 HIGH RESISTANCE COLD LAMINATED STEEL PLATE HAVING EXCELLENT UNIFORM STRETCHING AND HOLE EXPANSION CA
专利摘要:
Abstract: "High strength cold rolled steel plate having excellent uniform elongation and bore expandability and method for producing it [ljs1]". The present invention relates to a high strength cold rolled steel sheet having excellent uniform elongation and hole expandability containing c: 0.01 to 0.4%; si: 0.001 to 2.5%; mn: 0.001 to 4.0%; p: 0.001 to 0.15%; s: 0.0005 to 0.03%; al: 0.001 to 2.0%; n: 0.0005 to 0.01%; and o: 0.0005 to 0.01%; where si + al is limited to less than 1.0%, and the equilibrium being composed of iron and the inevitable impurities, where in a central portion of the plate thickness, the average value of the pole densities of the orientation group {100 } <011> at {223} <110> is 5.0 or less, and the density of the crystal orientation pole {332} <113> is 4.0 or less, the metal frame contains 5 to 80% ferrite , 5 to 80% bainite, and 1% or less martensite in terms of an area ratio and the total martensite, perlite, and retained austenite is 5% or less, and the value r (rc) in a perpendicular direction. The rolling direction is 0.70 or more and the value r (r30) in a 30 ° direction of the rolling direction is 1.10 or less. 公开号:BR112013026849B1 申请号:R112013026849-2 申请日:2012-04-19 公开日:2019-03-19 发明作者:Yuri Toda；Riki Okamoto；Nobuhiro Fujita；Kohichi Sano；Hiroshi Yoshida；Toshio Ogawa 申请人:Nippon Steel & Sumitomo Metal Corporation； IPC主号:
专利说明:
Descriptive Report of the Invention Patent for HIGH-RESISTANCE COLD LAMINATED STEEL SHEET HAVING EXCELLENT UNIFORM STRETCHING AND CAPACITY FOR EXPANSION OF HOLE AND METHOD FOR PRODUCTION OF THE SAME. Technical Field The present invention relates to a high-strength cold-rolled steel sheet having excellent uniform elongation and bore expansion capability that is used primarily for auto parts and the like, and the method of producing it. This application is based on, and claims priority benefit over, Japanese Patent Application No. 2011-095254, filed on April 21, 2011, the complete content of which is incorporated herein by reference. Background of the Technique To reduce the emission of carbon dioxide gas by automobiles, a reduction in the weight of automobile chassis was promoted using high-strength steel plates. In addition, to also ensure the safety of a passenger, a high-strength steel plate has been increasingly used for an automobile chassis in addition to the mild steel plate. In order to also promote a reduction in the weight of car chassis from now on, the strength of the high-strength steel plate has to be increased more than the conventional one. In order to use the high-strength steel sheet for a lower part, for example, the deburring work capacity has to be improved in particular. However, when a steel plate has increased strength, in general the forming capacity decreases, and uniform elongation, which is important for stamping and internal expansion, decreases. In Non-Patent Document 1, a method is described in which austenite is allowed to remain in a steel plate structure to ensure uniform elongation. In addition, in Non-Patent Document 2, a method is described to ensure uniform elongation with the same strength by making the metallic structure of the steel layer complex. 2/60 However, the control of a metallic structure that improves the local ductility necessary for folding, hole expansion and deburring is also described. Non-Patent Document 3 describes that controlling the inclusions, making the structure uniform and also decreasing the difference in hardness between the structures are effective measures for improving the bending and hole expansion capacity. This is a method to improve the hole expansion capacity by making the structure uniform by controlling the structure, but to make the structure uniform, a heat treatment from a single austenite phase takes a base as described in Non Patent Document 4. In order to achieve resistance and ductility, Non-Patent Document 4 describes that the transformation structure is controlled by cooling control, thus obtaining adequate fractions of ferrite and bainite. However, all cases are to improve the local deformation capacity with the control of the structure, and the desired properties are greatly affected by the way the structure is formed. However, as a method for improving a hot rolled steel sheet material, a technique for increasing the amount of reduction in continuous hot rolling is described. This is what is called the technique of making crystal grains thin, in which a heavy reduction is carried out at as low a temperature as possible in an austenite and non-recrystallized austenite region is turned into ferrite, to make the crystal grains thin of ferrite, which is the main phase of a product. Non-Patent Document 5 describes that, due to this grain refining, increased resistance and increased toughness are desired. However, Non-Patent Document 5 does not pay attention to improving the hole expansion capacity, which is desired to be resolved by the present invention, and does not describe a feature applied to cold-rolled steel sheet either. 