becomes at the point of transformation Ar3 or more, the cooling is carried out in a temperature range of the transformation point Ar3 up to 750 ° C at a rate of 20 ° C / s or more, the retention in a temperature range of less than 750 ° C to 600 ° C is subsequent then performed for a period of 5 to 20 seconds, the cooling is performed over a temperature range from the transformation point Ar3 to 750 ° C, the cooling is then performed again at a rate of 20 ° C / s or more until the temperature Petition 870190015116, of 02/14/2019, p. 8/125 4/110 reaches 550 ° C or less, and the resulting sheet is wound on a bobbin at a temperature of 550 ° C or less. [008] In addition, Patent Literature 6 describes a hot-rolled thin steel sheet of high strength excellent in workability, fatigue property, and low temperature toughness containing, as main components, C = 0.04 a 0.15% by mass, Si 1 1.0% by mass, Mn 1 1.0% by mass, Nb 1 0.005% by mass, Al = 0.005 to 0.10% by mass, S 0.01% by mass and Fe, having a microstructure formed mainly of ferrite and martensite, in which the ferrite space factor (Vf) is greater than 50%, the average diameter of the ferrite grain (dF) is equal to or less than 5 pm and the diameter average grain of martensite (õm) is equal to or less than 5 pm, and having, as properties, a tensile strength (TS) greater than 590MPa, a yield ratio (YR) equal to or less than 70%, a resistance-ductility balance (tensile strength x total elongation) equal to or greater than 18000 (MPa%), a bore expansion ratio (d / d0) of equal to or greater than 1.2, a fatigue ratio of equal to or greater than 0.40, and a fracture transition temperature equal to or less than -40 ° C. However, each of the techniques described in Patent Literature 1 through Patent Literature 6 is a Technique that refers to a hot rolled steel sheet, and thus cannot be applied to a method of producing a steel sheet including a cold rolling step and an annealing step. As a method of producing an excellent steel sheet in terms of impact resistance including a cold rolling stage and an annealing stage, the techniques described in Patent Literature 7 up to Patent Literature 11 have been proposed. [0010] In addition, Patent Literature 7 describes a high-strength, hot-dip galvanized alloy steel sheet Petition 870190015116, of 02/14/2019, p. 9/125 5/110 excellent in energy absorption properties, which uses, as base material, a steel plate having a composition of components containing C: 0.05 to 0.20% by weight, Si: 0.3 to 1.5 % by mass, Mn: 1.0 to 2.5% by mass, P: 0.1% by mass or less, and the balance being composed of Fe and the inevitable impurities, and having a microstructure containing one or two between martensite and austenite retained from 25 to 50% in volume in total, and a balance composed of ferrite and bainite, and galvanization, by hot dip immersion, is applied to flaps on the surfaces of the steel sheet. [0011] In addition, Patent Literature 8 describes a high-strength hot-dip galvanized steel sheet having a chemical composition containing, in weight%, C: 0.035 to 0.150%, Si: 0.05 to 0, 60%, Mn: 2.0 to 4.0%, P: 0.015% or less, S: less than 0.0015%, Al sol .: 0.8% or less, N: 0.0031 to 0.015%, O: 0.0030% or less, Ti: 0.005 to 0.130%, Nb: 0 to 0.130%, in which the total amount of Ti and Nb is 0.55% or more, and the balance composed of Fe and impurities, and having a metallic structure in which the average diameter of the ferrite crystal grain is 5.0 pm or less and the average diameter of the crystal grain of the second hard phase is 5.0 pm or less. [0012] In addition, Patent Literature 9 describes a method of producing a cold-rolled steel sheet of high strength excellent in property of impact resistance and fixability of the form in which a plate having a C composition: 0.08 to 0.18% by mass, Si: 1.00 to 2.0% by mass, Mn: 1.5 to 3.0% by mass, P: 0.03% by mass or less, S: 0.005 by mass or less, and T.Al: 0.01 to 0.1% by mass%, and having a degree of segregation of Mn = (concentration of Mn in the central portion of the plate - concentration of Mn in the base) / concentration base) from 1.05 to 1.10 and hot rolled, the resulting plate and also cold rolled the resulting plate is then heated for a retention time of 60 seconds Petition 870190015116, of 02/14/2019, p. 10/125 6/110 a two-phase region or a single-phase region at 750 to 870 ° C on a continuous annealing line, cooling is then performed in a temperature region of 720 to 600 ° C at an average rate of cooling 10 ° C / s or less, then cooling is performed until the temperature reaches 350 to 460 ° C at an average cooling rate of 10 ° C / s or more, retention is performed for 30 seconds to 20 minutes, and cooling is then carried out until the temperature reaches room temperature to obtain a five-phase structure, of polygonal ferrite, acicular ferrite, bainite, retained austenite and martensite. [0013] Patent Literature 10 describes a cold rolled steel sheet excellent in impact absorbing property having a hyperfine grain structure containing C, Si, Mn, Ni, Ti, Nb, Al, P, S, and N , having a ferrite phase whose volume fraction is 75% or more in which the average diameter of ferrite crystal grain is 3.5 pm or less, and having a balance, different from the ferrite phase, which becomes practically a structure of tempered martensite steel. [0014] Patent Literature 11 describes a high-tensile, high-tensile, cold-rolled steel sheet excellent in surface properties and impact absorption having, in mass%, C: 0.06 to 0.25% , Si: 2.5% or less, Mn: 0.5 to 3.0%, P: 0.1% or less, S: 0.03% or less, Al: 0.1 to 2.5%, Ti: 0.003 to 0.08%, N: 0.01% or less, and the compound balance of Fe and the inevitable impurities, in which the Ti content satisfies the ratio of (48/14) N Ti (48/14 ) N + (48/32) S + 0.01, and having a structure after lamination to recrystallization cooled being a structure containing austenite retained of 5% or more due to volume. LIST OF QUOTES PATENT LITERATURE [009] Patent Literature 1: Japanese Patent Publication Petition 870190015116, of 02/14/2019, p. 12/115 7/110 open to Public Inspection No. 2010-156016 [0010] Patent Literature 2: Japanese Patent Publication open to Public Inspection No. 2008-285741 [0011] Patent Literature 3: Japanese Patent Publication open to Public Inspection N ° 2008-266758 [0012] Patent Literature 4: Japanese Patent Publication Open to Public Inspection No. 2006-342387 [0013] Patent Literature 5: Japanese Patent Publication Open to Public Inspection No. 09-143570 [0014] Literature Patent 6: Japanese Patent Publication Open to Public Inspection No. 07-150294 [0015] Patent Literature 7: Japanese Patent Publication Open to Public Inspection No. 2009-68039 [0016] Patent Literature 8: Japanese Patent Publication open to Public Inspection No. 2008-255441 [0017] Patent Literature 9: Japanese Patent Publication open to Public Inspection No. 2004-300452 [0018] Patent Literature 10: Japanese Patent Publication open to Public Inspection No. 2004- 277858 [0019] Literature of Patent 11: Japanese Patent Publication Open to Public Inspection No. 10-130776 SUMMARY OF THE INVENTION TECHNICAL PROBLEM [0020] However, in conventional high-strength galvanized steel sheet whose tensile strength TS is 900 MPa or more, it is not possible to sufficiently obtain the impact resistance property at low temperature, and thus the improved property was also demanded resistance to impact at low temperature. [0021] In view of the current situation as described above, the present invention provides a dip galvanized steel sheet Petition 870190015116, of 02/14/2019, p. 12/125 8/110 high-strength hot-dip galvanized steel sheet, high-strength hot-dip galvanized, excellent in impact resistance properties at low temperature and tensile strength of 900 MPa or more, and their production methods . SOLUTION TO THE PROBLEM [0022] The present inventors have repeatedly conducted serious studies to obtain a high-strength hot-dip galvanized steel sheet excellent in impact resistance at low temperature and with a tensile strength of 900 MPa or more. As a result, the present inventors have discovered that it is necessary to produce a high strength galvanized steel sheet in which a base steel sheet having a hot dip galvanizing layer formed on its surface is adjusted to have predetermined chemical components with which a tensile strength of 900 MPa or more can be achieved, the structure of the steel sheet in a range of 1/8 of the thickness to 3/8 of the thickness centered around 1/4 of the thickness of the sheet from the surfaces has a retained austenite phase of 5% or less in volume fraction, and a bainite phase, a bainite ferrite phase, a new martensite phase, and a tempered martensite phase of 40% or more in total in fraction of volume, the effective average diameter crystal grain is 5.0 pm or less, the maximum effective diameter of crystal grain is 20 pm or less, and a decarbonized layer with a thickness of 0.01 pm to 10.0 pm is formed in one portion of the layer surface, in which the density and the oxides dispersed in the decarbonized layer is 1.0 χ 10 12 to 1.0 χ 10 16 oxides / m 2 , and the average grain diameter of the oxides is 500 nm or less. [0023] Specifically, in such a high-strength galvanized steel sheet, the volume fraction of the austenite phase retained from the base steel sheet to be the point of fracture is small, 5% or less. In addition, the average effective diameter of the crystal grain of the base steel plate in the Petition 870190015116, of 02/14/2019, p. 12/13 9/110 range of 18 thickness to 3/8 thickness centered around 1/4 of the plate thickness from the surface is 5.0 pm or less and 20 pm or less, respectively, and so both the average diameter effective of the crystal grain and the maximum effective diameter of the crystal grain are small, resulting in the fact that the high strength galvanized steel sheet becomes excellent in toughness at low temperature and with excellent property of resistance to impact at low temperature. [0024] Additionally, in such a high-strength galvanized steel sheet, the decarbonized layer with a thickness of 0.01 pm to 10.0 pm and with a small amount of hard structures is formed in the surface layer portion of the sheet. base steel, the density of the oxides dispersed in the decarbonized layer is 1.0 χ 10 12 to 1.0 χ 10 16 oxides / m 2 , and the average grain diameter of the oxides is 500 nm or less, which is difficult to make a fracture starting point, so that the difference in elasticity limit between the decarbonized layer and the central portion of the steel sheet is small. Consequently, in the high-strength galvanized steel sheet, it is possible to avoid the fracture that occurred from the surface layer of the base steel sheet, and the stress concentration at an interface between the decarbonized layer and a layer under the decarbonized layer, occurred at the moment of an impact, it is suppressed, so that the high-strength galvanized steel sheet becomes a sheet which the fragile fracture is difficult to occur, and with excellent impact resistance property. [0025] The present invention is completed based on such discoveries, and its essence is as follows. [0026] High strength hot dip galvanized steel sheet excellent in impact resistance property is characterized by the fact that it has a galvanized layer by Petition 870190015116, of 02/14/2019, p. 12/14 10/110 hot immersion formed on the surface of a base layer containing, in% by mass, C: 0.075 to 0.400%, Si: 0.01 to 2.00%, Mn: 0.80 to 3.50%, P: 0.0001 to 0.100%, S: 0.0001 to 0.0100%, Al: 0.001 to 2.00%, O: 0.0001 to 0.0100%, N: 0.0001 to 0.0100%, and [0027] the balance composed of Fe and the inevitable impurities, in which the base steel plate has a structure of the base steel plate and a range of 1/8 of the thickness a 3/8 of the thickness centered around if 1/4 of the thickness of a steel sheet from the surface, in which the volume fraction of a retained austenite phase is 5% or less, and the total volume fraction of the bainite phase , the bainitic ferrite phase, the new martensite phase and the tempered martensite phase is 40% or more, the effective mean diameter of the crystal grain and the maximum effective diameter of the crystal grain in the range of 1/8 of the thickness to 3/8 the thickness centered around 1/4 of the thickness of the steel sheet from the surface is 5.0 pm or less and 20 pm or less, respectively, and the decarbonized layer with a thickness of 0.01 pm to 10.0 pm is formed in the portion of the surface layer, in which the density of the oxides dispersed in the decarbonized layer is 1.0 χ 10 12 to 1.0 χ 10 16 oxides / m 2 , and the average diameter grain size of the oxides is 500 nm or less. [0028] It is characterized by the fact that the hot-dip galvanized steel sheet of excellent high strength in terms of impact resistance as per item (1), the base steel layer also contains, in mass%, a or two or more elements selected from Petition 870190015116, of 02/14/2019, p. 12/15 11/110 Ti: 0.001 to 0.150%, Nb: 0.001 to 0.100%, and V: 0.001 to 0.300%. [0029] It is characterized by the fact that in the hot-dip galvanized steel sheet of high strength excellent in impact resistance properties according to item (1) or (2), the base steel sheet also contains one or two or more elements selected from among Cr: 0.01 to 2.00%, Ni: 0.01 to 2.00%, Cu: 0.01 to 2.00%, Mo: 0.01 to 2.00%, B: 0.0001 to 0.0100%, and W: 0.01 to 2.00%, [0030] It is characterized by the fact that in hot-dip galvanized steel sheet of high strength excellent in impact resistance properties according to any of the items (1) to ( 3), the base steel sheet also contains 0.0001 to 0.0100% in the total of one or more elements selected from Ca, Ce, Mg, Zr, La, and REM. [0031] High strength bonded hot dip galvanized steel sheet excellent in impact resistance property is characterized by the fact that it has the hot dip galvanized layer of high strength hot dip galvanized steel sheet as any of items (1) to (4), the hot dip galvanized layer being bonded. [0032] The method of producing a hot-dip galvanized steel sheet of excellent high strength in terms of impact resistance is characterized by the fact that it includes: [0033] a step of obtaining a base steel sheet, the stage Petition 870190015116, of 02/14/2019, p. 12/165 12/110 including: [0034] a hot rolling step of performing hot rolling in which a plate containing, in mass%, C: 0.075 to 0.400%, Si: 0.01 to 2.00%, Mn: 0.80 to 3.50%, P: 0.0001 to 0.100%, S: 0.0001 to 0.0100%, Al: 0.001 to 2.00%, O: 0.0001 to 0.0100%, N: 0.0001 to 0.0100%, and [0035] a balance composed of Fe and the inevitable impurities is heated to 1080 ° C or more, hot rolling is completed at a temperature of 850 ° C to 950 ° C, and the rolling reduction in a temperature region of 1050 ° C to a hot rolling finish temperature that satisfies (expression 1) below to obtain a steel sheet hot rolled; [0036] a cold rolling step of performing cold rolling at a reduction rate of 30% to 75% on the hot rolled steel sheet to obtain a cold rolled steel sheet; and [0037] an annealing step of performing the annealing in which the cold rolled steel sheet is passed through a preheating zone in which the heating is performed using mixed gas whose air ratio being the ratio between the volume of air contained in the mixed gas per unit of volume and the volume of air that is theoretically necessary to cause complete combustion of the combustible gas contained in the mixed gas per unit of volume in the mixed air and fuel gas used for preheating, is 0.7 to 1.2, to generate an oxide coating film on a portion of the surface layer, the steel sheet is passed through a Petition 870190015116, of 02/14/2019, p. 12/17 13/110 reduction in an atmosphere in which the partial pressure ratio between H2O and H2 (Ρ (Η2 <3) / P (H 2 )) is 0.0001 to 2.00 at a maximum heating temperature of point AC3 - 50 ° C 0 more to reduce the oxide coating film to form a decarbonized layer, and 0 bending with a bending radius of 800 mm or less is performed once or more while a tension of 3 to 100 MPa is applied, while 0 cooling is carried out in a temperature range of 740 ° C to 500 ° C at an average cooling rate of 1.0 ° C / s or more; and [0038] a coating step of getting the steel sheet to be immersed in a coating bath in which the effective amount of Al is 0.01 to 0.18% by mass to form a hot dip galvanized layer in a surface of the base steel plate to produce a hot dip galvanized steel plate. [Mathematical expression 1] 0.10 <· £ (5.20xl0 ' 6 T- -1.06xlO ' 2 · Τ' 2 + 1.68x101, -5.67x10 s ) 2 -í ^ -1 -expf- 2 ' 20xl0 -X, U l T, 0.5 <1.00 (1) [0039] In (Expression 1), N indicates the total number of passes from the start of the hot rolling to the end of the hot rolling, i indicates the order of the pass, Ti indicates the temperature of lamination (° C) on the 1st pass, hi indicates the thickness of the plate after processing (mm) on the 1st pass, et, indicates the time elapsed from the 1st pass to the next pass. Note that when I is equal to 1, hO is equal to the thickness of the plate. In addition, the time elapsed from the final pass to the next pass is adjusted to the time elapsed from the final pass to a point in time when cooling starts after the end of the hot rolling. [0040] It is characterized by the fact that in the production method of high-strength hot-dip galvanized steel sheet Petition 870190015116, of 02/14/2019, p. 12/185 14/110 excellent in property of impact resistance according to item (6), the plate also contains, in mass%, one or two or more elements selected among Ti: 0.001 to 0.150%, Nb: 0.001 to 0.100%, and V: 0.001 to 0.300%, [0041] It is characterized by the fact that in the production method of hot-dip galvanized steel sheet of excellent resistance in terms of impact resistance as per item (6) or (7) , the card also contains one or two or more elements selected from among Cr: 0.01 to 2.00%, Ni: 0.01 to 2.00%, Cu: 0.01 to 2.00%, Mo: 0.01 to 2.00%, B: 0.0001 to 0.0100%, and W: 0.01 to 2.00%, [0042] It is characterized by the fact that in the production method of hot-dip galvanized steel sheet of excellent resistance in terms of impact resistance according to any of the stresses ( 6) to (8), the plate also contains 0.0001 to 0.0100% in total of one or two or more elements selected from Ca, Ce, Mg, Zr, La, and REM. [0043] It is characterized by the fact that in the production method of hot-dip galvanized steel sheet with excellent resistance to impact properties according to any of the items (6) to (9), the coating step it is a step of making the base steel sheet from 430 to 490 ° C enter and be immersed in a coating bath of 450 to 470 ° C [0044] It is characterized by the fact that the production method Petition 870190015116, of 02/14/2019, p. 12/195 15/110 of the hot-dip galvanized steel sheet of excellent high strength in terms of impact resistance according to any of the items (6) to (10), the process of transformation of retaining bainite is carried out, before and / or after immersing the base steel plate in the coating bath, the base steel plate in a temperature range of 300 to 470 ° C for 10 to 1000 seconds. [0045] Production method of high-strength hot-dip galvanized steel sheet with excellent impact resistance property is characterized by the fact that it includes performing the bonding treatment of retaining hot-dip galvanized steel sheet high resistance according to any of the items (6) to (11) in a temperature range of 470 to 620 ° C for 2 seconds to 200 seconds. ADVANTAGE EFFECTS OF THE INVENTION [0046] In accordance with the present invention, it is possible to provide a high-strength hot-dip galvanized steel sheet and an excellent high-strength hot-dip galvanized steel sheet in impact resistance property at low temperature and capable of obtaining a tensile strength of 900 MPa or more, and its production methods. DESCRIPTION OF MODALITIES [0047] The high strength galvanized steel sheet according to one embodiment of the present invention is produced by the formation of a hot dip galvanized layer on the surface of a base steel sheet containing, in mass%, C: 0.075 at 0.400%, Si: 0.01 to 2.00%, Mn: 0.80 to 3.50%, P: 0.0001 to 0.100%, S: 0.0001 to 0.0100%, Al: 0.001 to 2.00%, O: 0.0001 to 0.0100%, N: 0.0001 to 0.0100%, and the compound balance of Fe and the inevitable impurities. [0048] Note that the thickness of the base steel plate is suitable to be 0.6 mm or more and less than 5.0 mm. If the plate thickness Petition 870190015116, of 02/14/2019, p. 12/20 16/110 base steel is less than 0.6 mm, it becomes difficult to maintain the flat shape of the base steel plate, which is not suitable. In addition, if the thickness of the base steel plate is 5.0 mm or more, it becomes difficult to perform cooling control. Also, if the thickness of the plate is 5.0 mm or more, the distortion according to the fold is not sufficient, and a fine dispersion of bainite becomes difficult, resulting in it becoming difficult to produce a predetermined microstructure. [0049] Initially, the chemical components (composition) of the base steel sheet that forms the high-strength galvanized steel sheet according to the modality of the present invention will be described. Note that [%] in the present invention indicates [% by mass] unless otherwise indicated. [0050] [C: 0.075 to 0.400%] [0051] C is contained to increase the strength of a high-strength steel plate. However, if the C content exceeds 0.400%, the toughness and weldability become insufficient. From the point of view of toughness and weldability, the C content is preferably 0.300% or less, and is more preferably 0.250% or less. On the other hand, if the C content is less than 0.075%, the strength is decreased, and it becomes difficult to guarantee sufficient maximum tensile strength. To also increase the strength, the C content is preferably 0.085% or more, and is more preferably 0.100% or more. [0052] [Si: 0.01 to 2.00%] [0053] Si is an element that suppresses the generation of iron-based carbides, and increases strength and forming capacity. However, if the Si content exceeds 2.00%, the density of the oxides dispersed in a decarbonized layer is greatly increased, a result in which the decarbonized layer is greatly increased, resulting in the fact that the decarbonized layer breaks. Petition 870190015116, of 02/14/2019, p. 12/21 17/110 easily, and the impact resistance property is decreased. In addition, if the Si content exceeds 2.00%, the steel sheet is weakened and the ductility is deteriorated, resulting in the fact that it is difficult to perform cold rolling. From the point of view of the impact resistance property, the Si content is preferably 1.80% or less, and is more preferably 1.50% or less. On the other hand, if the Si content is less than 0.01%, the density of the oxides dispersed in the decarbonized layer becomes insufficient, and the resistance of the decarbonized layer becomes insufficient, resulting in the impact resistance property being decreased. . In addition, if the Si content is less than 0.01%, when the high-strength hot-dip galvanized steel sheet is bonded, a large amount of crude iron-based carbides is generated through the bond, resulting in fact that strength and conformability deteriorate. From the point of view of the impact resistance property, the lower limit value of Si is preferably 0.20% or more, and is more preferably 0.50% or more. [0054] [Mn: 0.80 to 3.50%] [0055] Mn is added to increase the strength of the steel plate. However, if the MN content exceeds 3.50%, the density of the oxides dispersed in the decarbonized layer breaks easily, and the impact resistance property is decreased. In addition, if the Mn content exceeds 3.50%, a concentrated portion of crude Mn is generated in the central portion of the steel plate thickness, embrittlement occurs easily, and problems such as rupture of the cast plate occur easily. In addition, if the Mn content exceeds 3.50%, the weldability also deteriorates. From the above description, it is necessary to adjust the Mn content to 3.50% or less. From the point of view of the impact resistance property, the Mn content is preferably 3.00% or less, and is more preferably 2.70% or less. Petition 870190015116, of 02/14/2019, p. 12/22 18/110 [0056] On the other hand, if the Mn content is less than 0.80%, the density of the oxides dispersed in the decarbonized layer becomes insufficient, and the resistance of the decarbonized layer becomes insufficient, resulting in the fact that the property of impact resistance is decreased. In addition, if the Mn content is less than 0.80%, a large number of soft structures are formed during cooling after annealing, which makes it difficult to guarantee a sufficiently high tensile strength. Therefore, it is necessary to adjust the Mn content to 080% or more. To also increase the strength, the Mn content is preferably 1.00% or more, and is more preferably 1.30% or more. [0057] [P: 0.0001 to 0.100%] [0058] P tends to be segregated in the central portion in the thickness of the steel plate, and weakens the welding zone. If the P content exceeds 0.100%, a significant weakening of the welding zone occurs, so that the upper limit of the P content is adjusted to 0.100%. On the other hand, 0.0001% is adjusted as a lower limit value since production costs increase greatly when the P content is adjusted to less than 0.0001%, and the P content is adjusted to less than 0 , 0001%, and the P content is preferably adjusted to 0.0010% or more. [0059] [S: 0.0001 to 0.0100%] [0060] S has an adverse effect on weldability and production capacity during casting and hot rolling. For this reason, the upper limit value of the S content is adjusted to 0.0100% or less. In addition, S joins Mn to form crude MnS and decreases ductility and flanging capacity in the stretch, so that the S content is preferably adjusted to 0.0050% or less, and is more preferably adjusted to 0 , 0030% or less. On the other hand, 0.0001% is adjusted as a lower limit value Petition 870190015116, of 02/14/2019, p. 12/23 19/110 since production costs increase greatly when the S content is adjusted to less than 0.0001%, and the S content is preferably adjusted to 0.0005% or more, and is more preferably adjusted to 0 , 0010% or more. [0061] [Al: 0.001 to 2.00%] [0062] Al suppresses the generation of iron-based carbides and increases the strength and forming capacity of the steel sheet. However, if the Al content exceeds 2.00%, the welding capacity worsens, so that the upper limit of the Al content is adjusted to 2.00%. Furthermore, from that point of view, the Al content is more preferably adjusted to 1.50% or less, and even more preferably adjusted to 1.20% or less. On the other hand, although the effect of the present invention is presented without particularly determining the lower limit of Al content, that lower limit is adjusted to 0001% or more, since Al is an unavoidable impurity that exists in a very small amount in a raw material, and production costs increase greatly when the Al content is adjusted to less than 0.001%. In addition, Al is an effective element also as a deoxidizing material, and to also sufficiently obtain the deoxidation effect, the Al content is more preferably adjusted to 0.010% or more. [0063] [N: 0.0001 to 0.0100%] [0064] N forms a crude nitride and deteriorates the ductility and flanging capacity in the stretch, so that its added quantity needs to be suppressed. If the N content exceeds 0.0100%, this trend becomes evident, so that the upper limit of the N content is adjusted to 0.0100%. Furthermore, since N causes the generation of bubbles during welding, the N content is preferably low. The N content is preferably 00070% or less, and is more preferably 0.0050% or less. Although the effect of Petition 870190015116, of 02/14/2019, p. 12/24 20/110 present invention without being particularly determined the lower limit of the N content, the production costs increase greatly when the N content is adjusted to 0.0001% or more. The N content is preferably 0.0003% or more, and is more preferably 0.0005% or more. [0065] [O: 0.0001 to 0.0100%] [0066] O forms an oxide and deteriorates the ductility and flanging capacity in the stretch, so its content needs to be suppressed. If the O content exceeds 0.0100%, the deterioration of the stretching flanging capacity becomes noticeable, so that the upper limit of the O content is adjusted to 0.0100%. In addition, the O content is preferably 0.0070% or less, and is more preferably 0.0050% or less. Although the effect of the present invention is presented without particularly determining the lower limit of the O content, 0.0001% is adjusted as a lower limit since the production costs increase greatly when the O content is adjusted to less than 0.0001 %. The O content is preferably 0.0003% or more, and is more preferably 0.0005% or more. [0067] Unlike the above, the following elements can also be added, as needed, to the base steel plate of the hot-dip galvanized steel plate according to the modality of the present invention. [0068] [Ti: 0.001 to 0.150%] [0069] Ti is an element that contributes to increase the strength of the steel sheet by reinforcing precipitation, reinforcing the fine grain by suppressing the growth of ferrite crystal grains, and reinforcing displacement by suppressing recrystallization. However, if the Ti content exceeds 0.150%, the precipitation of carbonitrides increases, and the forming capacity deteriorates, so that the Ti content is more preferably 0.150% or less. From the point of view of the ability to Petition 870190015116, of 02/14/2019, p. 12/25 21/110 conformation, the Ti content is more preferably 0.080% or less. Although the effect of the present invention is shown without particularly determining the lower limit of the Ti content, to sufficiently obtain the effect of increasing the strength provided by the addition of Ti, the Ti content is preferably 0.001% or more. To also increase the strength of the steel sheet, the Ti content is more preferably 0010% or more. [0070] [Nb: 0.001 to 0.100%] [0071] Nb is an element that contributes to increase the strength of the steel sheet by reinforcing precipitation, reinforcing the fine grain by suppressing the growth of ferrite crystal grains, and reinforcing displacement by suppressing recrystallization. However, if the Nb content exceeds 0.100%, the precipitation of carbonitrides increases, and the forming capacity deteriorates, so that the Nb content is more preferably 0.100% or less. From the point of view of forming ability, the Nb content is more preferably 0.050% or less. Although the effect of the present invention is shown without particularly determining the lower limit of the Nb content, to sufficiently obtain the effect of increasing the resistance provided by the addition of Nb, the Nb content is preferably 0.001% or more. To also increase the strength of the steel sheet, the Nb content is more preferably 0.010% or more. [0072] [V: 0.001 to 0.300%] [0073] V is an element that contributes to increase the strength of the steel sheet by reinforcing precipitation, reinforcing the fine grain by suppressing the growth of ferrite crystal grains, and reinforcing displacement by suppressing recrystallization. However, if the V content exceeds 0.300%, the precipitation of carbonitrides increases, and the forming capacity deteriorates, so that the V content is more preferably 0.300% or less, and is even more preferably Petition 870190015116, of 02/14/2019, p. 12/26 22/110 0.200% or less. Although the effect of the present invention is presented without particularly determining the lower limit of the V content, to obtain sufficiently the effect of increasing the strength provided by the addition of V, the V content is preferably 0.001% or more, and is more preferably 0.010% or more. [0074] [Cr: 0.01 to 2.00%] [0075] Cr is an effective element to increase resistance by suppressing a phase transformation at high temperature, and can be added instead of part of C and / or Mn. If the Cr content exceeds 2.00%, the working capacity during hot work is impaired and productivity is decreased, so that the Cr content is preferably adjusted to 2.00% or less, and is more preferably 1.40% or less. Although the effect of the present invention is presented without particularly determining the lower limit of the Cr content, to sufficiently obtain the effect of increasing the strength provided by the addition of Cr, the Cr content is preferably 0.01% or more, and is more preferably 0.01% or more, and more preferably 0.10% or more. [0076] [Ni: 0.01 to 2.00%] [0077] Ni is an effective element for increasing resistance by suppressing the phase transformation at high temperature, and can be added instead of part of C and / or Mn. If the Ni content exceeds 2.00%, the welding capacity is impaired, so that the Ni content is preferably adjusted to 2.00% or less, and is more preferably 1.40% or less. Although the effect of the present invention is presented without particularly determining the lower limit of the Ni content, to obtain sufficiently the effect of increasing the resistance provided by the addition of Ni, the Ni content is preferably 0.01% or more, and is more preferably 0.10% or more. [0078] [Cu: 0.01 to 2.00%] Petition 870190015116, of 02/14/2019, p. 12/27 23/110 [0079] Cu is an element that exists in steel as a fine particle to increase strength, and can be added instead of a part of C and / or Mn. If the Cu content exceeds 2.00%, the weldability is impaired, so that the Cu content is preferably adjusted to 2.00% or less, and is more preferably 1.40% or less. Although the effect of the present invention is presented without particularly determining the lower limit of the Cu content, to sufficiently obtain the effect of increasing the resistance provided by the addition of Cu, the Cu content is preferably 0.01% or more, and is more preferably 0.10% or more. [0080] [Mo: 0.01 to 2.00%] [0081] Mo is an effective element for increasing resistance by suppressing the phase transformation at a high temperature, and can be added instead of part of C and / or Mn. If the Mo content exceeds 2.00%, the working capacity during hot work is impaired, and productivity is decreased, so that the Mo content is preferably adjusted to 2.00% or less, and is more preferably 1.40% or less. Although the effect of the present invention is presented without particularly determining the lower limit of the Mo content, to obtain sufficiently the effect of increasing the strength provided by the addition of Mo, the Mo content is preferably 0.01% or more, and is more preferably 0.10% or more. [0082] [B: 0.0001 to 0.0100%] [0083] B is an effective element for increasing resistance by suppressing the phase transformation at a high temperature, and can be added instead of a part of C and / or Mn. If the B content exceeds 0.0100%, the workability during hot work is impaired and productivity is decreased, so that the B content is preferably adjusted to 0.0100% or less. From the point of view of productivity, the B content is more preferably 0.0060% or less. Petition 870190015116, of 02/14/2019, p. 12/28 24/110 Although the effect of the present invention is shown without particularly determining the lower limit of the B content, to sufficiently obtain the effect of increasing the strength provided by the addition of B, the B content is preferably adjusted to 0.0001% or more. To also increase the strength, the B content is more preferably 0.0005% or more. [0084] [W: 0.01 to 2.00%] [0085] W is an effective element to increase the resistance by suppressing the phase transformation at high temperature, and can be added instead of part of the C and / or Mn. If the W content exceeds 2.00%, the working capacity during hot work is impaired and productivity is decreased, so that the W content is preferably adjusted to 2.00% or less, and is more preferably 1 , 40% or less. Although the effect of the present invention is presented without particularly determining the lower limit of the W content, in order to sufficiently increase the resistance by using W, the W content is preferably 0.01% or more, and is more preferably 0, 10% or more. [0086] The base steel sheet on the hot-dip galvanized steel sheet of the mode of the present invention may also contain, as elements other than those mentioned above, 0.0001 to 0.0100% in total of one or two or more elements between Ca, Ce, Mg, Zr, La, and REM. The reason for adding these elements is as follows. [0087] Note that REM stands for Metal Terra Rara, and represents an element that belongs to the series of lantanoids. In the configuration of the present invention, REM and Ce are often added in metal misch, and there is the case that elements in the lanthanoid series are contained in a complex form, in addition to La and Ce. Even if those elements of the lanthanoid series other than La and Ce are contained as unavoidable impurities, the effect of the present invention is Petition 870190015116, of 02/14/2019, p. 12/29 25/110 presented. In addition, the effect of the present invention is shown even if metallic La and Ce are added. [0088] Ca, Ce, Mg, Zr, La, and REM are effective elements to improve the conformability, and one or two or more of them can be added. However, if the total amount of one or two or more elements between Ca, Ce, Mg, Zr, La, and REM exceeds 0.0100%, ductility may be impaired, so that the total content of the respective elements is preferably 0 , 0100% or less, and is more preferably 0.0070% or less. Although the effect of the present invention is presented without particularly determining the lower limit of the content of one or two or more elements between Ca, Ce, Mg, Zr, La, and REM, to sufficiently achieve the effect of improving the conformability of the steel plate, the total content of the respective elements is preferably 0.0001% or more. From the point of view of forming capacity, the total content of one or two or more elements between Ca, Ce, Mg, Zr, La, and REM is more preferably 0.0010% or more. [0089] The balance of the respective elements described above is made up of Fe and the inevitable impurities. Note that it is tolerable that each of the elements mentioned above Ti, Nb, V, Cr, Ni, Cu, Mo, B, and W is contained in a very small amount that is less than the lower limit value described above, as an impurity . In addition, it is also tolerable that Ca, Ce, Mg, Zr, La, and REM are contained in an extremely small amount that is less than the lower limit value of their total amount, as an impurity. [0090] The reason why the structure of the base steel sheet of the high strength galvanized steel sheet according to the embodiment of the present invention is specified is as follows. [0091] (Microstructure) [0092] The base steel plate of the high-grade galvanized steel plate Petition 870190015116, of 02/14/2019, p. 12/30 26/110 resistance according to the modality of the present invention has a steel plate structure in a range of 1/8 of the thickness to 3/8 of the thickness centered around 1/4 of the thickness of the steel plate from the surface, in which the retained austenite phase (hereinafter referred to as retained austenite) is 5% or less in volume fraction, and the total amount of the bainite phase (hereinafter referred to as bainite), the bainitic ferrite phase (hereinafter referred to as bainitic ferrite), the new martensite phase (hereinafter referred to as new martensite), and the tempered martensite phase (hereinafter referred to as tempered martensite) is 40% or more in fraction of volume. Retained austenite [0093] Retained austenite is a structure that increases the resistance-ductility balance, and increases the impact absorbing energy at room temperature. On the other hand, in an impact test at a temperature lower than the ambient temperature, the retained austenite is easily transformed into martensite by an impact. The martensite is very hard, and acts strongly as a starting point for the fragile fracture, so that the retained austenite significantly deteriorates tenacity at low temperature. When the volume fraction of retained austenite exceeds 