3/60 Previous Technique Documents Non-Patent Documents Non-Patent Document 1: Takahashi, Nippon Steel Technical Report (2003) No. 378, pg. 7 Non-Patent Document 2: O. Matsumura et al., Trans. ISIJ (1987) vol. 27, pg. 570 Non-Patent Document 3: Kato et al., Steelmaking Research (1984) vol. 312, pg. 41 Non-Patent Document 4: K. Sugimoto et al., (2000) Vol. 40, pg. 920 Non-Patent Document 5: Nakayama Steel Works, Ltd. NFG Catalog Description of the Invention Problems to be solved by the invention As described above, carrying out the control of the structure including inclusions is the main method to improve the performance of the local ductility of a high-strength steel plate. However, once the structure control is performed, the shape of the precipitates and the ferrite and bainite fractions needs to be controlled, and it is essential to limit the metal structure to be the base. Thus, the present invention has a task to improve the uniform elongation and deburring workability of a high-strength steel sheet and also to improve the anisotropy in the steel sheet by controlling the fractions and the shape of a metal structure to be the base and controlling the texture. The present invention aims to provide a high-strength cold-rolled steel sheet having excellent uniform elongation and bore expansion capacity that solves this task, and a method for producing it. Means to Solve Problems The present inventors have seriously examined a method for solving the task described above. As a result, it has been found that when rolling conditions and cooling conditions are met 4/60 trolled for the strips required to form a predetermined texture and the structure of the steel sheet, a high strength cold rolled steel sheet having excellent isotropic workability can thus be produced. The present invention is made on the basis of the knowledge described above and its essence is as follows. A high-strength cold-rolled steel sheet having excellent uniform elongation and expandability and bore contains, in mass%, C: 0.01 to 0.4%; Si: 0.001 to 2.5%; Mn: 0.001 to 4.0%; P: 0.001 to 0.15%; S: 0.0005 to 0.03%; Al: 0.001 to 2.0%; N: 0.0005 to 0.01%; and O: 0.0005 to 0.01%; in which Si + Al is limited to less than 1.0%, and the balance being composed of iron and the inevitable impurities, in which a portion of the plate's thick center being a range from 5/8 to 3/8 in the plate thickness from the steel plate surface, the average pole densities value of the {100} <011> to {223} <110> orientation group represented by the respective {100} <011>, { 116} <110>, {114} <110>, {113} <110>, {112} <110>, {335} <110>, and {223} <110> is 5.0 or less, and the pole density of the {332} <113> crystal orientation is 4.0 or less, the metal structure contains 5 to 80% ferrite, 5 to 80% bainite, and 1% or less martensite in terms of a ratio of area and the total of martensite, perlite, and retained austenite is 5% or less, and the r (rC) value in a direction perpendicular to the rolling direction is 0.70 or more and the r (r30) value in a direction a 30 ° from the direction 5/60 lamination is 1.10 or less. The high-strength cold-rolled steel sheet having excellent uniform elongation and hole expansion capacity as per item 1, in which the r (rl_) value in the rolling direction is 0.70 or more and the r (r60) value in a 60 ° direction from the rolling direction and 1.10 or less. The high-strength cold-rolled steel sheet having excellent uniform elongation and hole expansion capacity according to item 1, in which in the metallic structure, the average diameter of the crystal grains is 7 μηρί or less, and the average value of the ratio , in crystal grains, from length dL in the lamination direction to length dt in the direction of sheet thickness: dL / dt is 3.0 or less. The high-strength cold-rolled steel sheet having excellent uniform elongation and bore expansion capacity as per item 1, also contains one type or two or more types of elements between% by mass, Ti: 0.001 to 0.2%, Nb: 0.001 to 0.2%, B: 0.0001 to 0.005%, Mg: 0.0001 to 0.01%, REM: 0.0001 to 0.1%, Ca: 0.0001 to 0.01%, Mo: 0.001 to 1.0%, Cr: 0.001 to 2.0%, V: 0.001 to 1.0%, Ni: 0.001 to 2.0%, Cu: 0.001 to 2.0%, Zr: 0.0001 to 0.2%, W: 0.001 to 1.0%, As: 0.0001 to 0.5%, Co: 0.0001 to 1.0%, Sn: 0.0001 to 0.2%, 6/60 Pb: 0.001 to 0.1%, Y: 0.001 to 0.10%, and Hf: 0.001 to 0.10%. The high-strength cold-rolled steel plate having excellent uniform elongation and hole expansion capacity according to item 1, in which hot-dip galvanization is performed on the surface. The high-strength cold-rolled steel sheet having excellent uniform elongation and hole expansion capacity according to item 1, in which, after hot dip galvanizing, a bonding treatment at 450 to 600 * 0 is carried out. A method of producing a high-strength cold-rolled steel sheet having excellent uniform elongation and bore expansion capacity includes: in a steel block containing, in% by mass C: 0.01 to 0.4%; Si: 0.001 to 2.5%; Mn: 0.001 to 4.0%; P: 0.001 to 0.15%; S: 0.0005 to 0.03%; Al: 0.001 to 2.0%; N: 0.0005 to 0.01%; and O: 0.0005 q 0.01%; in which Si + Al is limited to less than 1.0%, and the balance being composed of iron and the inevitable impurities, initially perform hot rolling, in which rolling at a reduction rate of 40% or more is performed once or more in a temperature range of not less