5%, there is a possibility that the fragile fracture occurs even at 40 ° C. For this reason, the volume fraction of the retained austenite is adjusted to 5% or less. To also increase toughness, the volume fraction of the retained austenite is preferably adjusted to 3% or less, and is preferably adjusted to 3% or less, and is preferably adjusted to 2% or less. The smaller the volume fraction of the retained austenite, the more preferable it is, and there is no problem even if the volume fraction of the retained austenite is 0%. Ferrite [0094] Ferrite is a structure that has excellent ductility. However, since the ferrite has low strength, when the fraction Petition 870190015116, of 02/14/2019, p. 12/31 27/110 of ferrite volume is excessively increased, there is a need to greatly increase the strength of another hard structure to ensure strength. In this case, the interface between the hard structure and the ferrite easily becomes a starting point of fracture at the time of the low temperature impact test, resulting in the fact that the low temperature toughness deteriorates. From the point of view described above, the volume fraction of ferrite is preferably adjusted to 50% or less. To also increase toughness, the volume fraction of ferrite is preferably adjusted to 45% or less, and is more preferably 40% or less. The lower limit of the volume fraction of ferrite is not particularly provided, and there is no problem even if it is 0%, but, from the point of view of ductility, the volume fraction of ferrite is preferably adjusted to 5% or more, and is more preferably 10% or more. Bainitic and / or bainite ferrite [0095] Bainitic and / or bainite ferrite are excellent structures in strength, ductility, and toughness, and preferably contained in the structure of the steel sheet in an amount of 10 to 50% and volume fraction. In addition, bainitic ferrite and / or bainite are microstructures that have an intermediate resistance between soft ferrite and hard martensite, tempered martensite and retained austenite, and bainitic and / or bainite ferrite is more preferably contained in an amount of 15 % or more, and even more preferably contained in an amount of 20% or more, from the point of view of flange in the stretch. On the other hand, it is not preferable that the volume fraction of bainitic and / or bainite ferrite exceeds 50%, since there is a concern that the elasticity limit is excessively increased and the fixation capacity of the shape deteriorates. Tempered Martensite [0096] Tempered Martensite is a structure that improves Petition 870190015116, of 02/14/2019, p. 12/32 28/110 greatly increases the tensile strength, and can be contained in the structure of the steel plate in an amount of 50% or less in fraction of volume. From the point of view of tensile strength, the volume fraction of the tempered martensite is preferably adjusted to 10% or more. On the other hand, it is not preferable that the volume fraction of the tempered martensite contained in the steel sheet structure exceeds 50%, since there is a concern that the elasticity limit is increased excessively, and the fixing capacity of the shape deteriorates. . New Martensite [0097] New Martensite greatly improves tensile strength but, on the other hand, it becomes a fracture starting point for deteriorating low temperature toughness, so that it is preferably contained in the steel sheet structure in a amount of 20% or less in volume fraction. To increase toughness at low temperature, the volume fraction of new martensite is most preferably adjusted to 15% or less, and is even more preferably adjusted to 10% or less. Other microstructures [0098] It is also possible that the structure of the high-strength galvanized steel sheet according to the modality of the present invention contains a different structure from the above, such as perlite and / or crude cementite. However, when the amount of perlite and / or crude cementite is increased in the structure of the high-strength steel sheet, the ductility deteriorates. For that reason, the volume fraction of crude perlite and / or cementite contained in the steel sheet structure is preferably 10% or less in total, and is more preferably 5% or less in total. [0099] The volume fraction of each structure contained in the base steel sheet of the high-strength galvanized steel sheet of the present invention can be measured by a method to be described later, Petition 870190015116, of 02/14/2019, p. 12/33 29/110 for example. [00100] Regarding the volume fraction of the retained austenite, an x-ray analysis is conducted by adjusting a surface parallel to the surface of the steel sheet and 1/4 of the thickness from the surface of the base steel sheet as an observation surface to calculate the area fraction, and the result of the calculation can be considered as the volume fraction. [00101] Regarding the volume fractions of ferrite, perlite, bainitic ferrite, bainite, tempered martensite and new martensite contained in the structure of the base steel plate of the high strength galvanized steel plate according to the modality of the present invention, a sample is collected as a cross section in the direction of thickness and parallel to the rolling direction of the base steel plate is set as the observation surface, the observation surface is polished and etched with nital, and a range of 1/8 of the thickness a 3/8 of the thickness centered on a torus of 1/4 of the plate thickness from the surface, is observed in a FE-SEM (field emission scanning electron microscope) to measure the area fractions, and the results of the measurements can be considered as the volume fractions. [00102] The high strength galvanized steel sheet according to the modality of the present invention is one in which the average effective diameter of the crystal grain and the maximum effective diameter of the crystal grain of the base steel plate in the range of 1/8 of the thickness at 3/8 of the thickness centered around 1/4 of the thickness of the steel sheet from the surface, is 5.0 pm or less and 20 pm or less, respectively. [00103] In order to increase the toughness at low temperature and increase the property of resistance to impact at low temperature, it is important to make the effective crystal grain of the base steel plate to be fine. To obtain toughness at a low enough temperature, it is necessary to Petition 870190015116, of 02/14/2019, p. 12/34 30/110 adjust the effective average diameter of the crystal grain of the base steel plate in the range of 1/8 of the thickness to 3/8 of the thickness centered around 1/4 of the thickness of the plate from the surface, that is, in a strip where there is no decarbonized layer, to 5.0 pm or less. To also increase toughness at low temperature, the effective average diameter of the crystal grain of the base steel plate is preferably set to 4.0 pm or less, and is most preferably set to 3.0 pm or less. [00104] Furthermore, when the raw effective crystal grain exists locally, the low temperature toughness deteriorates, so that the maximum effective diameter of the crystal grain is set to 20 pm or less. In order to also increase the toughness at low temperature and increase the impact resistance property at low temperature, the maximum effective diameter of the crystal grain is preferably set to 15 pm or less, and is more preferably set to 12 pm or less. [00105] The effective crystal grain is evaluated by performing a high resolution crystal orientation analysis based on an EBSD method (Electron Bach-Scattering Diffraction) using m FE-SEM (Electron Scanning Microscope with Emission of Field). Note that the cross section in the thickness direction parallel to the lamination direction is finished to have a mirrored surface, a BCC iron crystal orientation (centered body cubic structure) in regions of 50000 pm 2 in total is measured in a range 1/8 of the thickness to 3/8 of the thickness centered around 1/4 of the thickness of the plate from the surface, adjusting the measurement step to 0.5 pm or less, and the edge on which the disorientation the plane (100) becomes at least 10 ° or more, between adjacent midpoints, is defined as an effective crystal grain boundary. Note that structures whose crystal structure is BBC are ferrite, martensite, Petition 870190015116, of 02/14/2019, p. 12/35 31/110 tempered martensite, bainite, bainitic ferrite, perlite, and a complex structure formed from two or more of the above structures. [00112] The effective average diameter of the crystal grain is determined by an intersection method to be described below. Specifically, a grain contour map is created using the effective crystal grain contour lines, whose lengths are 300 pm or more in total, parallel to the rolling direction are written on the grain contour map, and the value obtained by dividing the total lengths of the lines by the number of points of intersection of the lines and the contours of the effective crystal grains is adjusted to the effective average diameter of the crystal grain. In addition, the grain diameter at a position where the distance between two adjacent intersection points is the largest, is adjusted to the maximum effective crystal grain diameter. [00113] The high strength galvanized steel sheet according to the modality of the present invention is one in which a decarbonized layer with a thickness of 0.01 pm to 10.0 pm is formed in a portion of the surface layer of the steel sheet base, the density of oxides dispersed in the decarbonized layer is 1.0 χ 10 12 to 1.0 χ 10 16 oxides / m 2 , and the average grain diameter of the oxides is 500 nm or less. [00114] In the embodiment of the present invention, to prevent the fracture from occurring from a surface layer of the steel sheet in a low temperature impact test, the portion of the surface layer is adjusted to be formed by the decarbonized layer with small amount of hard structures. Note that it is adjusted that the decarbonized layer indicates the region continued from the uppermost surface of the base steel sheet, and the region in which the volume fraction of hard structures is half or less than the volume fraction of hard structures at 1 / 4 of the thickness. Note that Petition 870190015116, of 02/14/2019, p. 12/36 32/110 hard structures mean bainite, bainitic ferrite, new martensite and tempered martensite. [00115] The thickness of the decarbonized layer of the base steel plate can be measured by finishing the cross section in the direction of the thickness parallel to the rolling direction to be a mirrored surface, and performing the observation by an FE-SEM. In the embodiment of the present invention, the thicknesses of the decarbonized layers are measured in three positions or more by steel plate, and the average value of the thickness is adjusted to the thickness of the decarbonized layer. [00116] If the thickness of the decarbonized layer is less than 0.01 pm, the fracture in the portion of the surface layer cannot be sufficiently suppressed, so that the thickness of the decarbonized layer is adjusted to 0.01 pm or more. To also improve toughness at low temperature, the thickness of the decarbonized layer is preferably adjusted to 0.10 pm or more, and is most preferably adjusted to 0.30 pm or more. On the other hand, an excessively thick decarbonized layer decreases the tensile strength and fatigue strength of the high-strength galvanized steel sheet. From this point of view, the thickness of the decarbonized layer is adjusted to 10.0 pm or less. From the point of view of fatigue strength, the thickness of the decarbonized layer is preferably 9.0 pm less. and is most preferably 8.0 pm or less. [00117] The decarbonized layer has low resistance, so that the fracture whose starting point is the decarbonized layer is difficult to occur in the surface layer portion of the base steel plate. However, the difference in strength is large between the normal portion (central portion) of the base steel plate and the decarbonized layer, so that the interface between the standard portion and the decarbonized layer Petition 870190015116, of 02/14/2019, p. 37/125 33/110 can become a new fracture starting point. To avoid this, it is effective to make oxides containing si and / or Mn to be dispersed in a crystal grain and / or in the outline of a crystal grain of the decarbonized layer to increase the resistance of the decarbonized layer, thus reducing the difference in strength between the central portion of the base steel plate and the decarbonized layer. In the embodiment of the present invention, the property of impact resistance at low temperature is improved by setting the average diameter of the crystal grain to 5 pm or less, by setting the maximum effective diameter of the crystal grain to 20 pm or less, and by generating the decarbonized layer on the surface, the low temperature toughness of the base material of the steel sheet is improved and the low temperature toughness on the surface layer is improved by making the oxides from 1.0 χ 10 12 to 1 , 0 χ 10 16 oxides / m 2 are precipitated in the decarbonized layer, and the property of resistance to impact at low temperature is improved by reducing the resistance difference between the decarbonized layer and the normal portion of the base material of the steel plate. [00106] To obtain the decarbonized layer with sufficient strength, the density of the oxides containing Si and / or Mn dispersed in the decarbonized layer is adjusted to 1.0 χ 10 12 oxides / m 2 or more. To also improve toughness at low temperature, the density of the oxides dispersed in the decarbonized layer is preferably adjusted to 3.0 χ 10 12 oxides / m 2 or more, and is more preferably adjusted to 5.0 χ 10 12 oxides / m 2 or more. On the other hand, if the density of the oxides dispersed in the decarbonized layer exceeds 1.0 x 10 16 oxides / m 2 , the distance between the oxides becomes excessively close, and the fracture of the portion of the surface layer is caused by a low level process, which only decreases the resistance of the decarbonized layer and, consequently, the low toughness Petition 870190015116, of 02/14/2019, p. 38/125 34/110 temperature deteriorates. In addition, the fracture of the surface layer portion is caused by the low level of processing, so that the hot dip galvanized layer in the surface layer portion is damaged. For this reason, the density of the oxides dispersed in the decarbonized layer is adjusted to 1.0 χ 10 16 oxides / m 2 or less. In order to make the surface layer of the steel sheet have sufficient forming capacity, the density of the oxides dispersed in the decarbonized layer is preferably adjusted to 5.0 χ 10 15 oxides / m 2 or less, and is more preferably adjusted to 1.0 χ 10 15 oxides / m 2 or less. [00107] When the size of the oxide dispersed in the decarbonized layer is large, the oxide itself acts as a starting point for the fracture, so that the thinner the oxide, the more the low temperature toughness is improved. For this reason, the average grain diameter of the oxides is adjusted to 500 nm or less. To also increase toughness at low temperature, the average grain diameter of the oxides is preferably set to 300 nm or less, and is most preferably set to 100 nm or less. Although a lower limit of the average grain diameter is not provided particularly, the average grain diameter of the oxides is preferably set to 30 nm or more, since there is a need to tightly control the atmosphere and temperature in a described annealing step further on to adjust the diameter to less than 30 nm, which is difficult in practice. [00108] Oxides dispersed in the decarbonized layer can be observed with the use of an FE-SEM by finishing the cross section in the direction of the thickness parallel to the lamination direction to be a mirrored surface. The density of the oxides can be determined by looking at the 7 pm 2 decarbonized layer using an FE-SEM to counter the number of oxides, or using a Petition 870190015116, of 02/14/2019, p. 39/125 35/110 required observation area until when 1000 oxides are counted. In addition, the average grain diameter of the oxides is calculated by averaging 100 to 1000 equivalent circle diameters chosen at random. Note that, as an equivalent circle diameter, the square root of the product of the length of the minor axis by the length of the major axis is used. [00109] The high-strength hot-dip galvanized steel sheet of one embodiment of the present invention is produced by forming a hot-dip galvanized layer on a surface of the base steel sheet. [00110] The hot dip galvanized layer can also be bonded. [00111] In the configuration of the present invention, the hot dip galvanized layer or the linked hot dip galvanized layer may contain one or two or more elements between Pb, Sb, Si, Sn, Mg, Mn, Ni, Cr, Co, Ca, Cu, Li, Ti, Be, Bi, Sr, I, Cs, and REM, or one or two or more of these elements can be mixed in the hot dip galvanized layer or in the hot dip galvanized layer bonded . Even if the hot dip galvanized layer or the connected hot dip galvanized layer contains one or two or more of the elements described above, or one or two or more elements are mixed in the hot dip galvanized layer or each galvanized by hot-dip bonding, the effect of the present invention is not impaired, and there is sometimes a preferable case in which corrosion resistance and workability are improved depending on the content of the element. [00112] The amount of adhesion of the hot dip galvanized layer or of the hot dip galvanized bonded layer is not particularly limited, but is desirably 20 g / m 2 or more from the standpoint of corrosion resistance, and is desirably Petition 870190015116, of 02/14/2019, p. 40/125 36/110 150g / m 2 or less from the point of view of economic efficiency. Production method of the high-strength hot-dip galvanized steel sheet [00113] The production method for the high-strength galvanized steel sheet according to one embodiment of the present invention will be described in detail below. [00114] The production method of the high strength galvanized steel sheet according to the modality of the present invention is applied to the production of a steel sheet in which the thickness of the base steel sheet is 0.6 mm or more and less than 5 , 0 mm. If the thickness of the base steel plate is less than 0.6 mm, it becomes difficult to maintain the flat shape of the base steel plate, which is not suitable. In addition, if the thickness of the base steel plate is 5.0 mm or more, it becomes difficult to perform cooling control. In addition, if the thickness of the sheet is 5.0 mm or more, distortion according to folding is not sufficient, and fine dispersion of bainite becomes difficult, resulting in it becoming difficult to produce a predetermined microstructure. [00115] To produce the hot-dip galvanized steel sheet of high resistance according to the modality of the present invention, the steel sheet is initially produced to be the base steel sheet. To produce the steel plate, a plate containing the chemical components (composition) described above is initially cast. As a plate subjected to hot rolling, it is possible to use a continuously cast plate or a plate produced by a thin plate casting machine, or the like. The production method of the high-strength galvanized steel sheet according to the modality of the present invention is compatible with a process such as direct continuous laminating casting (CC-DR) in which hot rolling is performed immediately after casting. Hot rolling step Petition 870190015116, of 02/14/2019, p. 41/125 37/110 [00116] In a hot rolling step, the heating temperature of the plate is adjusted to 1080 ° C or more to suppress the anisotropy of the crystal orientation caused by the casting. The heating temperature of the plate is most preferably set to 1180 ° C or more. Although the upper limit of the plate heating temperature is not particularly determined, it is preferably set to 1300 ° C or less since a large amount of energy has to be introduced to perform heating at a temperature that exceeds 1300 ° C. [00117] After heating the plate, hot lamination is conducted. In the embodiment of the present invention, hot rolling, in which the hot rolling finish temperature is 850 ° C to 950 ° C, and the rolling reduction in a temperature range from 1050 ° C to the finishing temperature of the lamination is adjusted to fall within a range that satisfies (expression 1) below, it is conducted to obtain a hot rolled steel sheet. [Mathematical expression 1] [00118] In (expression 1), N indicates the total number of passes from the start of the hot rolling to the end of the hot rolling, i indicates the order of the pass, Ti indicates the rolling temperature (° C) in the i ° pass, hi indicates the thickness of the plate after processing (mm) in the first pass, and ti indicates the time elapsed from the first pass until the next pass. Note that when i is equal to 1, h0 is equal to the thickness of the plate. In addition, the time elapsed from the final pass to the next pass is adjusted to the time elapsed from the final pass to the point in time when cooling starts after the end of the hot rolling. Petition 870190015116, of 02/14/2019, p. 42/125 38/110 [00119] If the value described above (expression 1) exceeds 1.00, the crystal grain diameter of the hot-rolled steel sheet becomes crude, and the crystal grain diameter after cold rolling and annealing becomes rough, resulting in the fact that the effective diameter of the crystal grain of the high-strength galvanized steel sheet is made to be rough. For this reason, the value of (expression 1) is adjusted to 1.00 or less. In order to make the effective diameter of the crystal grain of the high-strength galvanized steel sheet to be thin to improve toughness at low temperature, the value of (expression 1) is preferably set to 0.90 or less, and is most preferably set to 0.80 or less. [00120] On the other hand, if the value of (expression 1) is less than 0.10, the recrystallization of the austenite steel sheet does not happen sufficiently in the hot rolling stage, the structure that stretches in the rolling direction is produced, and the structure remains in a microstructure after cold rolling and annealing, resulting in the fact that the effective diameter of the crystal grain of the base steel plate in the rolling direction becomes gross. For this reason, the value of (expression 1) is adjusted to 0.10 or more. In order to make the effective diameter of the crystal grain of the high strength galvanized steel sheet to be thin to also improve the low temperature toughness, the value of (expression 1) is preferably adjusted to 0.20 or more, and is more preferably adjusted to 0.30 or more. Consequently, it is possible to improve the toughness at low temperature which is one of the factors of improvement of the impact resistance property at low temperature. [00121] The average cooling rate even when the hot rolled steel sheet after being subjected to cold rolling is wound on a coil is preferably adjusted to 10 ° C / s or more. This is to make the transformation happen at a lower temperature of Petition 870190015116, of 02/14/2019, p. 43/125 39/110 so that the grain diameter of the hot-rolled steel sheet is made thin to make the effective diameter of the crystal grain of the base steel layer after cold rolling and the annealing being fine. [00122] The winding temperature of the hot rolled steel sheet is preferably set to not less than 500 ° C or more than 650 ° C. This is to make the effective diameter of the crystal grain of the base steel sheet after the annealing is fine by the dispersion of the perlite and / or cementite having an axis greater than 1 pm or more in the microstructure of the hot rolled steel sheet, locate the distortion introduced by cold lamination, and cause the reverse transformation into austenite with several crystal orientations in an annealing step. If the winding temperature is less than 500 ° C, there is the case that perlite and / or cementite are not generated, which is not favorable. On the other hand, if the winding temperature exceeds 650 ° C, each between pearlite and ferrite is generated in the form of a long strip in the rolling direction, and the effective crystal grain of the base steel plate generated from the ferrite part after cold rolling and annealing tends to be rough when stretching in the rolling direction, which is not favorable. [00123] Next, it is preferable to pick the hot-rolled steel sheet produced as above. An oxide on the surface of the hot-rolled steel plate is removed by blasting, so blasting is important to improve the coating capacity of the base steel plate. Stripping can be carried out once or several times separately. Cold rolling stage [00124] Next, cold rolling is performed on the hot-rolled steel plate after being subjected to pickling, to obtain a cold-rolled steel plate. Cold rolling is carried out so that the total reduction ratio becomes no less than 30% and no more than 75%. If the cold rolling reduction ratio is less than Petition 870190015116, of 02/14/2019, p. 44/125 40/110 30%, there is the case that a sufficient distortion is not accumulated in the steel sheet, the recrystallization does not happen sufficiently in the annealing stage after cold rolling, the structure left in the state after processing remains, and the grain is generated raw effective crystal that stretches in the lamination direction. To sufficiently accumulate the distortion through cold rolling, the total reduction ratio is preferably adjusted to 33% or more, and is most preferably adjusted to 36% or more. On the other hand, if the total reduction ratio exceeds 75%, the risk of fracturing the steel sheet during cold rolling becomes high, so that the total reduction ratio is adjusted to 75% or less. From that point of view, the total reduction ratio is preferably adjusted to 70% or less, and is more preferably adjusted to 65% or less. Note that cold rolling is preferably performed by a plurality of passes, in which the number of passes of the cold rolling and the distribution of the reduction ratio in relation to each pass are not particularly limited. Annealing step [00125] In the embodiment of the present invention, annealing is performed on cold rolled steel sheet. In the embodiment of the present invention, it is preferable that a coating line is used for continuous annealing having a preheating zone, a reduction zone, and a coating zone, in which the steel sheet is passed through the preheating zone and of the reduction zone while conducting the annealing step, the annealing step is completed even when the steel sheet reaches the coating zone, and the coating step is conducted in the coating zone. [00126] In the annealing step, the annealing is performed in which the cold-rolled steel sheet is passed through the preheating zone in which the heating is performed using gas Petition 870190015116, of 02/14/2019, p. 45/125 41/110 mixed whose air ratio which is the ratio of the volume of air contained in the mixed gas per unit volume and the volume of air that is theoretically necessary to cause complete combustion of the fuel gas contained in the mixed gas per unit volume in the mixed air and fuel gas used for a preheat burner, it is 07 to 1.2 to generate an oxide coating film on a portion of the surface layer, the steel sheet is passed through the reduction zone in an atmosphere in which the partial pressure ratio between H2O and H2 (P (H2Ü) / PH2)) is 0.0001 to 2.00 at a maximum heating temperature of point Ac3 - 50 ° C or more to reduce the film of oxide coating to form a decarbonized layer, and bending with a bending radius of 800 mm or less is performed once or more while applying a tension of 3 to 100 MPa, while cooling in a temperature region of 740 ° C to 500 ° C at an average cooling rate of 1.0 ° C / s or more is. [00127] The atmosphere in the preheating zone needs only to have an air ratio, the ratio between the volume of air contained in the mixed gas per unit volume and the volume of air that is theoretically necessary to cause the complete combustion of the combustible gas contained. in mixed gas per unit volume in mixed air and fuel gas used for the 0.7 to 1.2 preheat burner, and the atmosphere can be any one between an oxidizing atmosphere, a non-oxidizing atmosphere, and a direct reduction atmosphere. [00128] When the cold rolled steel sheet is passed through a preheat zone, a film of Fe oxide coating with a predetermined thickness is formed in the surface layer portion of the cold rolled steel sheet. By adjusting the air ratio with the volume of air contained in the mixed gas per unit volume and the volume of air that is theoretically necessary to cause complete combustion of the fuel gas contained in the mixed gas by Petition 870190015116, of 02/14/2019, p. 46/125 42/110 volume unit in the mixed air and fuel gas used for the preheat burner to 0.7 to 1.2, the 0.01 to 20 pm Fe oxide coating film is formed in the surface layer of cold rolled steel sheet. The Fe oxide coating film acts as a source of oxygen supply when it is reduced in the reduction zone to generate oxides of Si and / or Mn. [00129] If the volume ratio between air and fuel gas in the mixed gas used to heat the preheat zone exceeds 1.2, the Fe oxide coating film grows excessively in the surface layer portion of the steel sheet cold rolled, resulting in the fact that the thickness of the decarbonized layer of the base steel plate obtained after annealing becomes excessively thick. In addition, if the volume ratio between air and fuel gas exceeds 1.2, the density of oxides dispersed in the decarbonized layer sometimes becomes very large. In addition, if the volume ratio between air and fuel gas exceeds 1.2, there is the case that the excessively grown Fe oxide coating film is not reduced in the reduction zone, and remains in the state, ie , as an oxide coating film as a thick film thickness, which impairs the coating capacity of the base steel plate. [00130] Furthermore, if the air ratio being the ratio between the volume of air contained in the mixed gas per unit volume and the volume of air that is theoretically necessary to cause the complete combustion of the fuel gas contained in the mixed gas per unit of volume the mixed gas of air and fuel gas used for the preheat burner in the preheat zone is less than 0.7, the Fe oxide coating film does not grow sufficiently in the surface layer portion of the rolled steel sheet to cold, and there is a possibility that the decarbonized layer with a thickness Petition 870190015116, of 02/14/2019, p. 47/125 43/110 sufficient when the base steel plate is formed. In addition, if the air ratio is less than 0.7, there is a case where the density of oxides dispersed in the decarbonized layer becomes insufficient. [00131] The heating rate in the annealing step has an influence on the recrystallization behavior on the steel sheet. When the recrystallization is done sufficiently, it is possible to make the crystal grain diameter of the inversely transformed austenite to be thin, resulting in the fact that the effective crystal grain diameter of the base steel plate obtained after annealing becomes thin. In addition, when recrystallization takes place, it is possible to make the diameter of the ferrite crystal grain that remains without being inversely transformed be fine. To make recrystallization happen, the heating rate of 600 to 750 ° C is particularly important, and it is preferable to adjust the average heating rate in that temperature region to 20 ° C / s or less. In the reduction zone, the Fe oxide coating film generated in the preheat zone is reduced to form the decarbonized layer, and Si and / or Mn oxides with a moderate average grain diameter are dispersed in the decarbonized layer at a moderate density. . For this reason, the ratio P (H2Ü) / P (H2) between the partial pressure of water vapor P (H2Ü) and the partial pressure of hydrogen P (H2) in an atmosphere of the reduction zone is set to 0, 0001 to 2.00. P (H2Ü) / P (H2) is preferably adjusted to fall within a range of 0.001 to 1.50, and is most preferably adjusted to fall within a range of 0.002 to 1.20. [00145] Furthermore, if the atmosphere P (H2Ü) / P (H2) of the reduction zone is less than 0.0001, there is the case where oxides are generated on a steel plate surface, and it becomes difficult to disperse predetermined oxides within the decarbonized layer. In addition, if P (H2Ü) / P (H2) exceeds 2.00, there is a case where decarbonization Petition 870190015116, of 02/14/2019, p. 48/125 44/110 happens excessively, and the thickness of the decarbonized layer cannot be controlled to fall within a predetermined range. [00146] The temperature reaches the maximum heating temperature in the annealing step, in the reduction zone. If the maximum heating temperature is low, the reverse transformation to austenite does not happen sufficiently, and the volume fraction of ferrite becomes excessively large. To reduce the amount of austenite retained, and to ensure a sufficient volume fraction of hard structures, the maximum heating temperature is set to (point Ac3 - 50) ° C or more, and is preferably set to (point Ac3 - 35) ° C or more. Although the upper limit of the maximum heating temperature is not particularly provided, heating to a temperature exceeding 1000 ° C significantly impairs the appearance quality of the surface and deteriorates the wetting capacity of the base steel sheet lining, so that the temperature Maximum heating is preferably set to 1000 ° C or less, and is most preferably set to 950 ° C or less. [00147] After this, to make the effective crystal grain diameter of the base steel plate obtained after the annealing is fine, the cooling is conducted at an average cooling rate of 1.0 ° C / s or more in a region from 740 ° C to 500 ° C to suppress ferrite transformation and make the transformation temperature as low as possible. To sufficiently suppress the transformation of ferrite, the average cooling rate in the temperature region of 740 to 500 ° C is preferably adjusted to 2.5 ° C / s or more, and is more preferably adjusted to 4.0 ° C / s or more. Although the upper limit of the average cooling rate in the region of temperatures from 740 ° C to 500 ° C is not particularly provided, an excessively large average cooling rate is not preferable since equipment Petition 870190015116, of 02/14/2019, p. 49/125 45/110 special cooling and a cooling medium that does not interfere with the coating step become necessary to obtain the excessively large average cooling rate. From this point of view, the average cooling rate in the temperature region described above is preferably adjusted to 150 ° C / s or less, and is more preferably adjusted to 100 ° C / s or less. [00132] Furthermore, in the region of temperatures from 740 ° C to 500 ° C, bending with a bending radius of 800 mm or less is carried out once or more while a tension of 3 to 100 MPa is applied. Consequently, the nucleation of the crystal grains with different crystal orientations is facilitated in the cold-rolled steel plate to be the base steel plate, so that the effective diameter of the crystal grain of the base steel plate obtained after annealing is makes it thinner. [00133] When bending is carried out, a tension (tensile tension) of not less than 3 MPa or more than 100 MPa is applied in which the rolling direction is set as the tension axis. If the stress is less than 3 MPa, the effect of facilitating nucleation cannot be recognized, so 3 MPa is set as the lower limit. To also facilitate nucleation to make the effective diameter of the crystal grain thin, the tension is preferably set to 5MPa or more, and is most preferably set to 7 MPa or more. On the other hand, if the tension exceeds 100 MPa, there is the case where the steel sheet is greatly deformed by the execution of the bending, so that the tension is adjusted to 100 MPa or less. To also reduce the deformation of the steel sheet, the tension is preferably adjusted to be 70 MPa or less, and is more preferably adjusted to be 50 MPa or less. By bending it is possible to make the crystal grain be thinner, that is, it is possible to achieve an effective average diameter of the crystal grain of 5 pm or less, and the maximum effective diameter of the crystal grain. Petition 870190015116, of 02/14/2019, p. 50/125 46/110 crystal of 20 gm or less, and cause the oxides from 1.0 χ 10 12 to 1.0 χ 10 16 oxides / m 2 to precipitate in the decarbonized layer so that the difference between the resistance in the decarbonized layer and the resistance the normal portion of the base material of the steel plate can be reduced. [00134] In bending, for example, processing with a bending radius of 800 mm or less is conducted using a cylinder with a radius of 800 mm or less. The greater the degree of processing, the more nucleation is facilitated, so that the bending radius is preferably adjusted to 650 mm or less. On the other hand, although the lower limit of the bending radius is not particularly adjusted, it is difficult to homogeneously bend the entire area of the steel sheet with an excessively small radius, so that the bending radius is preferably adjusted to 50 mm or more, and is most preferably set to 100 m or more. [00135] The number of fold times is adjusted to one or more times, and is preferably adjusted to twice or more since the higher the degree of processing, the more nucleation is facilitated. Although the upper limit on the number of folding times is not particularly determined, it is preferably set to 20 times or less, since it is difficult to conduct the folding 20 times or more in a retention time in the temperature region described above. Coating step [00136] Then the base steel sheet obtained as above is immersed in a coating bath. The coating bath has a composition containing mainly zinc, in which the effective amount of Al being a value resulting from subtracting the total amount of Fe from the total amount of Al in the coating bath is 0.01 to 0.18% by weight . Particularly, when the bonding treatment is carried out after the coating step, the effective amount of Al in the Petition 870190015116, of 02/14/2019, p. 51/125 The coating bath is preferably adjusted to 0.07 to 0.12 mass% to control the progress of the hot dip galvanized layer bonding. In addition, when the coating layer is not bonded, there is no problem even if the effective amount of Al in the bath is in a range of 0.28 to 0.30% by mass. [00137] The coating bath can also be one in which one or two or more elements between Pb, Sb, Si, Sn, Mg, Mn, Ni, Cr, Co, Ca, Cu, Li, Ti, Be, Bi, Sr, I, Cs, and REM are mixed, and there is sometimes a preferable case in which the corrosion resistance and the workability of the hot dip galvanized layer are improved, depending on the contents of the respective elements. [00138] Furthermore, the temperature of the coating bath is preferably adjusted to 450 ° C to 470 ° C. If the temperature of the coating bath is less than 450 ° C, the viscosity of the coating bath is greatly increased, resulting in the fact that it becomes difficult to control the thickness of the coating layer, and the external appearance of the steel sheet is impaired . On the other hand, if the temperature of the coating bath exceeds 470 ° C, a large amount of vapors are generated, and it becomes difficult to perform safe production, so that the temperature of the coating bath is preferably 470 ° C or less . [00139] In addition, if the temperature of the steel sheet when the steel sheet enters the bath is below 430 ° C, it is necessary to give a large amount of heat to the coating bath to stabilize the temperature of the coating bath to 450 ° C or more, which in practice is inappropriate. On the other hand, if the temperature of the steel sheet when the steel sheet enters the coating bath is greater than 490 ° C, it is necessary to introduce equipment to remove a large amount of heat from the coating bath to stabilize the temperature of the bath coating to 470 ° C or Petition 870190015116, of 02/14/2019, p. 52/125 48/110 less, which is inadequate in terms of production