than 1000 * 0 or more than 12000; adjust the diameter of the austenite grain to 200 μιτι or less by the first hot rolling; perform the second hot lamination in which the lamination to be 7/60 a reduction ratio of 30% or more is performed on a pass at least once in a temperature region of not less than the temperature T1 + 30 * 0 nor more than T1 + 200 * 0 determined by the Expression (1 ) below; adjust the total reduction ratio in the second hot rolling to 50% or more; perform the final reduction at a reduction rate of 30% or more on the second hot rolling and then start the primary pre-cold rolling in such a way that the waiting time t seconds satisfies Expression (2) below; adjust the average cooling rate in the primary cooling to 50 ° C / s or more and perform the primary cooling so that the temperature change is in a range of not less than 40 * 0 nor more than 140 * C; perform cold rolling at a reduction rate of not less than 30% or more than 70%; perform heating up to a temperature range of 700 * 0 to 900Ό and perform retention for no less than 1 second or more than 1000 seconds; perform primary cooling after cold rolling to a temperature range of 580 to 750 * 0 at an average cooling rate of 12 ° C / s or less; perform secondary cooling after cold rolling to a temperature range of 350 to 500 * 0 at an average cooling rate of 4 to 300 * C / s; and perform an aging heat treatment in which retention is performed for no less than 12 seconds satisfying Expression (4) below or more than 400 s in a temperature region of no less than 350 * 0 or more than 500 * 0. T1 (° C) = 850 + 10 x (C + N) x Mn + 350 x Nb + 250 x Ti + 40 x B + 10xCr + 100xMo + 100 xV ··· (1) Here, C, N, Mn, Nb, Ti, B, Cr, Mo, and V each represent the 8/60 of the element (% by mass). t 2.5 x t1 - (2) Here, t1 is obtained by Expression (3) below. t1 = 0.001 x ((Tf - T1) x P1 / 100) 2 - 0.109 x ((Tf - T1) x P1 / 100) + 3.1 ··· (3) Here, in Expression (3) above, Tf represents the temperature of the steel block obtained after the final reduction at a reduction ratio of 30% or more and P1 represents the reduction ratio of the final reduction to 30% or more. Yog (t2) = 0.0002 (T2 - 425) 2 + 1.18 ... (4) Here, T2 represents the temperature of the aging treatment, and the maximum value of t2 is set to 400. The method of producing high-strength cold-rolled steel sheet having excellent uniform elongation and hole expansion capability as per item 7, also includes: after primary cold pre-lamination runs, perform secondary cold pre-lamination cooling to a cooling stop temperature of 600 * C or less, at an average cooling rate of 10 to SOOO / s before performing cold rolling, and winding at 600Ό or less to obtain a hot rolled steel sheet. The production method of high strength cold rolled steel sheet having excellent uniform elongation and hole expansion capacity as per item 7, in which the total production ratio in a temperature range of less than T1 + 30 * C is 3 0% or less. The production method of high-strength cold-rolled steel sheet having excellent uniform elongation and hole expansion capacity according to item 7, in which the waiting time t seconds also satisfies Expression (2a) below. t <t1 · (2a) The production method of high-strength cold-rolled steel sheet having excellent uniform elongation and hole expansion capacity according to item 7, in which the waiting time t seconds 9/60 also satisfies Expression (2b) below. t1 t t1 x 2.5 ··· (2b) The production method of high-strength cold-rolled steel sheet having excellent uniform elongation and hole expansion capacity according to item 7, in which the primary cooling after hot lamination is initiated between the rolling chairs. The production method of high strength cold rolled steel sheet having excellent uniform elongation and hole expansion capacity according to item 7, in which when the heating is carried out to the temperature range of 700 to 900Ό after cold rolling , an average heating rate of not less than room temperature or greater than 650 ° C is set to HR1 (° C / s) Expressed by Expression (5) below, and an average heating rate of more than 650 * 0 at 70 0 * 0 to 900 * C is adjusted to HR2 (* C / s) expressed by Expression (6) below. HR1 0.3 ... (5) HR2 0.5 x HR1 ... (6) The method of producing high-strength cold-rolled steel sheet having excellent uniform elongation and hole expansion capability as per item 7, also includes hot-dip galvanizing the surface. The production method of high-strength cold-rolled steel sheet having excellent uniform elongation and hole expansion capacity as per item 14, also includes performing a bonding treatment at 450 to 600 ° C after the execution of immersion galvanizing hot. Effect of the Invention According to the present invention, it is possible to provide a high-strength cold-rolled steel sheet that is not large in anisotropy even when Nb, Ti, and / or the like are added and has excellent uniform elongation and bore expansion capacity. Brief Description of Drawings 10/60 [FIG. 1 is an explanatory view of a continuous hot rolling line. Mode for Carrying Out the Invention The present invention will now be explained in detail. Initially, a high strength cold rolled steel sheet having excellent uniform elongation