costs. Consequently, to stabilize the bath temperature, the temperature of the base steel sheet when the base steel sheet enters the coating bath is preferably 430 ° C to 490 ° C. [00140] Furthermore, in the present modality, it is preferable to carry out the bainite transformation process of, before and / or after dipping the base steel plate in the coating bath, retaining the base steel plate in a temperature range of 300 to 470 ° C for 10 to 1000 seconds, with the purpose of making the transformation of bainite happen. When the bonding treatment is carried out after the coating step, the bainite transformation process can be carried out before or after the bonding treatment. [00141] Note that when the temperature in the bainite transformation process is 430 ° C or less, there is the case that a large amount of carbon is concentrated in the untransformed austenite according to the progress of the bainite transformation, and the fraction volume of the retained austenite remained on the steel plate after cooling the steel plate until room temperature becomes large. The amount of carbon in the solid solution in austenite is reduced by reheating at a temperature higher than the temperature at which the bainite transformation takes place. For this reason, when the temperature in the bainite transformation process is 430 ° C or less. It is preferable that the bainite transformation process is limited to being carried out before immersing the base steel sheet in the coating bath, the amount of carbon in the solid solution in the untransformed austenite is reduced, and the amount of retained austenite that remains in the steel sheet after cooling the steel sheet until room temperature is reduced. [00142] There is no problem even if the bonding treatment of a hot dip galvanized layer is carried out after immersion Petition 870190015116, of 02/14/2019, p. 53/125 49/110 of the steel sheet in the coating bath. The bonding does not take place sufficiently at a temperature of less than 470 ° C, so the temperature of the bonding treatment is adjusted to 470 ° C or more. In addition, if the temperature of the bonding treatment exceeds 620 ° C, crude cementite is generated and the strength is significantly decreased, so that the temperature of the bonding treatment is adjusted to 620 ° C or less. The temperature of the bonding treatment is preferably set to 480 to 600 ° C, and is most preferably set to 490 to 580 ° C. [00143] To make the bonding of the hot dip galvanized layer happen sufficiently, the bonding treatment time is set to 2 seconds or more, and is preferably set to 5 seconds or more. On the other hand, if the bonding treatment time exceeds 200 seconds, there is a concern that overlaying of the coating layer will occur, and the properties will deteriorate. For that reason, the time for the binding treatment is set to 200 seconds or less, and is most preferably set to 100 seconds or less. [00144] Note that the bonding treatment is preferably carried out immediately after the base steel plate is immersed in the coating bath, but there is no problem even if the base steel plate is immersed in the coating bath, and then after the temperature of the coating. the hot-dip galvanized steel sheet obtained is lowered to 150 ° C or less, the steel sheet is reheated to the temperature of the bonding treatment to conduct the bonding treatment. [00145] In addition, it is preferable that the average cooling rate even when the temperature of the hot dip galvanized steel sheet or the hot dip galvanized steel sheet obtained after the coating step or after the bonding treatment if Petition 870190015116, of 02/14/2019, p. 54/125 50/110 make 150 ° C less than 0.5 ° C / s or more. This is because if the cooling rate is less than 5 ° C / s, when the untransformed austenite remains on the hot-dip galvanized steel sheet or on the hot-dip galvanized steel sheet, the bainite transformation takes place in untransformed austenite, and the concentration of carbon in austenite occurs, so that there is a case where the volume fraction of the retained austenite obtained after cooling is performed until room temperature exceeds 5%. From this point of view, the average cooling rate described above is most preferably adjusted to 1.0 ° C / s or more. [00146] Note that there is no problem even if the reheat treatment is carried out for the purpose of tempering the martensite during cooling or after cooling the hot-dip galvanized steel sheet or wire after the coating step or after the bonding treatment. If the heating temperature when carrying out the reheat treatment is less than 200 ° C, quenching does not happen sufficiently, so that the heating temperature is preferably adjusted to 200 ° C or more. In addition, if the temperature in the reheat treatment exceeds 620 ° C, the resistance deteriorates significantly, so that the temperature is preferably adjusted to 550 ° C 08 less. [00147] Note that the present invention is not limited to the modalities described above. [00148] For example, in the embodiments of the present invention, there is no problem even if the coating film made of a composite oxide containing an oxide of P and / or P is given to a surface of the galvanized layer of the galvanized steel sheet obtained by previously mentioned method. [00149] The coating film made of composite oxide containing phosphorus and / or phosphorus oxide can function as a lubricant when Petition 870190015116, of 02/14/2019, p. 55/125 51/110 the steel plate processing is carried out, resulting in the fact that the galvanized layer formed on the surface of the base steel plate can be protected. [00150] Furthermore, in the present configuration, there is no problem even if cold rolling is carried out on high-strength galvanized steel sheet cooled to room temperature, at a reduction rate of 3.00% or less for the purpose of correction of the form. EXAMPLES [00151] Examples of the present invention will be described. [00152] Plates containing chemical components (composition) from A to AC presented in Table 1 to Table 3 were cast, the hot rolling was carried out under the conditions (plate heating temperature, hot rolling finish temperature, reduction of rolling in the temperature region of 1050 ° C until the end temperature of the hot rolling) presented in Table 4 to Table 8, and the winding was carried out at the temperatures presented in Table 4 to Table 8, thus obtaining hot-rolled steel sheets . [00153] After this, the pickling was carried out on the hot rolled steel sheets, and the cold rolling under the condition (reduction ratio) presented in Table 4 to Table 8 was carried out, thus obtaining cold rolled steel sheets. Petition 870190015116, of 02/14/2019, p. 56/125 [TABLE 1] Component and chemical Ç SI Mn P s Al N O% in large scale % in large scale % in large scale % in large scale % in large scale % in large scale % in large scale % in large scale THE 0.213 0.54 1.84 0.0145 0.0060 0.043 0.0030 0.0005 Example B 0.094 1.44 2.31 0.0114 0.0026 0.041 0.0033 0.0004 Example Ç 0.174 1.87 1.87 0.0176 0.0028 0.064 0.0049 0.0013 Example D 0.087 1.00 2.41 0.0121 0.0028 0.024 0.0037 0.0023 Example AND 0.335 0.64 2.10 0.0160 0.0023 0.130 0.0042 0.0014 Example F 0.119 0.45 2.55 0.0091 0.0053 0.228 0.0055 0.0008 Example G 0.264 0.07 2.91 0.0082 0.0060 1,139 0.0063 0.0022 Example H 0.135 1.37 1.34 0.0130 0.0053 0.018 0.0041 0.0018 Example I 0.239 1.66 1.58 0.0122 0.0010 0.006 0.0051 0.0007 Example J 0.172 0.58 2.70 0.0060 0.0042 0.747 0.0061 0.0007 Example K 0.244 0.52 0.95 0.0084 0.0047 0.546 0.0038 0.0023 Example L 0.119 1.43 1.55 0.0107 0.0029 0.022 0.0022 0.0011 Example M 0.142 0.98 1.93 0.0146 0.0047 0.069 0.0024 0.0004 Example N 0.239 1.11 2.38 0.0207 0.0038 0.042 0.0018 0.0022 Example O 0.203 1.80 0.89 0.0152 0.0006 0.025 0.0055 0.0018 Example P 0.178 0.70 1.76 0.0097 0.0039 0.221 0.0029 0.0025 Example Q 0.196 0.89 1.11 0.0048 0.0004 0.142 0.0053 0.0013 Example R 0.224 0.73 1.93 0.0116 0.0052 0.354 0.0026 0.0016 Example s 0.115 1.26 1.72 0.0103 0.0027 0.073 0.0021 0.0010 Example 52/110 Petition 870190015116, of 02/14/2019, p. 57/125 [TABLE 1] CONTINUED T 0.177 1.91 1.25 0.0096 0.0024 0.020 0.0024 0.0023 Example U 0.167 0.45 2.80 0.0147 0.0052 0.379 0.0038 0.0023 Example V 0.168 0.14 2.02 0.0187 0.0046 0.736 0.0037 0.0012 Example W 0.088 0.69 1.35 0.0105 0.0062 0.054 0.0041 0.0004 Example X 0.278 0.25 3.17 0.0117 0.0017 1,021 0.0041 0.0030 Example Y 0.210 0.95 1.96 0.0157 0.0027 0.072 0.0057 0.0019 Example Z 0.178 1.14 2.06 0.0075 0.0031 0.048 0.0042 0.0006 Example AA 0.176 0.89 2.31 0.0078 0.0043 0.044 0.0020 0.0009 Example AB 0.162 0.44 1.97 0.0078 0.0013 0.660 0.0019 0.0025 Example B.C 0.124 0.94 2.13 0.0103 0.0036 0.066 0.0032 0.0006 Example AD 0.234 1.28 1.64 0.0071 0.0045 0.074 0.0019 0.0022 Example AE 0.061 1.28 2.25 0.0101 0.0043 0.036 0.0056 0.0018 Comparative example. AF 0.473 1.32 2.17 0.0091 0.0039 0.042 0.0048 0.0015 Comparative example. AG 0.184 1.26 0.12 0.0109 0.0036 0.037 0.0044 0.0013 Comparative example. BA 0.186 2.91 2.49 0.017 0.0042 0.028 0.0023 0.0009 Comparative example. BB 0.154 0.00 2.31 0.016 0.0022 0.019 0.0024 0.0013 Comparative example. BC 0.188 0.94 4.20 0.013 0.0038 0.106 0.0044 0.0011 Comparative example. BD 0.181 0.74 2.59 0.008 0.0045 2.57 0.0032 0.0015 Comparative example. BE 0.103 2.26 3.88 0.005 0.0008 0.068 0.0023 0.0003 Comparative example. 53/110 Petition 870190015116, of 02/14/2019, p. 58/125 [TABLE 2] Chemical component You Nb V Cr Ni Ass Mo B W% in large scale % in large scale % in large scale % in large scale % in large scale % in large scale % in large scale % in large scale % in large scale THEExample BExample ÇExample DExample ANDExample F 0.016 0.008 Example G 0.14 0.0007Example HExample I 0.50 0.69 Example J 0.110 Example K 0.26 Example L0.29 Example M 0.059 0.0010Example NExample O 1.24Example PExample Q 0.80 Example R 0.003 0.0540.0017Example s 0.085 Example T 0.25 0.05 Example UExample 54/110 Petition 870190015116, of 02/14/2019, p. 59/125 [TABLE 2] CONTINUED V 0.88Example W 0.28 0.10 Example X 0.0043Example YExample ZExample AAExample AB 0.11 Example B.C0.039 Example ADExample AEComparative example AFComparative example AGComparative example BAComparative example BBComparative example BCComparative example BDComparative example BEComparative example 55/110 Petition 870190015116, of 02/14/2019, p. 60/125 56/110 [TABLE 3] Compo You Nb V Cr Ni Assnente % in % in % in % in % in % inchemical pasta pasta pasta pasta pasta pastaTHE Example B Example Ç Example D Example AND Example F Example G Example H 0.0015 Example I0.0038 Example J Example K Example L Example M 0.0012Example N 0.0026Example O Example P0.0040 Example Q Example R0.0008 Example s Example T Example U 0.0027 Example V Example W0.0015 Example X Example Y 0.0030Example Z 0.0016 0.0009 Example AA0.0018 Example AB Example Petition 870190015116, of 02/14/2019, p. 61/125 57/110 Chemical componentB.C You Nb V Cr Ni Ass Example % in large scale % in large scale % in large scale % in large scale % in large scale % in large scale AD0.0041 Example AE Comparative example AF Comparative example AG Comparative example BA Comparative example BB Comparative example BC Comparative example BD Comparative example BE Comparative example [TABLE 4] Experimental Example Chemical component Hot rolling step Cold rolling stage Plate heating temperature ° C Expression 1 Lamination termination temperature ° C Average cooling rate at ° C / s Cooling temperatures at ° C Reduction ratio% 1 THE 1265 0.70 941 31 578 65 2 THE 1210 0.77 905 25 602 48 3 THE 1235 0.85 907 49 549 39 4 THE 1235 0.25 935 26 541 57 5 B 1260 0.75 910 15 604 45 6 B 1205 0.55 908 46 537 53 7 B 1185 0.28 944 32 562 45 Petition 870190015116, of 02/14/2019, p. 62/125 58/110 Experimental Example8 Chemical componentB Hot rolling step Cold rolling stage Plate heating temperature ° C1255 Expression 10.35 Lamination termination temperature ° C915 Average cooling rate at ° C / s14 Cooling temperatures at ° C 623 Reduction ratio%43 9 Ç 1270 0.68 943 21 600 61 10 Ç 1270 0.55 925 19 549 50 11 Ç 1200 0.64 887 45 564 56 12 Ç 1210 0.76 910 60 562 47 13 D 1205 0.32 920 21 575 50 14 D 1245 0.73 928 52 526 50 15 D 1215 0.50 898 26 547 43 16 D 1270 0.52 932 47 526 57 17 AND 1250 0.56 922 33 592 45 18 AND 1235 0.56 919 29 570 48 19 AND 1190 0.58 927 23 590 53 20 AND 1230 0.54 930 50 603 56 21 F 1220 0.94 937 20 607 48 22 F 1220 0.80 936 48 585 50 23 F 1265 0.18 880 16 580 50 24 F 1240 0.42 946 63 565 53 25 G 1205 0.78 942 19 626 50 26 G 1220 0.57 902 33 590 48 27 G 1235 0.74 942 24 573 54 28 G 1265 0.57 946 20 535 48 29 H 1215 0.87 937 40 565 60 30 H 1235 0.42 923 21 572 47 Petition 870190015116, of 02/14/2019, p. 63/125 59/110 [TABLE 5] Experimental Example Chemical component Hot rolling step Cold rolling stage Plate heating temperatures Expres are 1 Lamination termination temperatures Average cooling rate Cooling stop temperatures Reduction ratio ° C ° C ° C / s ° C % 31 H 1210 0.78 946 17 610 45 32 H 1260 0.78 923 33 579 20 33 I 1265 0.37 931 23 601 54 34 I 1240 0.62 913 28 604 60 35 I 1240 0.51 895 25 624 63 36 I 1215 0.41 897 13 633 53 37 J 1210 0.52 935 20 558 65 38 J 1215 0.58 915 58 565 39 39 J 1270 0.46 918 41 645 40 40 J 1240 0.49 918 25 568 60 41 K 1279 0.39 946 54 590 50 42 K 1220 0.55 892 28 536 54 43 K 1230 0.38 943 31 540 54 44 K 1015 0.72 884 30 586 41 45 L 1200 0.48 912 34 596 48 46 L 1205 0.37 914 32 560 68 47 L 1205 0.54 895 29 589 31 48 L 1200 0.59 947 41 599 48 49 M 1275 0.57 926 21 604 60 50 M 1245 0.67 916 16 563 61 51 M 1260 0.52 921 19 588 58 52 M 1250 0.44 923 48 515 45 53 N 1265 0.35 920 33 571 37 54 N 1190 0.20 921 30 562 46 55 N 1185 0.72 911 20 548 35 56 N 1260 0.77 911 25 564 85 57 O 1205 0.42 916 61 553 42 58 O 1260 0.51 912 24 566 48 59 O 1255 0.56 946 23 594 41 60 O 1250 0.69 920 45 604 62 Petition 870190015116, of 02/14/2019, p. 64/125 60/110 [TABLE 6] Experimental Example Chemical component Hot rolling step Cold rolling stage Plate heating temperatures Expression are 1 Lamination termination temperature Average cooling rate Cooling stop temperature Reduction ratio ° C ° C ° C / s ° C % 61 P 1185 0.39 937 18 629 59 62 P 1240 0.57 925 40 552 58 63 P 1200 0.51 950 17 634 60 64 P 1235 0.50 931 17 566 59 65 Q 1215 0.67 947 20 548 38 66 Q 1270 0.32 911 26 509 63 67 Q 1210 0.48 928 22 574 70 68 Q 1250 0.82 930 20 573 41 69 R 1235 0.72 923 48 539 40 70 R 1185 0.57 939 24 579 57 71 R 1225 0.57 879 50 587 67 72 R 1275 0.42 906 21 570 50 73 s 1240 0.56 934 20 619 48 74 s 1255 0.71 912 52 546 50 75 s 1220 0.60 940 24 544 39 76 s 1220 0.60 949 24 591 57 77 T 1205 0.85 941 47 572 60 78 T 1210 0.45 895 35 521 44 79 T 1255 0.47 910 27 554 53 80 T 1260 0.58 921 29 558 55 81 U 1205 0.41 905 18 568 60 82 U 1245 0.82 930 33 558 46 83 U 1275 0.23 920 50 576 43 84 U 1200 0.31 903 51 586 53 85 V 1250 0.62 943 15 633 46 86 V 1215 0.44 926 20 613 63 87 V 1225 0.50 887 27 548 50 88 V 1230 0.78 933 26 625 48 Petition 870190015116, of 02/14/2019, p. 65/125 61/110 Experimental Example89 Chemical componentW Hot rolling step Cold rolling stage Plate heating temperatures Expression are 1 Lamination termination temperature Average cooling rate Cooling stop temperature Reduction ratio ° C ° C ° C / s ° C % 1200 0.47 927 23 563 53 90 W 1220 0.70 890 18 606 50 [TABLE 7] Experimental Example Chemical component Hot rolling step Cold rolling stage Plate heating temperatures Expres are 1 Lamination termination temperature Average cooling rate Cooling stop temperature Reduction ratio ° C ° C ° C / s ° C % 91 W 1255 0.49 922 20 553 53 92 W 1280 0.36 902 30 550 60 93 X 1250 0.47 918 31 584 44 94 X 1205 0.65 920 15 623 48 95 X 1185 0.69 896 18 604 70 96 X 1260 2.35 922 30 570 38 97 Y 1225 0.18 901 12 622 47 98 Y 1210 0.62 916 12 621 59 99 Y 1245 0.55 922 66 548 56 100 Y 1270 0.50 932 22 548 72 101 Z 1265 0.45 950 34 575 55 102 Z 1210 0.41 900 24 531 45 103 Z 1180 0.56 925 22 538 47 104 Z 1225 0.77 930 26 602 47 105 AA 1225 0.49 915 15 605 60 Petition 870190015116, of 02/14/2019, p. 66/125 62/110 Experimental Example106 Chemical componentAA Hot rolling step Cold rolling stage Plate heating temperatures Expres are 10.36 Lamination termination temperature Average cooling rate Cooling stop temperature Reduction ratio ° C1245 ° C909 ° C / s25 ° C600 %61 107 AA 1240 0.47 937 36 566 48 108 AA 1215 0.84 920 34 545 47 109 AB 1200 0.84 931 18 599 65 110 AB 1255 0.75 940 18 579 58 111 AB 1235 0.51 932 36 556 40 112 AB 1255 0.72 909 19 518 57 113 B.C 1265 0.60 915 19 552 43 114 B.C 1230 0.34 931 26 606 59 115 B.C 1195 0.66 915 25 593 53 116 B.C 1245 0.04 932 29 578 48 117 AD 1215 0.55 889 20 608 44 118 AD 1215 0.61 898 55 541 53 119 AD 1185 0.34 928 40 559 54 120 AD 1275 0.53 909 16 588 54 [TABLE 8] Experimental Example Chemical component Hot rolling step Cold rolling stage Plate heating temperatures Expression1 Lamination termination temperatures Average cooling rate Cooling stop temperature Reduction ratio ° C ° C ° C / s ° C % 121 AE 1235 0.61 907 36 569 50 122 AF 1220 0.65 924 38 617 39 123 AG 1235 0.34 941 39 572 54 124 BA 1230 0.28 892 33 587 Petition 870190015116, of 02/14/2019, p. 67/125 63/110 Experimental Example125 BB chemical component Hot rolling step Cold rolling stage Plate heating temperatures Expression1 Lamination termination temperatures Average cooling rate Cooling stop temperature Reduction ratio ° C ° C ° C / s ° C % 1220 0.49 919 20 596 73 126 BC INTERRUPTED TEST DUE TO FRACTURE ON THE PLATE127 BD 1220 0.42 880 31 609 73 128 BE 1255 0.54 920 26 589 53 129 THE 1195 0.51 904 29 600 60 130 B 1240 0.03 793 37 603131 B 1300 1.40 1004 34 593 47 132 H 1245 0.46 883 41 621 50 133 F 1230 0.38 907 37 620 60 [00154] Next, the annealing was carried out under the conditions presented in Tables 9 to 13 (volume ratio between air and combustible gas in the mixed gas used for heating the preheating zone (volume of air / volume of fuel gas), heating rate at 600 to 750 ° C, partial pressure ratio between H2O and H2 in the atmosphere of the reduction zone (P (H2O) / P (H2)), maximum heating temperature, average cooling rate in the region of 740 ° C to 500 ° C, folding conditions (tension (load tension), bending radius, number of folding times)), thus obtaining the base steel sheets of experimental examples 1 to 133 (note that the experiment was interrupted in part of the experimental examples). Petition 870190015116, of 02/14/2019, p. 68/125 [TABLE 9] Experimental Example 0Chemical composition Steel type Annealing step 600 heating rateat 750 ° C Maximum heating temperature Ac3 Maximum heating temperature Average cooling rate from 740 to 500 ° C Stress and load Bending radius Number of fold times preheating zone reduction zone Air volume to fuel gas ratio P (H2O) /P (H2) ° C / s ° C ° C ° C ° C / s MPa mm times 1 THE GI 4.7 809 794 15 2.5 10 450 5 1.2 0.005 2 THE GI 4.7 813 794 19 5.2 5 350 3 0.7 0.170 3 THE GA 3.8 781 794 -13 12.9 11 400 4 1.0 0.004 4 THE GI 4.4 807 794 13 5.6 11 350 4 0.8 0.316 5 B GI 2.3 875 852 23 3.1 8 550 2 1.0 0.110 6 B GI 17.2 841 852 -11 17.0 6 450 3 1.0 0.015 7 B GA 3.9 855 852 3 5.8 12 350 2 1.0 0.138 8 B GI 1.8 862 852 10 5.4 0 550 2 1.1 0.002 9 Ç GI 3.8 859 866 -7 4.5 14 450 1 1.0 0.126 64/110 Petition 870190015116, of 02/14/2019, p. 69/125 [TABLE 9] CONTINUED 10 Ç GA 2.8 893 866 27 4.7 19 350 4 0.8 0.081 11 Ç GA 11.3 853 866 -13 4.6 4 550 2 1.0 0.355 12 Ç GI 4.5 875 866 9 6.0 13 250 3 1.0 0.068 13 D GI 3.9 813 828 -15 4.5 21 450 4 0.7 0.035 14 D GI 3.7 862 828 34 52.9 7 450 2 0.7 0.251 15 D GA 4.3 842 828 14 6.4 7 550 2 0.9 0.589 16 D GI 2.9 857 828 29 5.8 4 350 3 1.0 0.027 17 AND GI 2.1 779 785 -6 6.2 31 450 3 1.2 0.048 18 AND GA 2.4 827 785 42 3.0 9 600 3 0.9 0.062 19 AND GA 4.0 758 785 -27 18.9 10 250 1 0.9 0.155 20 AND GI 4.6 807 785 22 2.9 6 350 4 0.9 0.030 21 F GI 2.0 811 830 -19 3.3 8 450 2 0.9 0.033 22 F GI 2.2 839 830 9 16.7 7 350 2 0.8 0.263 23 F GA 2.3 834 830 4 4.0 14 550 4 0.7 0.107 24 F GI 4.7 798 830 -32 17.1 12 1250 2 0.9 0.050 25 G GI 4.0 957 950 7 23.7 9 550 2 0.9 0.389 26 G GA 9.8 922 950 -28 28.2 6 550 2 0.7 0.447 27 G GA 3.0 930 950 -20 5.6 9 500 5 0.9 0.129 28 G GI 3.8 931 950 -19 41.1 9 450 3 0.8 0.062 29 H GI 4.5 842 961 -19 6.4 8 400 4 0.9 0.024 30 H GI 3.0 877 961 16 16.5 11 450 2 0.9 0.0004 65/110 Petition 870190015116, of 02/14/2019, p. 70/125 [TABLE 10] Experimental Example Chemical composition Steel type Annealing step Heating rate600 to 750 ° C Maximum heating temperatures Ac3 Maximum heating temperatures Average cooling rate from 740 to 500 ° C Load stress Bending radius Number of fold times preheating zone reduction zone Air volume to fuel gas ratio P (H2O) /P (H2) ° C / s ° C ° C ° C ° C / s MPa mm times 31 H GA 3.5 842 861 -19 27.4 10 300 2 1.1 0.015 32 H GI 1.6 860 861 -1 4.4 10 550 3 0.8 0.026 33 I GI 4.5 810 829 -19 3.2 27 550 3 1.1 0.021 34 I GI 3.2 806 829 -23 9.0 21 350 2 0.9 0.331 35 I GA 3.5 852 829 23 4.4 10 250 7 0.8 0.031 36 I GI 2.2 839 829 10 4.1 10 300 6 0.9 0.002 37 J GI 5.0 884 921 -37 2.5 8 550 1 0.9 0.038 38 J GI 1.6 891 921 -30 5.1 11 550 2 0.8 1.74 39 J GA 7.1 956 921 35 4.3 14 450 3 1.0 0.069 40 J GI 2.8 902 921 -19 4.2 11 200 3 1.0 0.007 41 K GI 1.6 966 920 46 31.6 6 550 1 0.9 0.029 42 K GI 3.3 890 920 -30 4.1 8 550 7 0.8 0.011 43 K GA 4.6 898 920 -22 29.3 8 400 3 0.8 0.102 44 K GI 2.8 925 920 5 33.1 8 350 2 0.8 0.004 45 L GI 4.7 905 862 43 15.4 10 300 3 1.0 0.083 46 L GA 9.9 893 862 31 12.0 11 550 3 0.9 0.603 47 L GA 5.9 849 862 -13 10.7 12 450 4 0.9 0.003 48 L GI 3.3 856 862 -6 4.4 9 550 4 1.0 0.013 49 M GI 3.6 832 834 -2 5.9 5 550 4 0.8 0.030 50 M GI 4.6 847 834 13 4.9 9 550 1 1.2 0.028 66/110 Petition 870190015116, of 02/14/2019, p. 71/125 [TABLE 10] CONTINUED 51 M GA 1.9 802 834 -32 5.4 8 400 5 0.8 0.019 52 M GI 2.4 887 834 53 4.3 10 550 1 18 0.050 53 N GI 3.8 777 798 -21 20.9 18 250 4 1.0 0.017 54 N GI 2.0 786 798 -12 2.8 32 250 3 0.8 0.010 55 N GA 3.7 805 798 7 31.1 11 550 3 1.2 1,023 56 N GI 2.5 833 798 35 11.1 7 450 4 0.8 0.955 57 O GI 3.2 831 865 -34 12.4 9 350 3 0.8 0.148 58 O GI 3.5 873 865 8 11.3 34 450 5 0.9 0.007 59 O GA 2.9 910 865 45 5.7 8 450 3 1.1 1,330 60 O GA 2.5 821 865 -44 5.6 11 450 4 0.9 0.0490 67/110 Petition 870190015116, of 02/14/2019, p. 72/125 [TABLE 11] Experiment example l Chemical composition Steel type Annealing step Heating rate of600 to 750 ° C Maximum heating temperature Ac3 Maximum heating temperatures Average cooling rate from 740 to 500 ° C Load stress Folding radius Number of folding times pre-heating zone reduction zone Air volume to fuel gas ratio P (H2O) / P (H2) ° C / s ° C ° C ° C ° C / s MPa mm times 61 P GI 4.0 864 850 14 3.6 5 450 2 1.0 0.005 62 P GA 11.9 832 850 -18 6.2 17 250 3 0.9 0.046 63 P GA 3.3 819 850 -31 6.4 10 500 5 0.8 0.135 64 P GI 4.8 830 850 -20 5.0 8 350 4 0.9 0.191 65 Q GI 2.2 833 840 -7 5.2 8 450 3 1.0 0.014 66 Q GI 3.1 800 840 -40 6.8 11 300 4 0.7 0.006 67 Q GA 3.6 872 840 32 12.8 9 350 1 0.9 0.105 68 Q GI 4.3 832 840 -8 4.9 0 0.9 0.105 69 R GI 4.0 915 860 55 19.4 8 650 4 1.0 0.138 70 R GA 4.4 874 860 14 4.0 8 300 3 1.2 0.617 71 R GA 2.1 842 860 -18 24.1 11 450 3 1.0 0.093 72 R GI 2.4 870 860 10 11.4 9 350 2 0.7 0.135 73 s GI 3.3 849 861 -12 5.2 7 550 5 0.9 0.005 74 s GI 4.7 879 861 18 5.7 13 450 5 1.2 0.016 75 s GA 9.7 860 861 -1 28.4 11 350 3 0.7 0.427 76 s GI 3.1 891 861 30 3.5 6 350 4 1.1 2.32 77 T GI 1.9 849 874 -25 4.2 11 450 5 0.8 0.019 78 T GI 3.0 903 874 29 5.2 13 450 1 0.9 0.030 79 T GA 7.0 914 874 40 28.6 12 550 4 1.1 0.040 80 T GI 2.2 852 874 -22 5.3 13 550 2 0.4 0.015 68/110 Petition 870190015116, of 02/14/2019, p. 73/125 [TABLE 11] CONTINUED 81 U GI 4.2 833 839 -6 4.2 9 550 6 1.2 0.004 82 U GA 3.0 812 839 -27 3.3 10 550 3 1.0 0.059 83 U GA 4.6 873 839 34 25.4 8 700 3 1.2 0.017 84 U GI 1.7 740 839 -99 5.3 9 350 3 0.9 0.085 85 V GI 2.7 922 911 11 2.9 9 450 4 0.8 0.468 86 V GI 3.8 910 911 -1 5.4 11 550 6 0.8 0.002 87 V GA 11.5 923 911 12 6.2 6 450 2 0.8 0.245 88 V GI 2.4 906 911 -5 0.3 10 500 5 0.8 0.065 89 W GI 3.8 825 846 -21 6.4 6 550 3 1.0 0.007 90 W GA 1.8 852 846 6 5.1 25 500 2 0.9 0.076 69/110 Petition 870190015116, of 02/14/2019, p. 74/125 [TABLE 12] Experimental example Chemical composition Steel type Annealing step Heating rate of 600at 750 ° C Maximum heating temperature Ac3 Maximum heating temperature Average cooling rate from 740 to 500 ° C Load stress Bending radius Number of folding times pre-heating zone reduction zone Air volume to fuel gas ratio P (H2O) /P (H2) ° C / s ° C ° C ° C ° C / s MPa mm times 91 W GA 3.3 894 846 48 2.9 6 550 5 0.9 0.151 92 W GI 2.8 840 846 -6 21.1 14 500 3 0.9 0.0000 93 X GI 2.7 929 924 5 4.3 10 450 4 0.7 0.026 94 X GI 4.6 936 924 12 41.2 22 550 2 0.8 0.006 95 X GA 1.0 919 924 -5 2.7 8 350 4 1.0 0.170 96 X GI 2.6 890 924 -34 2.8 6 550 6 1.0 1,122 97 Y GI 2.5 794 816 -22 37.7 8 450 5 1.1 0.047 98 Y GA 3.9 819 816 3 7.3 6 450 1 1.1 0.072 99 Y GA 4.0 816 816 0 5.6 12 450 4 1.1 0.055 100 Y GI 3.6 795 816 -21 4.2 8 650 7 0.9 0.085 101 Z GI 3.2 826 824 2 6.1 30 250 4 1.2 0.479 102 Z GI 1.8 795 824 -29 21.4 10 200 4 0.8 0.575 70/110 Petition 870190015116, of 02/14/2019, p. 75/125 [TABLE 12] CONTINUED 103 Z GA 4.5 853 824 29 4.7 14 500 2 1.1 0.017 104 Z GI 3.6 850 824 26 14.9 7 500 4 0.9 0.006 105 AA GI 3.2 777 805 -28 2.9 10 550 5 1.1 0.005 106 AA GA 3.2 808 805 3 4.2 4 300 3 1.1 0.302 107 AA GA 8.3 822 805 17 2.9 17 450 7 0.9 0.123 108 AA GI 2.9 785 805 -20 5.9 12 350 2 1.0 0.135 109 AB GI 6.1 923 921 2 2.5 8 450 7 1.0 0.240 110 AB GA 1.9 903 921 -18 4.8 6 150 3 10 0.162 111 AB GA 3.3 956 921 35 5.7 5 450 2 1.0 0.004 112 AB GI 2.0 920 921 -1 38.3 7 400 2 0.7 0.029 113 B.C GI 3.8 821 830 -9 21.5 6 250 4 0.9 0.026 114 B.C GI 1.8 861 830 31 8.7 9 450 6 1.1 0.006 115 B.C GA 3.4 798 830 -32 4.6 11 450 2 1.2 0.012 116 B.C GI 1.7 856 830 26 6.4 6 450 2 0.8 0.017 117 AD GI 1.7 859 835 24 5.7 5 550 6 1.1 0.525 118 AD GA 1.8 794 835 -41 40.2 10 450 5 1.1 0.005 119 AD GA 6.1 814 835 -21 4.7 10 200 5 0.9 0.052 120 AD GI 3.7 838 835 3 3.4 29 350 3 1.0 0.001 71/110 Petition 870190015116, of 02/14/2019, p. 76/125 [TABLE 13] Experimental example Chemical composition Steel type Annealing step Heating rate from 600 to 750 ° C Maximum heating temperature Ac3 Maximum heating temperature Average cooling rate from 740 to 500 ° C Stress and load Bending radius Number of folding times preheating zone reduction zone Air volume to fuel gas ratio P (H2O) /P (H2) ° C / s ° C ° C ° C ° C / s MPa mm times 121 AE GI 2.0 837 857 -20 6.0 11 250 3 0.8 0.093 122 AF GI 2.9 756 773 -17 6.7 10 650 3 0.8 0.005 123 AG GI 2.8 854 884 -30 6.7 9 550 3 0.9 0.028 124 BA INTERRUPTED TEST DUE TO FRACTURE IN THE COLD LAMINATION STEP 125 BB GA 2.0 809 787 22 6.9 14 460 4 1.1 0.062 126 BC INTERRUPTED TEST DUE TO FRACTURE ON THE PLATE 127 BD INTERRUPTED TEST DUE TO FRACTURE OF THE WELDING ZONE AT THE RECOVERY STEP 128 BE GA 3.9 852 838 14 4.8 17 460 4 1.1 1.33 129 THE GA 2.6 816 794 22 4.0 25 460 4 0.5 0.134 130 B INTERRUPTED TEST DUE TO THE DEFECTIVE SHAPE OF THE HOT-LAMINATED STEEL SHEET 131 B GA 3.9 870 852 18 4.6 15 460 4 1.0 0.080 132 H GI 3.0 865 861 4 0.5 21 460 4 1.0 0.051 133 F GA 2.5 853 830 23 4.0 20 460 4 0.9 0.083 72/110 Petition 870190015116, of 02/14/2019, p. 77/125 73/110 [00155] Experimental example 124 is an example in which the Si content was large, and the fracture of the steel plate occurred in the cold rolling stage, resulting in the fact that the test was interrupted. [00156] Experimental example 126 is an example in which the Mn content was large, and the plate fractured even when it was subjected to the hot rolling step, resulting in the fact that the test was interrupted. [00157] Experimental example 127 is an example in which the Al content was large, and there was a fracture of the welding zone between steel sheets at the front and at the rear of the steel sheet in the annealing step, resulting in the fact that the test was stopped. [00158] Next, the bainite transformation process was carried out in which some base steel sheets outside the base steel sheets of experimental examples 1 to 133 were heated to temperatures in a temperature range presented in Table 14 to Table 18 and retained for a period of time shown in Table 14 to Table 18. [00159] Then the base steel sheets at the inlet temperatures shown in Table 14 to Table 18 were made to enter and be immersed in coating baths having effective amounts of Al and temperatures shown in Table 14 to Table 18, thus obtaining layers of hot dip galvanized steel from Experimental Examples 1 to 133. [00160] In addition, some hot-dip galvanized steel sheets outside the hot-dip galvanized steel sheets of Experimental Examples 1 to 133 were subjected to the bonding treatment in which they were heated to temperatures in a given temperature range in Table 14 to Table 18 and retained by the retention times shown in Table 14 to Table 18, thus obtaining hot-dip galvanized steel sheets Petition 870190015116, of 02/14/2019, p. 78/125 74/110 bonded (GA) of Experimental Examples 1 to 133. Steel sheets other than the above were formed as hot dip galvanized steel sheets (GI) in which the coating layers were not bonded due to the non-execution of the treatment switch-on or by adjusting the treatment temperature to less than 470 ° C. Petition 870190015116, of 02/14/2019, p. 79/125 [TABLE 14] Example of the Experiment Bainite transformation process Coating step Link Average cooling rate even when the temperature reaches 150 ° C or less after the coating or bonding step Tempering step Cold rolling Amount Temperatu ra Tempera tura of Temperatu ra Time Temperature Reduction ratio Time to Tempera tura effective Al of the bath inlet binding in retention coating steel sheettreatment second s ° C % in large scale ° C ° C ° C seconds ° C % 1 47 439 0.07 468 469 3.2 Example 2 191 419 0.12 463 443 3.6 Example 3 0.07 452 442 527 16 4.0 360Example 4 0.10 461 471 4.0 Example 5 72 373 0.07 457 460 2.2 Example 6 0.10 464 480 2.7 320Example 7 491 437 0.12 459 454 499 15 4.10.10 Example 8 0.11 456 467 5.2 Comparative example 9 0.11 459 468 4.2 260Example 10 130 411 0.09 466 472 541 40 2.7 Example 11 0.08 452 484 596 11 3.8 Example 12 0.11 461 458 3.4 Example 13 325 435 0.07 459 440 5.7 Example 14 0.08 462 479 3.1 Example 15 0.10 462 454 537 31 3.50.06 Example 75/110 Petition 870190015116, of 02/14/2019, p. 80/125 [TABLE 14] CONTINUED 16 63 416 0.11 455 441 3.2 Example 17 0.10 456 459 0.9 300Example 18 287 452 0.08 452 441 526 13 1.7 Example 19 0.07 464 444 516 20 2.8 Example 20 184 453 0.25 458 452 4.2 Comparative example 21 31 407 0.11 460 446 2.7 Example 22 179 469 0.10 459 437 2.9 Example 23 0.08 460 452 498 27 4.1 400Example 24 0.10 460 468 3.8 Comparative example 25 172 439 0.11 456 468 1.4 Example 26 207 387 0.07 458 436 491 10 2.0 Example 27 0.12 465 465 528 4 3.10.15 Example 28 6500.07 462 460 3.3 Comparative example 29 0.09 462 441 5.4 Example 30 0.12 461 444 3.4 Example 76/110 Petition 870190015116, of 02/14/2019, p. 81/125 [TABLE 15] Experimental example Bainite transformation process Coating step Link Average cooling rate even when the temperature reaches 150 ° C or less after the coating or bonding step Tempering step Cold rollingRetention time Tempera tura Effective amount of Al Coating bath temperature Steel sheet inlet temperature Connection temperature Treatment time Tempering tempering Reduction ratio second s ° C % in large scale ° C ° C ° C second ° C / sec ° C % 31 330 409 0.10 461 452 554 34 3.2 Example 32 0.07 462 433 2.9 Comparative example 33 0.09 453 464 3.7 Example 34 43 433 0.11 460 454 41.00.55 Example 35 0.11 464 481 570 10 2.5 335Example 36 0.11 457 459 4.9 Example 37 31 421 0.10 464 472 1.9 Example 38 45 447 0.09 468 465 3.0 Example 39 0.11 462 462 536 24 2.0 380Example 40 0.07 463 452 2.7 Example 41 44 444 0.07 457 450 5.0 Example 42 0.14 469 448 3.1 Example 77/110 Petition 870190015116, of 02/14/2019, p. 82/125 [TABLE 15] CONTINUED 43 92 439 0.10 461 456 542 15 2.0 Example 44 52 466 0.10 467 458 2.3 Comparative example 45 0.08 455 481 4.50.04 Example 46 0.17 465 438 608 9 1.5 Example 47 60 441 0.10 458 448 510 19 3.8 Example 48 0.11 460 456 3.2 Example 49 213 381 0.11 456 459 2.3 380Example 50 0.12 461 449 2.0 Example 51 60 456 0.11 465 461 542 42 4.5 Example 52 40 449 0.10 458 456 3.1 Example 53 308 407 0.09 461 462 4.5 Example 54 0.10 465 475 2.9 Example 55 62 440 0.12 460 479 2.5 Example 56 0.10 468 464 3.0 Comparative example 57 0.12 466 439 3.0 Example 58 286 384 0.04 451 454 3.3 Example 59 76 464 0.09 467 470 505 48 3.5 Example 60 35 447 0.10 462 438 520 1 3.8 Comparative example 78/110 Petition 870190015116, of 02/14/2019, p. 83/125 [TABLE 16] Example of the Experiment Bainite transformation process Coating step Link Average cooling rate even when the temperature reaches 150 ° C or less after the coating or bonding step Tempering step Cold rollingRetention time Temp eratur a Effective amount of Al Temperament of the coating bath Steel sheet entry temper Bonding temper Treatment time Temperature Reduction ratio second s ° C % in large scale ° C ° C ° C seconds ° C % 61 44 441 0.11 462 442 3.4 Example 62 105 368 0.09 459 464 526 15 2.20.75 Example 63 0.07 460 446 478 136 1.7 Example 64 0.07 454 451 3.6 Example 65 0.11 461 447 4.8 260Example 66 192 448 0.09 464 458 3.3 Example 67 46 371 0.09 467 447 543 20 2.2 Example 68 171 457 0.07 466 446 1.7 Comparative example 69 192 448 0.11 465 465 4.4 Example 70 0.10 459 466 482 53 2.0 Example 71 49 375 0.10 457 445 532 36 1.9 Example 72 0.07 461 473 5.1 Example 73 140 378 0.07 452 463 2.3 Example 74 0.08 455 476 3.7 330Example 75 0.12 463 464 564 18 0.7 Example 76 0.09 462 444 4.0 Comparative example 77 54 452 0.11 464 487 4.4 Example 78 49 449 0.11 463 468 587 7 3.40.20 Example 79 0.07 458 441 516 52 2.3 Example 79/110 Petition 870190015116, of 02/14/2019, p. 84/125 [TABLE 16] CONTINUED 80 45 457 0.11 453 476 4.6 Comparative example 81 0.11 461 470 4.7 280Example 82 40 462 0.08 468 474 535 25 2.6 Example 83 188 446 0.11 459 439 481 40 2.6 Example 84 0.10 464 484 3.3 Comparative example 85 0.09 463 438 3.2 Example 86 67 377 0.09 459 434 4.2 Example 87 0.11 454 451 554 23 3.7 450Example 88 0.09 459 438 4.5 Comparative example 89 0.12 451 432 5.2 Example 90 82 459 0.08 459 476 500 44 2.4 Example 80/110 Petition 870190015116, of 02/14/2019, p. 85/125 [TABLE 17] Experimental example Bainite transformation process Coating step Link Average cooling rate even when the temperature reaches 150 ° C or less after the coating or bonding step Tempering stage Temperature Cold rolling mill Reduction ratioRetention timeEffective amount of Al Coating bath temperature Inlet temperature of steel sheet Bonding temper Treatment time Temper atura second ° C % in large scale ° C ° C ° C seconds ° C % 91 208 368 0.11 462 460 562 18 2.6 Example 92 0.11 463 464 5.5 Comparative example 93 0.08 460 475 3.4 Example 94 100 462 0.11 459 439 1.8 Example 95 0.09 462 452 536 36 1.5 Example 96 0.09 465 451 4.7 Comparative example 97 0.12 458 469 3.4 350Example 98 66 461 0.12 453 439 559 8 2.2 Example 99 150 451 0.01 459 440 493 107 3.7 Example 100 0.10 465 485 526 290 3.3 Comparative example 101 178 467 0.09 456 465 3.2 Example 102 32 391 0.08 462 483 5.30.10 Example 103 0.08 462 477 529 38 4.3 370Example 104 0.08 453 457 0.7 Example 105 195 467 0.10 465 447 3.2 Example 106 0.09 466 451 537 40 4.7 Example 81/110 Petition 870190015116, of 02/14/2019, p. 86/125 [TABLE 17] CONTINUED 107 305 341 0.11 452 446 571 19 5.6 Example 108 332 397 0.00 456 460 1.8 Comparative example 109 332 410 0.11 459 477 4.80.65 Example 110 61 438 0.09 457 473 564 18 2.1 Example 111 0.08 454 447 510 29 4.0 260Example 112 178 439 0.12 461 480 659 17 4.3 Comparative example 113 0.07 461 447 3.7 380 0.35 Example 114 0.09 456 438 1.9 Example 115 94 439 0.11 454 454 560 33 1.4 Example 116 55 463 0.07 458 445 4.0 Comparative example 117 0.11 461 481 2.8 Example 118 68 372 0.11 464 440 566 15 2.5 Example 119 51 437 0.07 459 447 480 81 5.2 Example 120 0.07 463 483 2.7 Example 82/110 Petition 870190015116, of 02/14/2019, p. 87/125 [TABLE 18] Example experiment al Bainite transformation process Coating step Link Average cooling rate even when the temperature reaches 150 ° C or less after the coating or bonding step Tempering step Cold rollingRetention time Temperatur a Effective amount of Al Temperament of the coating bath Steel sheet inlet temperature Connection temperature Treatment Time Tempering temperatures Reduction ratio second s ° C % in large scale ° C ° C ° C seconds ° C % 121 132 437 0.12 462 448 5.2 Comparative example 122 103 461 0.08 460 447 5.0 Comparative example 123 54 439 0.09 452 473 4.6 Comparative example 124 Comparative example 125 79 451 0.10 462 458 533 31 2.8 Comparative example 126 Comparative example 127 Comparative example 128 92 451 0.12 463 462 569 21 2.8 Comparative example 129 0.11 461 468 521 21 4.6 Comparative example 130 Comparative example 83/110 Petition 870190015116, of 02/14/2019, p. 88/125 [TABLE 18] CONTINUED 131 0.11 460 461 523 17 3.2 Comparative example 132 0.10 463 458 1.9 Comparative example 133 94 255 0.10 464 467 548 18 3.3 Comparative example 84/110 Petition 870190015116, of 02/14/2019, p. 89/125 85/110 [00161] Hot dip galvanized steel sheets (or hot dip galvanized steel sheets bonded after bonding treatment) of Experimental Examples 1 to 133 after the coating step were cooled at average rates of cooling rates shown in Table 14 to Table 18 until their temperatures become 150 ° C or less. [00162] Note that some of the hot-dip galvanized steel sheets (or hot-dip galvanized steel sheets bonded after bonding treatment) after the coating step of experimental examples 1 to 133 were subjected to the reheat treatment at reheat temperatures shown in Table 14 to Table 18, during the cooling of the steel sheets at the average cooling rates presented in Table 14 to Table 18 until the temperatures of the steel sheets become 150 ° C or less. [00163] In addition, some of the hot-dip galvanized steel sheets (or hot-dip galvanized steel sheets bonded) from experimental examples 1 to 133 cooled to room temperature have been subjected to cold rolling for the reasons of reduction shown in Table 14 to Table 18. [00164] In each of the hot-dip galvanized steel sheets (or hot-dip galvanized steel sheets bonded) of experimental examples 1 to 133 obtained as above, microstructures in a range of 1/8 of the thickness at 3 / 8 of the thickness centered around 1/4 of the thickness of the plate from the surface were observed to measure the volume fractions. Their results are shown in Table 19 to Table 23. [00165] Among the volume fractions of the microstructures, the amount of austenite retained was measured based on the x-ray analysis, and the volume fractions of the other microstructures were obtained by cutting a cross section in the direction of the thickness parallel to the Petition 870190015116, of 02/14/2019, p. 90/125 86/110 direction of rolling of the steel plate, executing the caustication with natal in the mirror polished cross section, and observing the cross section using an FE-SEM (Field Scanning Electron Microscope). [00166] In addition, an iron content at 1/2 the thickness of each of the connected galvanized layers was measured using an EDX. Its results are shown in Table 19 to Table 23. Petition 870190015116, of 02/14/2019, p. 91/125 [TABLE 19] Example of the Experiment Chemical composition Steel type Microstructure Portion of the surface layer Plate thickness Structural fraction Diameter effective Thickness of the layer to be reduced Oxide density Average diameter of the oxide grain the grain of crystal Ferrite Bainit a Bainit a ferrític a Mars nsita nova Marten finds temper Austeni ta retained Total hard structure Others Medium Maximum % % % % % % % % pm pm pm 10 12 oxides / m2 nm mm 1 THE GI 17 33 36 10 0 2 79 1 2.4 7.0 0.52 17.0 51 1.3 2 THE GI 4 36 42 14 0 3 92 0 1.9 11.0 3.32 22.0 71 1.3 3 THE GA 23 27 24 23 0 0 74 2 1.4 12.7 0.24 9.4 57 1.6 4 THE GI 11 48 32 6 0 1 86 1 2.5 9.6 2.84 11.6 92 1.6 5 B GI 17 11 55 13 0 3 79 0 1.8 7.5 1.67 116.6 42 1.8 6 B GI 21 4 30 0 44 0 78 0 2.5 9.4 0.78 75.8 45 1.6 7 B GA 17 15 52 13 2 0 82 1 4.2 11.0 2.37 136.5 46 1.6 8 B GI 6 10 65 13 0 3 88 2 6.5 12.8 0.20 36.1 38 1.3 9 Ç GI 5 27 43 0 24 0 94 1 2.1 6.4 2.19 296.4 40 1.0 10 Ç GA 18 12 