and bore expansion capacity of the present invention will be explained (which will hereinafter be sometimes referred to as the steel sheet of the present invention). (Crystal Orientation) In the steel plate of the present invention, the average value of the pole densities of the orientation group {100} <011> to {223} <110> in a central portion of the plate thickness being the range from 5/8 to 3/8 the thickness of the plate from the surface of the steel plate is a particularly important characteristic value. Since the mean value of the pole densities of the {100} <011> to {223} <110> orientation group is 5.0 or less when X-ray diffraction is performed on the central portion of the plate thickness with the 5/8 to 3/8 in the thickness of the sheet from the surface of the steel sheet to obtain the pole densities of the respective orientations, it is possible to satisfy the bending radius of the sheet thickness 1.5 that is required to work a structural layer required in recent years. When the average value described above exceeds 5.0, the anisotropy the mechanical properties of the steel sheet becomes extremely strong, and thus the local deformation capacity is improved in only a certain direction, but a material in a direction other than it deteriorates significantly , resulting in it becoming impossible to satisfy the thickness of the folding plate / radius 1.5. The average value of pole densities in the {100} <011> to {223} <110> guidance group is desirably 4.0 or less. When more excellent bore expansion capacity and small limited bending capacity are required, the average value described above is desirably 3.0 or less. On the other hand, when the average value described above is taken 11/60 less than 0.5, which is difficult to achieve in a general current continuous hot rolling process, the deterioration of local deformation capacity is concerned, so that the average value described above is preferably 0.5 or more. The {100} <011>, {116} <110>, {114} <110>, {113} <110>, {112} <110>, {335} <110>, and {223} <110 guidelines > are included in the guidance group {100} <011> to {223} <110>. The pole density is synonymous with the random X-ray intensity ratio. The polar density (X-ray random intensity ratio) is the numerical value obtained by measuring the X-ray intensities of a standard sample without accumulation in a specific orientation. and a test sample under the same conditions by X-ray diffractometry or similar and dividing the X-ray intensity obtained from the test sample by the X-ray intensity of the standard sample. This pole density is measured using an X-ray diffraction device EBSD (Electronic Backscatter Diffraction), or similar. In addition, it can be measured by an EBSP (Electronic Backscatter Standard) method or an ECP (Electronic Plumbing Standard) method. It can be obtained from a three-dimensional texture calculated by a vector method based on a pole figure of {110}, or it can also be obtained from a three-dimensional texture calculated by a series of expansion methods using a plurality (preferably three or more) of pole figures between the pole figures of {110}, {100}, {211}, and {310}. For example, for the pole density of each of the crystal orientations described above, each of the intensities of (001) [1-10], (116) [1-10], (114) [1-10], ( 113) [1-10], (112) [1-10], (335) [1-10], and (223) [1-10] a cross section φ2 = 45 ° in the three-dimensional texture (ODF) can be used as is. In the {100} <011> orientation group {223} <110> is an arithmetic mean of the pole densities of these orientations. When it is impossible to obtain all the intensities of these orientations, the arithmetic mean of the pole densities of the respective orientations of {100} <011>, {116} <110>, 12/60 {114} <110>, {112} <110>, and {223} <110> can also be used as a substitute. In addition, due to a similar reason, the pole density of the crystal orientation {332} <113> of a flat plate in the central portion of the plate thickness being the range from 5/8 to 3/8 in the plate thickness from of the steel sheet surface must be 4.0 or less. Once it is 4.0 or less, it is possible to satisfy the sheet thickness bending radius ^ 1.5 that is required to work a structural part demanded in recent years. It is, desirably, 3.0 or less. When the pole density of the {332} <113> crystal orientation is greater than 4.0, the anisotropy of the mechanical properties of the steel sheet becomes extremely strong, and also the local deformation capacity is improved only in a certain direction, but the material in a direction other than this deteriorates significantly, resulting in it becoming impossible to safely satisfy the folding plate / radius thickness ü 1.5. On the other hand, when the pole density becomes less than 0.5, which is difficult to achieve in a continuous hot rolling process, the deterioration of the local deformation capacity is concerned, so that the pole density of the crystal orientation {332} <113> is preferably 0.5 or more. The reason why the pole densities of the crystal orientations described above are important for the freezing property of the shape at the time of the folding work is not necessarily obvious, but it is inferentially related to the sliding behavior of the crystal at the moment of the folding deformation. The sample to be subjected to X-ray diffraction is manufactured in such a way that the steel plate is reduced in thickness to a plate thickness predetermined by mechanical polishing or similar, and then the tension is removed by chemical polishing, electrolytic polishing, or similar, and in the range of 5/8 to 3/8 in the thickness of the sheet from the surface of the steel sheet, a suitable plane becomes the measurement plane. As usual, pole density meets the limited pole density range described above 13/60 not only in the central portion of the plate thickness, the range being 5/8 to 3/8 in the plate thickness from the surface of the steel plate, but also in as many thickness positions as possible, and thus the elongation uniform and the hole expansion capacity are also improved. However, the range from 5/8 to 3/8 from the surface of the steel sheet is measured to make it possible to generally represent the material property of the entire steel sheet. Thus, 5/8 to 3/8 of the thickness of the plate is prepared as the measurement range. Incidentally, the crystal orientation represented by {hkl} <uvw> means that the normal direction of the steel layer plane is parallel to <hkl> and the rolling direction is parallel to <uvw>. Regarding the crystal orientation, normally, the vertical orientation to the plate plane is represented by [hkl] or {hkl} and the orientation parallel to the lamination direction is represented by (uvw) or <uvw>. {hkl} and <uvw> are generic terms for equivalent plans, and [hkl] and (uvw) each indicate an individual crystal plane. That is, in the present invention, a body-centered cubic structure is desired, and so, for example, the planes (111), (-111), (1-11), (11-1), (-1-11 ), (-11-1), (1-1-1), and (-1-1-1) are equivalent to make it impossible to make them different. In such a case, these guidelines are generically referred to as {111}. In an ODF representation, [hkl] (uvw) is also used to represent orientations of other low symmetrical crystal structures, and so it is common to represent each orientation as [hkl] (uvw), but in the present invention, [hkl] (uvw ) and {hkl} <uvw> are synonymous with each other. The measurement of crystal orientation by an X-ray is performed according to the method described, for example, in Cullity, Elements of X-ray Diffraction, new edition (published in 1986, translated by MATSUMURA, Gentaro, published by AGNE Inc. ) on pages 274 to 296. (r value) An r (rC) value in a direction perpendicular to the rolling direction is important in the steel sheet of the present invention. As a result of the thorough examination, the present inventors found that a good bore expansion capacity and good bending 14/60 can always be obtained even when the pole densities of various crystal orientations are in the appropriate ranges. To achieve good hole expansion capacity and good bending capacity, the ranges of pole densities described above must be satisfied, and at the same time, rC must be 0.70 or more. The upper limit of rC is not defined in particular, but if it is 1.10 or less, a more excellent hole expansion capacity can be obtained. An r (r30) value in a 30 ° direction from the rolling direction is important in the steel sheet of the present invention. As a result of careful examination, the present inventors have found that good hole expansion capacity and good bending capacity cannot always be obtained, even when the pole densities of various crystal orientations are in the appropriate ranges. In order to obtain good hole expansion capacity and good bending capacity, the ranges of pole densities described above must be satisfied and, at the same time, r30 must be 1.10 or less. The lower limit of r30 is not determined in particular, but if it is 0.70 or more, a more excellent hole expansion capacity can be obtained. As a result of thorough examinations, the present inventors found that in addition to the pole densities of the various crystal orientations, rC, and r30, and an r (rL) value in the lamination direction and an r (r60) value in a 60 direction ° from the rolling direction are rL ü 0.70 and e r60 1.10 respectively, better hole expansion capacity can be obtained. The upper limits of rL and r60 are not determined in particular, but if rL is 1.00 or less and r60 is 0.90 or more, a more excellent hole expansion capacity can be obtained. The r-values described above can be obtained by a tensile test using a JIS No. 5 tensile specimen. The tensile stress to be applied is normally 5 to 15% in the case of a high-strength steel plate. strength, and r values can be evaluated over a range of uniform elongation. Incidentally, the direction in which the folding work is 15/60 performance varies depending on the parts to be worked, and so is not particularly limited, and in the case of the steel sheet of the present invention, similar folding capacity can be obtained even when the steel sheet of the present invention is folded in either direction. Generally, the texture and the r-value are correlated with each other, but in the steel sheet of the present invention, the limitation of the pole densities of the crystal orientations and the limitation of the r-values are not synonymous