50 19 0 0 81 1 2.5 7.3 2.70 321.2 37 1.5 11 Ç GA 23 7 58 11 0 1 76 0 3.7 11.0 3.30 442.5 43 1.7 12 Ç GI 8 9 65 15 0 3 89 0 1.3 9.4 1.40 121.2 50 1.6 13 D GI 34 22 32 8 0 2 62 2 2.9 9.0 1.87 46.2 50 1.6 14 D GI 6 43 0 42 4 4 89 1 1.0 8.4 4.26 91.2 50 1.6 15 D GA 8 30 46 12 0 2 88 2 2.8 8.8 5.26 69.0 60 1.3 16 D GI 17 25 43 13 0 0 81 2 2.1 8.0 1.30 96.9 45 1.6 17 AND GI 20 34 38 0 8 0 80 0 1.9 12.3 1.50 10.7 83 1.8 18 AND GA 11 31 49 7 0 2 87 0 1.7 10.5 2.04 16.5 82 2.4 19 AND GA 13 22 23 42 0 0 87 0 1.3 10.7 2.95 20.1 78 1.7 87/110 Petition 870190015116, of 02/14/2019, p. 92/125 [TABLE 19] CONTINUED 20 AND GI 17 34 41 3 0 3 78 2 2.6 10.4 1.09 22.1 68 1.4 21 F GI 42 19 30 6 0 2 55 1 0.7 7.8 1.89 24.7 63 1.3 22 F GI 6 41 38 12 0 3 91 0 1.4 12.8 4.78 30.0 76 1.3 23 F GA 17 30 40 0 13 0 83 0 2.7 8.7 2.20 15.6 82 1.5 24 F GI 39 15 14 27 0 3 56 2 57 13.6 2.08 25.3 65 1.7 25 G GI 3 41 24 28 2 2 95 0 1.3 10.6 3.41 80.2 52 1.5 26 G GA 12 48 16 22 0 0 86 2 3.7 9.0 3.76 49.3 58 12.0 27 G GA 20 34 24 18 0 2 76 1 0.9 8.3 2.68 41.2 58 1.3 28 G GI 12 37 40 0 0 10 77 1 1.5 10.1 1.86 96.0 37 1.3 29 H GI 31 0 53 13 0 3 66 0 1.2 4.4 0.83 40.4 56 1.8 30 H GI 9 11 38 37 4 0 90 1 1.2 6.7 0.25 24.7 33 1.6 88/110 Petition 870190015116, of 02/14/2019, p. 93/125 [TABLE 20] Example of the Experiment Chemical composition Steel type Microstructure Portion of the surface layer Plate thickness Structural fraction Effective diameter of the crystal grain Thickness of the decarburized layer Oxide density Diameter of the oxide grain Ferrit a Bain ita Bainit a ferrític a Marten is new Marten finds temper Auste nita retained Total hard structure Others Medium Maximum % % % % % % % % pm pm pm 10 12 oxides / m2 nm mm 31 H GA 26 10 58 4 0 2 72 0 1.2 9.4 0.51 31.7 58 1.8 32 H GI 23 10 59 6 0 0 75 2 4.2 21.4 1.77 70.7 46 2.6 33 I GI 25 13 49 11 0 2 73 0 3.3 7.7 0.98 64.6 50 1.3 34 I GI 19 8 59 13 0 0 80 1 2.1 7.4 4.00 178.8 52 1.2 35 I GA 9 23 52 0 16 0 91 0 1.4 8.7 1.53 86.1 52 1.9 36 I GI 16 10 59 13 0 1 82 1 1.9 6.5 0.72 61.0 30 1.3 37 J GI 31 21 35 13 0 0 69 0 2.7 5.6 1.24 80.0 52 1.3 38 J GI 24 53 9 13 0 0 75 1 2.3 9.2 5.79 62.6 70 1.5 39 J GA 9 34 40 0 17 0 91 0 3.1 9.9 1.37 49.3 62 1.8 40 J GI 27 31 28 14 0 0 73 0 3.1 8.2 0.31 17.5 54 0.8 41 K GI 0 32 25 39 0 4 96 0 1.2 9.2 1.65 8.6 84 1.8 42 K GI 25 33 37 5 0 0 75 0 1.2 9.9 1.28 8.0 74 1.5 43 K GA 12 29 35 19 0 3 83 2 1.5 6.0 1.96 9.5 88 1.3 44 K GI 0 31 25 42 0 2 98 0 3.9 20.5 0.78 7.0 64 1.3 89/110 Petition 870190015116, of 02/14/2019, p. 94/125 [TABLE 20] CONTINUED 45 L GI 10 18 51 19 0 0 88 2 3.0 7.7 2.79 99.0 58 1.3 46 L GA 0 16 56 26 0 2 98 0 3.4 7.8 3.43 116.8 55 1.8 47 L GA 26 7 61 5 0 0 73 1 2.5 7.1 0.48 32.3 47 1.6 48 L GI 18 24 51 7 0 0 82 0 2.3 9.8 1.17 27.9 59 1.6 49 M GI 22 18 48 0 12 0 78 0 2.6 9.5 1.28 1.8 77 1.4 50 M GI 7 33 46 11 0 3 90 0 2.5 8.3 1.13 30.0 60 1.4 51 M GA 40 19 32 8 0 1 59 0 1.8 10.4 1.77 19.9 70 1.3 52 M GI 15 24 48 12 0 0 84 1 1.7 10.1 19.50 32.2 61 1.3 53 N GI 14 21 49 15 0 0 85 1 2.3 10.7 0.60 33.5 58 1.3 54 N GI 28 15 44 13 0 0 72 0 13 6.5 0.74 45.2 47 1.2 55 N GA 4 24 40 29 0 3 93 0 0.7 5.1 6.03 107.0 64 1.6 56 N GI 4 20 45 30 0 1 95 0 3.9 22.4 4.26 271.1 50 2.0 57 O GI 30 5 39 23 0 1 67 2 2.9 6.8 2.76 46.1 66 1.5 58 O GI 0 15 66 15 0 3 96 1 1.7 9.1 0.82 95.1 32 1.4 59 O GA 0 35 46 17 0 2 98 0 1.9 12.8 6.16 62.4 65 1.4 60 O GA 39 9 40 10 0 0 59 2 1.6 6.0 1.27 68.1 55 1.3 90/110 Petition 870190015116, of 02/14/2019, p. 95/125 [TABLE 21] Experimental example Chemical composition Steel type Microstructure Portion of the surface layer Plate thickness Structural fraction Effective diameter of the crystal grain Thickness of the decarburized layer Oxide density Average diameter of the oxide grain Ferrit a Bainit a Bainit a ferrític a Mars nsita nova Marten finds temper Auste nita retained Total hard structure Others Medium Max mo % % % % % % % % pm pm pm 10 12 oxides / m2 nm mm 61 P GI 14 30 53 0 0 3 83 0 3.4 8.6 0.76 18.6 54 1.3 62 P GA 33 58 0 7 0 0 65 2 4.6 8.0 2.15 26.3 65 1.5 63 P GA 33 35 30 2 0 0 67 0 3.4 8.7 2.98 28.3 73 1.5 64 P GI 28 28 42 0 0 2 70 0 3.1 8.7 2.75 48.2 61 1.4 65 Q GI 15 31 24 0 28 2 83 0 0.7 5.6 1.56 10.9 72 1.6 66 Q GI 35 20 45 0 0 0 65 0 2.8 7.5 1.23 7.9 69 1.6 67 Q GA 0 31 69 0 0 0 100 0 2.7 0.4 2.89 24.1 70 1.8 68 Q GI 19 32 49 0 0 0 81 0 6.1 20.2 2.47 17.6 85 1.8 69 R GI 3 29 54 12 0 2 95 0 1.7 9.8 2.94 47.0 56 2.0 70 R GA 13 34 40 10 0 3 84 0 2.8 7.3 5.56 56.9 72 1.0 71 R GA 12 38 27 20 0 3 85 0 1.2 6.5 2.31 49.2 61 1.0 72 R GI 13 19 49 17 0 0 85 2 1.6 7.4 2.51 27.1 71 1.0 73 s GI 17 21 55 5 0 2 81 0 3.3 7.4 0.80 25.5 45 1.0 74 s GI 10 23 60 0 7 0 90 0 1.8 9.2 0.98 3.5 55 1.3 75 s GA 6 47 25 17 0 3 89 2 3.1 9.9 5.62 148.4 45 1.5 76 s GI 18 11 64 4 0 0 79 3 1.8 7.6 18.30 32.9 109 1.6 91/110 Petition 870190015116, of 02/14/2019, p. 96/125 [TABLE 21] CONTINUED 77 T GI 26 0 64 8 0 0 72 2 0.8 6.2 1.00 43.7 58 1.4 78 T GI 0 0 86 12 0 2 98 0 2.5 6.0 1.33 55.0 49 1.7 79 T GA 10 30 30 20 5 3 85 2 3.5 9.0 1.00 44.3 58 1.6 80 T GI 33 0 58 7 0 0 65 2 1.9 6.7 0.00 1.7 81 U GI 13 39 31 15 0 0 85 2 4.5 7.8 0.48 23.2 46 1.5 82 U GA 45 44 0 9 0 2 53 0 1.0 9.1 1.25 22.5 70 1.3 83 U GA 3 35 43 17 0 0 95 2 3.6 10.9 0.94 31.5 52 1.3 84 U GI 76 2 6 16 0 0 24 0 1.3 10.1 2.48 28.2 70 1.3 85 V GI 15 49 20 13 0 2 82 1 2.0 14.0 3.91 21.8 78 0.8 86 V GI 16 25 43 15 0 0 83 1 3.9 11.8 1.08 12.5 41 1.2 87 V GA 7 48 33 10 0 2 91 0 4.5 8.5 3.48 9.3 86 1.4 88 V GI 56 20 10 0 0 0 30 14 5.4 12.3 1.59 18.5 65 1.6 89 W GI 40 30 21 9 0 0 60 0 1.6 10.0 0.80 19.5 56 1.6 90 W GA 12 43 40 4 0 1 87 0 1.0 9.1 2.11 13.5 79 1.3 92/110 Petition 870190015116, of 02/14/2019, p. 97/125 [TABLE 22] Example of the Experiment Chemical composition Steel type Microstructure Portion of the surface layer Plate thickness Structural fraction Effective diameter of the crystal grain Thickness of the decarburized layer Density and oxide Average diameter of the oxide grain Ferri ta Bainit a Bainit a ferrític a Mars nsita nova Marten finds temper Auste nita retained Total hard structure Others Medium Max mo % % % % % % % % who who who 10 12 oxides / m 2 nm mm 91 W GA 21 55 24 0 0 0 79 0 2.5 8.9 1.85 15.1 82 1.0 92 W GI 14 16 29 38 0 0 83 3 2.5 6.5 0.00 10 93 X GI 4 36 37 19 0 3 92 1 2.1 11.0 3.19 110.8 31 1.5 94 X GI 0 42 33 19 3 0 97 3 2.2 9.6 0.89 53.0 34 1.3 95 X GA 17 31 28 17 4 2 80 1 2.0 7.3 1.95 74.9 54 1.3 96 X GI 14 32 25 24 0 3 81 2 6.9 21.9 6.76 103.2 53 1.0 97 Y GI 23 9 17 0 47 3 73 1 1.7 10.6 2.00 48.6 48 2.3 98 Y GA 14 34 43 7 0 0 84 2 2.1 10.7 1.14 29.3 69 1.3 99 Y GA 14 24 53 5 0 3 82 1 2.1 8.8 1.17 38.1 58 1.3 100 Y GA 29 17 47 7 0 0 71 0 2.3 8.5 2.37 49.2 65 1.5 101 Z GI 3 25 59 10 0 3 94 0 2.5 9.4 4.13 58.5 75 1.5 93/110 Petition 870190015116, of 02/14/2019, p. 98/125 [TABLE 22] CONTINUED 102 Z GI 20 11 36 30 0 2 77 1 1.8 8.2 7.04 81.5 53 1.8 103 Z GA 16 21 52 9 0 2 82 0 2.1 9.4 0.62 27.5 66 2.0 104 Z GI 0 29 37 29 0 0 95 5 1.7 7.8 0.98 26.9 54 0.7 105 AA GI 37 15 38 7 0 2 60 1 3.7 7.3 0.29 20.9 48 1.6 106 AA GA 20 45 23 11 0 0 79 1 1.6 8.8 2.98 34.0 83 1.4 107 AA GA 8 37 41 10 0 4 88 0 4.1 12.6 2.15 54.2 61 1.6 108 AA GI 34 19 37 10 0 0 66 0 1.5 7.3 2.46 27.1 73 1.6 109 AB GI 23 38 35 0 0 3 73 1 2.6 8.6 3.92 22.3 75 1.4 110 AB GA 24 42 30 3 0 0 75 1 2.0 7.0 3.09 29.1 65 1.3 111 AB GA 4 36 55 5 0 0 96 0 1.4 8.9 0.26 8.5 63 1.3 112 AB GI 5 50 32 0 0 0 82 13 0.8 8.9 2.45 20.6 65 13.0 113 B.C GI 13 9 24 0 49 5 82 0 1.5 8.9 2.15 55.7 42 1.2 114 B.C GI 8 30 49 10 0 3 89 0 1.5 8.6 0.24 16.0 61 1.2 115 B.C GA 47 15 31 7 0 0 53 0 2.7 7.8 0.29 20.0 61 1.2 116 B.C GI 16 24 49 11 0 0 84 0 4.3 21.8 1.44 41.5 54 1.5 117 AD GI 2 17 74 7 0 0 98 0 2.0 10.6 4.63 60.2 72 1.3 118 AD GA 29 10 33 20 5 3 68 0 1.2 6.8 0.37 18.8 55 1.3 119 AD GA 33 19 44 0 0 4 63 0 4.8 9.9 2.82 42.2 61 1.5 120 AD GI 5 18 70 4 0 3 92 0 2.3 7.3 0.42 30.6 34 1.6 94/110 Petition 870190015116, of 02/14/2019, p. 99/125 [TABLE 23] Example of the Experiment Chemical composition Steel type Microstructure Portion of layer of surface Plate thickness Structural fraction Effective diameter of the crystal grain Thickness of the decarburized layer Oxide density Diameter of the oxide grain Ferrit a Bainit a Ferritic Bainite Marten is new Marten finds temper Austeni ta retained Total hard structure Others Medium Max mo % % % % % % % % μm μm μm 10 12 oxides / m2 nm mm 121 AE GI 43 11 36 8 0 0 55 2 1.9 8.4 2.73 65.0 54 1.3 122 AF GI 25 13 30 27 0 4 70 1 2.4 8.5 1.00 24.6 48 1.3 123 AG GI 34 19 37 0 0 0 56 10 2.1 10.1 1.27 8.9 83 1.3 124 BA 125 BB GA 17 57 10 2 0 2 69 12 4.1 13.2 2.74 0.2 97 1.1 126 BC 127 BD 128 BE GA 36 5 19 28 7 3 59 2 3.8 1.35 4.15 10300 31 1.5 129 THE GA 32 15 6 25 20 2 66 0 3.9 15.6 1.23 0A 512 1.3 130 B 131 B GA 13 11 45 20 10 1 86 0 73 22.0 1.75 26.4 61 1.7 132 H GI 67 5 8 17 0 3 30 0 4.5 16.2 2.29 49.5 85 1.8 133 F GA 24 3 6 0 62 2 71 3 1.2 9.3 1.67 36.0 65 1.4 95/110 Petition 870190015116, of 02/14/2019, p. 100/125 96/110 [00167] In addition, the average effective diameter of the crystal grain, the maximum effective diameter of the crystal grain, and the decarbonized layer (thickness, density of the oxides, average diameter of the oxide grains) of each of the examples Experiments 1 to 133 were measured using a method to be described below. Its results are shown in Table 19 to Table 23. [00168] Average effective diameter of the crystal grain, maximum effective diameter of the crystal grain [00169] The cross section in the thickness direction parallel to the rolling direction of each of the hot-dip galvanized steel sheets (or steel sheets) hot dip galvanized alloys) from Experimental Examples 1 to 133 was finished to be a mirrored surface, and the crystal orientation of the BCC iron (centered body cubic structure) was measured by performing a high crystal orientation analysis resolution based on the EBSD method using a FE-SEM in the regions of 50000 pm 2 in total in a range of 1/8 of the thickness to 3/8 of the thickness centered around 1/4 of the plate thickness from the surface, adjusting the measurement step to 0.5 pm or less. [00170] Furthermore, the edge on which the disorientation of the plane (100) has become at least 10 ° or more, between adjacent measuring points, has been defined as the effective contour of the crystal grain. The grain contour map was created using the effective measured crystal grain contour, lines, whose lengths were 300 pm or more in total, parallel to the rolling direction were written on the grain contour map, and the value obtained dividing the total lengths of the lines by the number of intersections of the lines with the effective contour of the crystal grains was adjusted to be the effective average diameter of the crystal grains. [00171] Decarbonized plate thickness Petition 870190015116, of 02/14/2019, p. 101/125 97/110 [00172] The cross section in the thickness direction parallel to the rolling direction of each of the hot-dip galvanized steel sheets (or hot-dip galvanized steel sheets attached) of Experimental Examples 1 to 133 has been finished to be a mirrored surface, and observed using m FE-SEM to measure the thickness of the decarbonized layer. Note that the thickness of the decarbonized layer was measured in three positions or more by steel plate, and the average thickness value was adjusted to be the thickness of the decarbonized layer. [00173] Oxide density, Average grain diameter of the oxides [00174] The cross section in the thickness direction parallel to the rolling direction of each of the hot-dip galvanized steel sheets (or hot-dip galvanized steel sheets) of Experimental Examples 1 to 133 was finished to be a mirrored surface, and the oxide density was calculated by observing the 7 pm 2 cross-section using an FE-SEM to counter the number of oxides, or using if a required observation area until when 1000 oxides are counted. In addition, the average grain diameter of the oxides was calculated by averaging the diameters of equivalent circles from 100 to 1000 oxides selected at random. [00175] In addition, the toughness of each of the experimental examples 1 to 133 was measured using a method to be described below. Its results are shown in Table 24 to Table 28. [00176] Tenacity (impact absorbing energy (-40 ° C), brittle fracture rate) [00177] Since the thickness of each of the galvanized steel sheets by hot dip (or bonded hot dip galvanized steel sheets) from experimental examples 1 to 133 is fine Petition 870190015116, of 02/14/2019, p. 102/125 98/110 to be 0.5 to 3.5 mm, it is difficult to conduct an accurate test using a piece of steel sheet. Consequently, the steel sheets were overlapped, connected by a screw, and processed in a predetermined form after confirming that there was no gap between the steel sheets, thus preparing a stacked Charpy specimen. The number N of steel sheets to be superimposed was adjusted so that [late thickness] χ N became as close as 10 mm. For example, when the thickness of the plate was 1.8 mm, N was adjusted to 6, and the total thickness of the cover was adjusted to 10.8 mm. [00178] Charpy's stacked specimen has a cross section in the direction of thickness parallel to the lamination direction that is the fracture surface, so that it was collected by adjusting the width direction of the plate to the longitudinal direction. The impact absorbing energy of the steel plate was obtained by dividing the total absorption energy in an impact test by the fracture surface area 0.8 x [late thickness] x N, and evaluated as absorption energy by unit to (-40 ° C). [00179] The fracture surface of the steel plate has a fine crystal grain diameter, so that it is not possible to distinguish the surface of a fragile fracture and the surface of a ductile fracture using an optical microscope or magnifying glass. Consequently, the fracture surface was observed using an SEM, in order to determine the brittle fracture rate. [00180] The measurement was conducted based on conditions other than those above according to JIS Z 2242. Petition 870190015116, of 02/14/2019, p. 103/125 99/110 [TABLE 24] Example of Experi mental Property Steel type External appearance Peeling the coating Traction property Low temperature impact resistance property Elasticity limit Tensile strength Total Stretch Fragile Fracture Rate Energy absorption (-40 ° C) MPa MPa % % J / cm 2 1 O O 854 1204 17 0 50 Example 2 O O 1127 1441 12 0 65 Example 3 O O 968 1452 13 0 47 Example 4 O O 797 1081 20 0 57 Example 5 O O 996 1425 10 0 47 Example 6 O O 1321 1480 9 0 42 Example 7 O O 897 1278 13 0 49 Example 8 O O 931 1213 13 64 35 Comparative example 9 O O 1220 1502 11 0 51 Example 10 O O 1002 1430 10 0 45 Example 11 O O 800 1196 16 0 47 Example 12 O O 1029 1370 12 0 46 Example 13 O O 797 1324 14 0 51 Example 14 O O 1367 1760 9 0 44 Example 15 O O 951 1293 14 0 53 Example 16 O O 648 949 23 0 62 Example 17 O O 923 1295 15 0 58 Example 18 O O 946 1276 14 0 43 Example 19 O O 1343 1868 6 0 47 Example 20 X O 811 1171 19 0 42 Comparative example 21 O O 685 1151 19 0 52 Example 22 O O 999 1263 16 0 44 Example 23 O O 1014 1284 15 0 47 Example 24 O O 748 1148 17 290 27 Comparative example 25 O O 1016 1305 13 0 68 Example 26 O O 996 1343 14 0 41 Example 27 O O 1033 1516 9 0 36 Example 28 O O 842 1172 20 100 13 Comparative example 29 O O 813 1342 13 0 45 Example 30 O O 1209 1621 8 0 47 Example Petition 870190015116, of 02/14/2019, p. 104/125 100/110 [TABLE 25] Example of Experi mental Property Steel type External appearance Peeling the coating Traction property Low temperature impact resistance property Elastic limit of Tensile strength Total elongation Fragile fracture rate Energy absorption (-40 ° C) MPa MPa % % J / cm 2 31 O O 821 1236 16 0 45 Example 32 O O 723 1072 13 55 45 Comparative example 33 O O 929 1341 12 0 36 Example 34 O O 1047 1496 13 0 56 Example 35 O O 1233 1389 10 0 46 Example 36 O O 1145 1420 9 0 41 Example 37 O O 924 1473 11 0 54 Example 38 O O 839 1294 13 0 42 Example 39 O O 1122 1456 11 0 39 Example 40 O O 885 1367 11 0 54 Example 41 O O 1087 1493 10 0 60 Example 42 O O 784 1185 14 0 52 Example 43 O O 1074 1315 12 0 44 Example 44 O O 1289 1625 5 100 8 Comparative example 45 O O 956 1263 14 0 52 Example 46 O O 1153 1418 11 0 78 Example 47 O O 813 1218 13 0 55 Example 48 O O 797 1158 17 0 55 Example 49 O O 981 1275 13 0 51 Example 50 O O 841 1104 16 0 47 Example 51 O O 806 1201 17 0 55 Example 52 X O 656 876 18 0 45 Comparative example 53 O O 866 1216 15 0 62 Example 54 O O 978 1333 12 0 47 Example 55 O O 1035 1520 8 0 57 Example 56 O O 978 1380 13 13 47 Comparative example 57 O O 998 1452 7 0 46 Example 58 O O 973 1330 14 0 80 Example 59 O O 1057 1540 8 0 53 Example 60 O X 703 1236 16 0 43 Comparative example Petition 870190015116, of 02/14/2019, p. 105/125 101/110 [TABLE 26] Example Experime ntal Property Steel type External appearance Peeling the coating Traction property Low temperature impact resistance property Elasticity limit Tensile strength Along ament the total Fragile fracture rate Energy absorption (-40 ° C) MPa MPa % % J / cm 2 61 O O 742 1022 20 0 51 Example 62 O O 580 982 22 0 53 Example 63 O O 594 1001 21 0 60 Example 64 O O 615 988 23 0 46 Example 65 O O 923 1292 14 0 55 Example 66 O O 519 937 22 0 70 Example 67 O O 952 1164 14 0 88 Example 68 O O 720 1009 16 89 23 Comparative example 69 O O 972 1296 14 0 61 Example 70 O O 891 1237 13 0 58 Example 71 O O 860 1294 15 0 45 Example 72 O O 1035 1361 10 0 46 Example 73 O O 778 1058 19 0 48 Example 74 O O 957 1222 15 0 59 Example 75 O O 1006 1334 15 0 48 Example 76 O O 582 865 18 0 48 Comparative example 77 O O 899 1359 12 0 54 Example 78 O O 980 1255 13 0 89 Example 79 O O 1020 1387 12 0 40 Example 80 O O 722 1209 16 10 35 Comparative example 81 O O 977 1375 13 0 45 Example 82 O O 636 1031 15 0 56 Example 83 O O 1094 1417 9 0 53 Example 84 O O 580 1090 18 100 12 Comparative example 85 O O 954 1330 16 0 48 Example 86 O O 1022 1416 13 0 54 Example 87 O O 885 1182 18 0 46 Example 88 O O 346 813 16 34 29 Comparative example 89 O O 627 1107 18 0 44 Example 90 O O 689 979 20 0 52 Example Petition 870190015116, of 02/14/2019, p. 106/125 102/110 [TABLE 27] Example Experime ntal Property Steel type External appearance Peeling the coating Traction property Low temperature impact resistance property Elastic limit of Tensile strength Total elongation Fragile fracture rate Energy absorption (-40 ° C) MPa MPa % % J / cm 2 91 O O 484 926 22 0 56 Example 92 X X 861 1203 15 9 40 Comparative example 93 O O 863 1323 13 0 48 Example 94 O O 1000 1300 9 0 64 Example 95 O O 998 1372 13 0 39 Example 96 O O 906 1324 10 26 35 Comparative example 97 O O 1077 1418 11 0 40 Example 98 O O 811 1131 16 0 55 Example 99 O O 988 1362 16 0 46 Example 100 O X 902 1407 11 0 39 Comparative exampleExample 101 O O 938 1217 16 0 67 102 O O 1086 1557 11 0 36 Example 103 O O 861 1239 14 0 59 Example 104 O O 582 950 16 0 73 Example 105 O O 633 1109 19 0 48 Example 106 O O 840 1210 13 0 63 Example 107 O O 1020 1380 12 0 43 Example 108 O X 636 1038 17 0 52 Comparative example 109 O O 654 992 19 0 41 Example 110 O O 584 929 23 0 67 Example 111 O O 916 1159 18 0 52 Example 112 X X 560 784 11 0 44 Comparative example 113 O O 1041 1390 11 0 42 Example 114 O O 974 1267 15 0 41 Example 115 O O 657 1077 18 0 55 Example 116 O O 930 1271 14 7 45 Comparative example 117 O O 1163 1508 10 0 61 Example 118 O O 1000 1514 12 0 47 Example 119 O O 576 961 25 0 38 Example 120 O O 1013 1293 16 0 48 Example Petition 870190015116, of 02/14/2019, p. 107/125 103/110 [TABLE 28] Example Experime ntal Property Steel type External appearance Peeling the coating Traction property Low temperature impact resistance property Elasticity limit Tensile strength Along ament the total Fragile fracture rate Energy absorption (-40 ° C) MPa MPa % % J / cm 2 121 O O 403 806 19 0 45 Comparative example 122 X X 1083 2047 7 100 16 Comparative example 123 O O 506 837 18 0 65 Comparative example 124 O O Comparative example 125 O O 621 849 15 11 36 Comparative example 126 O O Comparative example 127 O O Comparative example 128 X X 499 1450 12 35 21 Comparative example 129 O O 791 1236 15 100 12 Comparative example 130 O O Comparative example 131 O O 697 1078 14 78 17 Comparative example 