with each other, and unless both limitations are satisfied at the same time, good hole expansion capacity cannot be achieved. (Metal structure) In the following, the reasons for limitation relating to the steel structure of the steel sheet of the present invention will be explained. The steel sheet structure of the present invention contains 5 to 80% ferrite in terms of area ratio. Due to the existence of ferrite having excellent deformation capacity, uniform elongation improves, but when the area ratio is less than 5%, a good uniform elongation cannot be obtained, so that the lower limit is adjusted to 5%. On the other hand, when ferrite is greater than 80% in terms of area ratio, the hole expansion capacity deteriorates dramatically, so that the upper limit is adjusted to 80%. In addition, the steel sheet of the present invention contains 5 to 80% bainite in terms of area ratio. When the area ratio is less than 5%, the resistance decreases significantly, so that the lower limit is adjusted to 5%. On the other hand, when bainite is greater than 80%, the hole expansion capacity deteriorates significantly, so that the upper limit is adjusted to 80%. In the steel plate of the present invention, as a balance, the area ratio of 5% or less of martensite, perlite and retained austenite is allowed. The interface between martensite and ferrite or bainite becomes the starting point for fractures, thus deteriorating the hole expansion capacity, so that the martensite is adjusted to 1% or less. 16/60 Retained austenite is transformed by tension induced to be martensite. The interface between martensite and ferrite or bainite becomes the starting point for fractures, thereby deteriorating the hole expansion capacity. In addition, when there is a lot of perlite, resistance and work capacity are sometimes impaired. Therefore, the total area ratio of martensite, perlite and austenite retained is adjusted to 5% or less. (Average diameter of crystal grains) In the steel plate of the present invention, it is necessary to adjust the average diameter of the crystal grains in a grain unit of 7 μηη or less. When there are crystal grains having an average diameter of more than 7 μηη, uniform elongation is low and also the hole expansion capacity is low, so that the average diameter of the crystal grains is adjusted to 7 μηη or less. Here, conventionally, the definition of crystal grain is extremely vague and its quantification is difficult. In contrast to this, the present inventors have found it possible to solve the problem of quantification of the crest grains if the grain unit of the crystal grains is determined as follows. The grain unit of the crystal grains determined in the present invention is determined as follows in an analysis of the orientations of the steel sheet by an EBSP (Electronic Backscatter Standard). That is, in an analysis of the orientations of the steel plate by an EBSP, for example, the orientations are measured at an amplification of 1500 with a measured step of 0.5 μηη or less, and a position in which the disorientation between points of adjacent measurement exceeds 15 ° is adjusted to an edge between crystal grains. Then, the region encircled with that edge is determined to be the grain unit of crystal grains. In relation to the crystal grains of the grain unit determined in this way, the equivalent circle diameter d is obtained and the volume of the crystal grains of each grain unit is obtained by 4 / 3πό 3 . Then the average heavy volume is calculated and the average diameter (Average Diameter) is obtained. As there are more large crystal grains although the number of them 17/60 is small, the determination of local ductility becomes greater. Therefore, the size of the crystal grains is not a common average size, and the average diameter defined as the average heavy volume is strongly related to the local ductility. To achieve this effect, the average diameter of the crystal grains must be 7 μηη or less. It is desirable at least 5 μιτι or less to guarantee the hole expansion capacity at a higher level. Incidentally, the method of measuring crystal grains is adjusted as previously described. (Equiaxial property of crystal grains) In addition, as a result of thorough examination, the present inventors have found that when the ratio of the crystal grains in the grain unit, a length dL in the lamination direction to a length dt in the direction of the thickness of the dL / dt plate is 3.0 or less, the hole expansion capability greatly improves. This physical meaning is not obvious, but it is conceivable that the shape of the crystal grains in the grain unit is similar to a sphere rather than an ellipsoid, and thus the stress concentration at the grain edges is attenuated and thus the ability to expand hole improves. In addition, as a result of refined studies, the present inventors have found that when the average value of the ratio of length dL in the rolling direction to length dt in the direction of sheet thickness dL / dt is 3.0 or less, a good capacity hole expansion can be obtained. When the average value of the ratio of the length dL in the rolling direction to the length dt in the direction of the thickness of the plate dL / dt is greater than 3.0, the hole expansion capacity deteriorates. (Chemical composition) The reasons for limiting the chemical composition of the steel sheet of the present invention will be explained below. Incidentally,% according to chemical composition means% by mass. C: 0.01 to 0.4% C is an effective element for improving mechanical strength, so that 0.01% or more is added. It is preferably 0.03% or 18/60 more, and more preferably 0.05% or more. On the other hand, when it exceeds 0.4% the working capacity and the welding capacity deteriorate, outside of the upper limit and adjusted to 0.4%. It is preferably 0.3% or less, and is more preferably 0.25% or less. Si: 0.001 to 2.5% Si is an effective element for improving mechanical strength. However, when Si becomes greater than 2.5%, the work capacity deteriorates and surface flaws also occur, so that 2.5% is adjusted as an upper limit. On the other hand, it is difficult to decrease Si to less than 0.001% in a practical steel, so that 0.001% is adjusted as a lower limit. Mn: 0.001 to 4.0% Mn is also an effective element for improving mechanical strength, but when Mn becomes greater than 4.0%, the working capacity deteriorates, so 4.0% is adjusted as an upper limit. It is preferably 3.0% or less. On the other hand, it is difficult to decrease Mn to less than 0.001% in a practical steel, so that 0.001% is adjusted as a lower limit. When elements such as Ti that suppress the occurrence of hot fractures caused by S are not sufficiently added except Mn, an Mn satisfying Mn / S H 20 in mass% is desirably added. P: 0.001 to 0.15% The upper limit of P is adjusted to 0.15% to avoid deterioration of the working capacity and fracture during hot rolling or cold rolling. It is preferably 0.04% or less. The lower limit is set to 0.001% for general refining (including secondary refining). S: 0.0005 to 0.03% The upper limit of S is adjusted to 0.03% to prevent deterioration of the working capacity and fracture during hot rolling or cold rolling. It is preferably 0.01% or less. The lower limit is set to 0.0005% applicable in current common refining (in19 / 60 including secondary refining). Al: 0.001 to 2.0% For deoxidation, 0.001% or more of Al is added. In addition, Al significantly increases the transformation point γ to a, so that it is an effective element when hot rolling to an Ar 3 point or less is aimed in particular, but when its content is very high, the welding capacity deteriorates , so that the upper limit is adjusted to 2.0%. N eO: 0.0005 to 0.01% N and O are impurities, and both elements are adjusted to 0.01% or less to prevent deterioration in the workability. The lower limits are each adjusted to 0.0005% applicable to the current common refining (including secondary refining). Si + Al: less than 1.0% When Si and Al are excessively contained in the steel sheet of the present invention, precipitation of cementite during the aging treatment is suppressed and the fraction of austenite retained becomes very large, so that the total amount of Si and Al added is adjusted to less than 1%. In the steel plate of the present invention, one or two or more types of elements between Ti, Nb, B, Mg, REM, Ca, Mo, Cr, V, W, Zr, Cu, Ni, As, Co, Sn, Pb, Y, and Hf, being elements that have been used until now, can be contained to improve the hole expansion capacity by controlling the inclusions to make the precipitates thin. Ti, Nb, and B are elements to improve the material through mechanisms for fixing carbon and nitrogen, reinforcing precipitation, controlling the structure, reinforcing fine grains, and the like, so that according to needs, 0.001% or more of Ti is added, 0.001% or more of Nb is added, and 0.0001% or more of B is added. Ti is preferably 0.01% or more, and Nb is preferably 0.005% or more. However, even when they are added excessively, no significant effect is obtained and, on the contrary, the working capacity and the production capacity deteriorate, so that the upper limit of Ti is adjusted to 0.2%, the upper limit of Nb is set to 0.2%, and upper limit of B is set to 0.005% .B is preferably 0.003% or less. Mg, Rem, and Ca are elements to take the innocuous inclusions, so that the lower limit of each one is adjusted to 0.0001%. Mg is preferably 0.0005% or more, Rem is preferably 0.001% or more and Ca is preferably 0.0005% or more. On the other hand, when they are added excessively, the cleanliness of the steel deteriorates, so that the upper limit of Mg is adjusted to 0.01%, the upper limit of Rem is adjusted to 1.0%, and the upper limit of Ca is adjusted to 0.1%. Ca is preferably at 0.01% or less. Mo, Cr, Ni, W, Zr, and As are effective elements to increase the mechanical strength and improve the material, so that as needed, 0.001% or more of Cr is added, 0.001% or more of Ni is added, 0.001% or more of W is added, 0.0001% or more of Zr is added, and 0.0001% or more of As is added. Mo is preferably 0.01% or more, Cr is preferably 0.01% 0.01% or more, Ni is preferably 0.05% or more, and W is preferably 0.01% or more. However, when they are added excessively, the working capacity is deteriorated by inverses, in order that the upper limit of Mo is adjusted to 1.0%, the upper limit of Cr is adjusted to 2.0%, the upper limit of Ni is adjusted