132 O O 599 1106 17 100 15 Comparative example 133 O O 804 839 12 0 38 Comparative example [00181] Table 24 to Table 28 represent the results obtained by evaluating the properties of hot-dip galvanized steel sheets (or hot-dip galvanized steel sheets linked from experimental examples 1 to 133 using methods to be described) below. [00182] The tensile specimen based on JIS Z 2201 was collected from each of the hot-dip galvanized steel sheets (or from the hot-dip galvanized steel sheets) Petition 870190015116, of 02/14/2019, p. 108/125 104/110 linked) of Experimental Examples 1 to 133, and the tensile test was conducted based on JIS Z 2241 to measure the yield strength YS, the tensile strength TS and the total elongation EL. [00183] The external appearance of a steel sheet surface was evaluated by visual determination of the state of peeling occurrence. X indicates a steel plate in which peeling with a diameter of 0.5 mm or more has been observed, and thus the steel plate was outside the tolerance range in terms of external appearance, and O indicates a steel plate different from above, having an external appearance that is practically tolerable. [00184] In addition, to assess the adhesion of the coating during processing in which a compression stress is applied, a 60 ° V-fold test was performed and, after that, a tape was attached to the inside of the folded portion, and the tape was removed. The adhesion capacity of the coating was assessed by the peeling state of the peeled coating layer along with the tape. X indicates a steel sheet that is practically not tolerable since the stripping width is 7.0 m or more, and O indicates a steel sheet different from the above, having a coating adherence capacity that is practically tolerable. [00185] As shown in Table 24 to Table 28, all the experimental examples being the examples of the present invention outside of the experimental examples 1 to 133 have a good external appearance without peeling, had TS tensile strength of 900 MPa or more, and had no fragile fracture surface. In addition, in all the experimental examples being the examples of the present invention, the evaluation regarding peeling of the coating was 0, the adhesion capacity was excellent, and the sufficient elasticity limit and total elongation were obtained. [00186] On the contrary, in the experimental examples from the examples Petition 870190015116, of 02/14/2019, p. 109/125 105/110 comparisons outside of experimental examples 1 to 133, there was no example in which peeling of the coating and peeling had not occurred, the tensile strength TS was 900 MPa or more, and the brittle fracture surface was not observed. [00187] In experimental example 121, the amount of C added was small, and the hard structures could not be obtained, so that the resistance was lower. [00188] In experimental example 122, the amount of C added was large, the toughness was insufficient, and the brittle fracture rate was 100%. [00189] In experimental example 123, the amount of Mn added was small, and a large amount of soft structures was formed during cooling after annealing, so that the resistance was insufficient. [00190] Experimental example 32 is an example in which the reduction rate in cold rolling was low, and with that the maximum effective diameter of the crystal grain was large, the toughness was insufficient, and the fragile fracture surface was observed . [00191] Experimental example 44 is an example in which the heating temperature of the plate in hot rolling was low, and thus the maximum effective diameter of the crystal grain was large, the toughness was insufficient, and the fracture surface fragile was observed, [00192] Experimental example 56 is an example in which the ratio of reduction in cold rolling was high, and thus the maximum effective diameter of the crystal grain was large, the toughness was insufficient, and the fracture surface fragile was observed. [00193] Experimental example 96 is an example in which the reduction of lamination in hot rolling was large, and with that the effective average diameter of the crystal grain and the maximum effective diameter of the crystal grain were large, the toughness was insufficient , and the surface of Petition 870190015116, of 02/14/2019, p. 110/125 106/110 fragile fracture was observed. [00194] Experimental example 116 is an example in which the reduction in lamination in hot rolling was low, and thus the maximum effective diameter of the crystal grain was large, the toughness was insufficient, and the brittle fracture surface was observed . [00195] Experimental example 8 is an example in which no load stress was applied in the annealing step, and with that the effective average diameter of the crystal grain was large, the toughness was insufficient, and the fragile fracture surface was observed . [00196] Experimental example 20 is an example in which the effective amount of Al in the coating bath was excessive in the coating step, with which the peeling occurred and the external appearance was not good. [00197] Experimental example 24 is an example in which the bending radius when bending was large in the annealing step, and with that the effective mean diameter of the crystal grain was large, the toughness was insufficient, and the fracture surface fragile was observed. [00198] Experimental example 28 is an example in which the bainite transformation process was carried out after immersing the steel sheet in the coating bath, so that the steel sheet was cooled to room temperature in a state where the carbon was concentrated in the untransformed austenite, in which the amount of austenite retained was large, the tenacity was insufficient, and the surface of the fragile fracture was observed. For this reason, although the retention time in the bainite transformation process is in the range of the present invention, experimental example 28 is not the example, but a comparative example (indicated by in the Table). [00199] Experimental example 52 is an example in which the volume ratio between the fuel gas and the air was large, and with that the thickness of the decarbonized layer was thick, the Petition 870190015116, of 02/14/2019, p. 111/125 107/110 peeling, and the resistance was insufficient. [00200] Experimental example 60 is an example in which the bonding treatment time was short, and with that the peeling of the coating occurred. [00201] Experimental example 68 is an example in which no bending was carried out, and thus the effective average diameter of the crystal grain and the maximum effective diameter of the crystal grain were large, the toughness was insufficient, and the fracture surface fragile was observed. [00202] Experimental example 76 is an example in which the partial pressure ratio between H2O and H2 was high, and with that the thickness of the decarbonized layer was thick, and the resistance was insufficient. [00203] Experimental example 80 is an example in which the volume ratio between the fuel gas and the air was small, and with that the decarbonized layer was not formed, the tenacity was insufficient and the fragile fracture surface was observed. [00204] Experimental example 84 is an example in which the maximum heating temperature in the annealing step low wire, and with that the amount of hard structures was small, the toughness was insufficient, and the fragile fracture surface was observed. [00205] Experimental example 88 is an example in which the average cooling rate of 740 ° C to 500 ° C in the annealing step was small, and with that the amount of hard structures was small, the effective average diameter of the grain. crystal was large, tenacity was insufficient, and the fragile fracture surface was observed. [00206] Experimental example 92 is an example in which the partial pressure ratio between H2O and H2 was low, and with that the decarbonized layer was not formed, the toughness was insufficient, and the fragile fracture surface was observed. In addition, in experimental example 92, the coating peeled and Petition 870190015116, of 02/14/2019, p. 112/125 108/110 detachment. [00207] Experimental example 100 is an example in which the bonding treatment time was long, and with that the peeling of the coating occurred. [00208] Experimental example 108 is an example in which the effective amount of Al in the coating bath was small, and with that the peeling of the coating occurred. [00209] Experimental example 112 is an example in which the temperature of the bonding treatment was high, with which the peeling of the coating and the detachment occurred, and the resistance was insufficient. [00210] In the hot-dip galvanized steel plate bonded from experimental example 125, the Si content was small, the density of the oxides dispersed in the decarbonized layer became insufficient, and a large amount of iron-based carbides was generated through of the bonding treatment, so that the steel plate was inferior in terms of toughness and strength. [00211] In the hot-dip galvanized steel sheet linked to experimental example 128, the density of the oxides in the decarbonized layer was significantly high, and thus the toughness and adhesion of the steel sheet coating were lower. [00212] In the hot-dip galvanized steel sheet linked to experimental example 129, the size of the oxide in the decarbonized layer was significantly large, and thus the toughness of the steel sheet was lower. [00213] Experimental example 130 is an example in which the hot rolling finish temperature was low, the flatness of the steel plate was significantly lower, and the cold rolling was difficult to perform, resulting in the fact that the test was interrupted. The bonded hot-dip galvanized steel sheet of the example Petition 870190015116, of 02/14/2019, p. 113/125 109/110 experimental 131 is an example in which the hot rolling finish temperature was high, and the value of Expression 1 was outside the specified range, resulting in the fact that the grain diameter becomes rough, and the toughness was deteriorated. [00231] The hot dip galvanized steel sheet of experimental example 132 is an example in which the average cooling rate at 740 to 500 ° C was small, and the ferrite fraction was greatly increased, resulting in the fact that the tenacity has been deteriorated. [00232] The hot-dip galvanized steel plate bonded from experimental example 133 is an example in which the temperature of the bainite transformation process was low, the martensite was generated in the bainite transformation process, and then the tempering was carried out the high temperature through the connection, so that the resistance has been significantly decreased. [00233] Although the respective modalities of the present invention have been described in detail, the modalities described above merely illustrate concrete examples of implementation of the present invention. The technical scope of the present invention is not construed in a restrictive manner by these modalities. That is, the present invention can be implemented in several ways without leaving its technical spirit or its main characteristics. INDUSTRIAL APPLICABILITY [00234] The present invention is an effective technique for a high strength hot dip galvanized steel sheet excellent in impact strength properties and its production method, and a high strength hot dip galvanized steel sheet bonded resistance and its production method. In addition, according to the present invention, it is possible to provide a high strength hot dip galvanized steel sheet and an excellent bonded and high strength hot dip galvanized steel sheet Petition 870190015116, of 02/14/2019, p. 114/125 110/110 impact strength at low temperature and capable of tensile strength of 900 MPa or more, and its production methods. Petition 870190015116, of 02/14/2019, p. 115/125 1/5
权利要求:
Claims (7) [1] 1. High-strength hot-dip galvanized steel sheet, characterized by the fact that a hot-dip galvanized layer formed on a surface of a base steel plate consisting of, in mass%, C: 0.075 to 0.400%, Si: 0.01 to 2.00%, Mn: 0.80 to 3.50%, P: 0.0001 to 0.100%, S: 0.0001 to 0.0100%, Al: 0.001 to 2.00%, O: 0.0001 to 0.0100%, N: 0.0001 to 0.0100%, and optionally one or two or more elements selected from among Ti: 0.001 to 0.150%, Nb: 0.001 to 0.100%, V: 0.001 to 0.300%, Cr: 0.01 to 2.00%, Ni: 0.01 to 2.00%, Cu: 0.01 to 2.00%, Mo: 0.01 to 2.00%, B: 0.0001 to 0.0100%, W: 0.01 to 2.00%, and a total of one or two or more elements selected from Ca, Mg, Zr and REM: 0.0001 to 0.0100%, and a balance composed of Fe and the unavoidable impurities, where: the base steel plate has a steel plate structure in a range of 1/8 of the thickness to 3/8 of the thickness centered on 1/4 of Petition 870190015116, of 02/14/2019, p. 116/125 [2] 2/5 a thickness of the steel sheet from a surface, in which a volume fraction of a retained austenite phase is 5% or less, a volume fraction of a ferrite phase is 50% or less, and a fraction of total volume of a bainite phase, a bainite ferrite phase, a new martensite phase and a tempered martensite phase is 40% or more; an average effective diameter of the crystal grain and a maximum effective diameter of the crystal grain in the range of 1/8 of the thickness to 3/8 of the thickness centered in 1/4 of the thickness of the plate from the surface is 5.0 pm or less and 20 pm or less, respectively; and a decarbonized layer with a thickness of 0.01 pm to 10.0 pm is formed in a portion of the surface layer, in which a density of the oxides dispersed in the decarbonized layer is 1.0 χ 10 12 to 1.0 χ 10 16 oxides / m 2 , and an average grain diameter of the oxides is 500 nm or less. 2. High-strength hot-dip galvanized steel sheet according to claim 1, characterized by the fact that REM contains at least one from Ce and La. [3] 3. High-strength hot-dip galvanized steel sheet according to claim 1, characterized by the fact that the hot-dip galvanized layer formed on the surface of the base steel sheet is bonded. [4] 4. Production method of a high-strength hot-dip galvanized steel sheet, as defined in claim 1, characterized by the fact that: a step of obtaining a base steel plate, the step comprising: a hot rolling step of performing hot rolling in which a plate consisting of, in mass%, Petition 870190015116, of 02/14/2019, p. 117/125 3/5 C: 0.075 to 0.400%, Si: 0.01 to 2.00%, Mn: 0.80 to 3.50%, P: 0.0001 to 0.100%, S: 0.0001 to 0.0100%, Al: 0.001 to 2.00%, O: 0.0001 to 0.0100%, N: 0.0001 to 0.0100%, and optionally one or two or more elements selected from among Ti: 0.001 to 0.150%, Nb: 0.001 to 0.100%, V: 0.001 to 0.300%, Cr: 0.01 to 2.00%, Ni: 0.01 to 2.00%, Cu: 0.01 to 2.00%, Mo: 0.01 to 2.00%, B: 0.0001 to 0.0100%, W: 0.01 to 2.00%, and not the total of one or two or more elements selected from Ca, Ce, Mg, Zr, La, and REM: 0.0001 to 0.0100%, and a compound balance of Fe and the inevitable impurities is heated to 1080 ° C or more, hot rolling is completed at a temperature of 850 ° C to 950 ° C, and a reduction of rolling in a temperature region of 1050 ° C to a temperature termination of hot rolling meets the following (Expression 1) to obtain a hot rolled steel sheet; a cold rolling step of performing cold rolling at a reduction rate of 30% to 75% on the hot rolled steel sheet to obtain a cold rolled steel sheet; and Petition 870190015116, of 02/14/2019, p. 118/125 4/5 an annealing step of carrying out the annealing in which the cold rolled steel sheet is passed through a preheating zone in which heating is carried out using mixed gas whose air ratio being a ratio between a volume of air contained in the mixed gas per unit of volume and an air volume that is theoretically necessary to cause complete combustion of the combustible gas contained in the mixed gas per unit of volume in the mixed gas of air and combustible gas used for preheating, is 0, 7 to 1.2, to generate an oxide coating film on a portion of the surface layer, the steel sheet is passed through a reduction zone in an atmosphere in which a partial pressure ratio between H2O and H2 ( P (H2Ü) / P (H2)) is 0.0001 to 2.00 at a maximum heating temperature of point Ac3 - 50 ° C or more to reduce the oxide coating film to form a decarbonized layer, and fold in a bending radius of 800 mm or less is performed once or more while applying a tension of 3 to 100 MPa, while cooling in a temperature range of 740 ° C to 500 ° C is performed at an average cooling rate of 1.0 ° C / s or more; a coating step of making the base steel sheet dipped in a coating bath in which the effective amount of Al is 0.01 to 0.18% by weight to form a hot dip galvanized layer on a surface of the sheet base steel to produce a hot dip galvanized steel sheet, [Mathematical expression 1] [5] 5/5 hot, i indicates a pass order, Ti indicates a rolling temperature (° C) in the i pass, hi indicates a thickness of the plate after processing (mm) in the i pass, and ti indicates a time elapsed from the first pass to the next pass; note that when i is equal to 1, h0 is equal to the thickness of the plate; in addition, a time elapsed from a final pass to a next pass is adjusted to a time elapsed from the final pass to a point in time when cooling starts after the hot rolling is finished. 5. Production method of the high-strength hot-dip galvanized steel sheet according to claim 4, characterized by the fact that the coating step is a step of making the base steel sheet from 430 to 490 ° C enter and be immersed in a coating bath at 450 to 470 ° C. [6] 6. Production method of the high-strength hot-dip galvanized steel sheet according to claim 4, characterized by the fact that the transformation process of the retaining bainite is carried out, before and / or after the immersion of the steel sheet base steel in the coating bath, the base steel plate in a temperature range of 300 to 470 ° C for 10 to 1000 seconds. [7] 7. Production method of a high-strength hot-dip galvanized steel sheet, according to claim 4, characterized by the fact that it performs the bonding treatment of retaining high-heat-galvanized steel sheet resistance, as defined in claim 3, in a temperature range of 470 ° C to 620 ° C for 2 seconds to 200 seconds. Petition 870190015116, of 02/14/2019, p. 120/125
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同族专利:
公开号 | 公开日 US9702035B2|2017-07-11| JPWO2013047755A1|2015-03-30| BR112014007677A2|2017-04-18| EP2762589B1|2017-08-23| RU2566121C1|2015-10-20| TWI467028B|2015-01-01| WO2013047755A1|2013-04-04| MX2014003715A|2014-07-09| CA2850195A1|2013-04-04| EP2762589B8|2017-10-04| US20150083278A1|2015-03-26| KR20140054379A|2014-05-08| US20140227555A1|2014-08-14| KR101570629B1|2015-11-19| TW201329252A|2013-07-16| US8932729B2|2015-01-13| CA2850195C|2016-10-25| JP5327410B1|2013-10-30| CN103842542B|2016-01-20| EP2762589A4|2015-12-02| EP2762589A1|2014-08-06| CN103842542A|2014-06-04|
引用文献:
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法律状态:
2018-05-08| B07A| Application suspended after technical examination (opinion) [chapter 7.1 patent gazette]| 2018-12-11| B07A| Application suspended after technical examination (opinion) [chapter 7.1 patent gazette]| 2019-08-20| B25D| Requested change of name of applicant approved|Owner name: NIPPON STEEL CORPORATION (JP) | 2020-02-27| B09A| Decision: intention to grant [chapter 9.1 patent gazette]| 2020-04-22| B16A| Patent or certificate of addition of invention granted [chapter 16.1 patent gazette]|Free format text: PRAZO DE VALIDADE: 20 (VINTE) ANOS CONTADOS A PARTIR DE 28/09/2012, OBSERVADAS AS CONDICOES LEGAIS. | 2021-08-10| B21F| Lapse acc. art. 78, item iv - on non-payment of the annual fees in time|Free format text: REFERENTE A 9A ANUIDADE. | 2021-11-30| B24J| Lapse because of non-payment of annual fees (definitively: art 78 iv lpi, resolution 113/2013 art. 12)|Free format text: EM VIRTUDE DA EXTINCAO PUBLICADA NA RPI 2640 DE 10-08-2021 E CONSIDERANDO AUSENCIA DE MANIFESTACAO DENTRO DOS PRAZOS LEGAIS, INFORMO QUE CABE SER MANTIDA A EXTINCAO DA PATENTE E SEUS CERTIFICADOS, CONFORME O DISPOSTO NO ARTIGO 12, DA RESOLUCAO 113/2013. |
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