to 2.0%, the upper limit of W is adjusted to 1.0%, the upper limit of Zr is adjusted to 0.2%, and the upper limit of As is adjusted to 0.5%. Zr is preferably 0.05% or less. V and Cu, similar to Nb and Ti, are effective elements for reinforcing precipitation, and are elements that cause less deterioration of the local deformation capacity applicable to reinforcement by the addition of Nb and Ti, so that V and Cu are more effective elements than Nb and Ti, when high strength and better hole expansion capacity are required. Therefore, the lower limits of V and Cu are both adjusted to 0.001%. They are each preferably 0.01% or more. 21/60 However, when they are excessively added, the working capacity deteriorates, so that the upper limit of V is adjusted to 1.0%, and the upper limit of Cu is adjusted to 2.0%. V is preferably 0.5% or less. Co significantly increases the transformation point from γ to a, so that it is an effective element when hot rolling at point Ar 3 or less is targeted in particular. To obtain an addition effect, 0.0001% or more is added. It is preferably 0.001% or more. However, when it is added excessively, the weldability deteriorates, so the upper limit is adjusted to 1.0%. It is preferably 0.1% or less. Sn and Pb are effective elements to improve the wetting capacity and the adhesion of the galvanization, so that 0.0001% or more of Sn is added and 0001% or more of Pb is added. Sn is preferably 0.001% or more. However, when they are added excessively, a failure is likely to occur at the time of production, and also the toughness decreases, so that the upper limit of Sn is set to 0.2% and the upper limit of Pb is set to 0 ,1%. Sn is preferably 0.1% or less. Y and Hf are effective elements for improving corrosion resistance. When the elements are each less than 0.001%, the effect of the addition is not obtained, so that its lower limits are adjusted to 0.001%. On the other hand, when each of them exceeds 0.10%, the hole expansion capacity deteriorates, so that the upper limit of each element is adjusted to 0.10%. (Production Method) In the following, a method of producing the steel sheet of the present invention will be explained (which will hereinafter be referred to as the production method of the present invention). In order to achieve excellent uniform elongation and hole expansion capacity, it is important to form a texture that is random in terms of pole density and to control the conditions of the ferrite and bainite structural fractions and to form dispersion. 22/60 From now on, details will be explained. The production method before hot rolling is not particularly limited. That is, subsequent to melting by a vat oven, an electric oven, or the like, a secondary refining can be performed in several ways, and then the casting can be performed by conventional continuous casting, or by a conventional casting method, or also by casting thin plates, or the like. In the case of a continuous caster plate, it is possible that a continuous caster plate is cooled once to a low temperature and is then reheated to then be subjected to hot rolling, or it is also possible that a continuous caster plate is subjected to continuous hot rolling after casting. Incidentally, a scrap can also be used as a raw material for steel. (First hot rolling) A plate extracted from a heating oven is subjected to a roughing lamination process which is the first hot rolling to be roughed, and then a raw bar is obtained. The steel sheet of the present invention must satisfy the following requirements. First, the austenite grain diameter after rough lamination, that is, the austenite grain diameter before finishing lamination, is important. An austenite grain diameter of 200 μηη or less contributes greatly to making the crystal grains fine and for the homogenization of the crystal grains, thus making it possible to finely and uniformly disperse the martensite to be formed in a later process. To obtain the austenite grain diameter of 200 μπι or less before the finishing lamination, it is necessary to perform the lamination at a reduction rate of 40% or more once or more in the raw lamination in a temperature region of 1000 to 1200Ό . The austenite grain diameter before the finishing lamination is desirably 100 μιτι or less, and to obtain this grain diameter, a lamination at 40% or more is performed twice or more. However, when in the rough lamination, the reduction is greater than 70% or the lamina 23/60 nation run more than 10 times, there is concern that the rolling temperature will decrease, or scale will be excessively generated. In this way, when the grain diameter of the austenite before the finishing lamination is set to 200 pm or less, the recrystallization of the austenite is promoted in the finishing lamination, and through the formation of the texture and the uniformity of the grain unit, the uniform elongation and puncture expandability of a final product are improved. This is supposed to be because the austenite grain edge after roughing lamination (i.e., before finishing lamination) functions as one of the recrystallization cores during the finishing lamination. The grain diameter of the austenite after roughing rolling is confirmed in such a way that a part of the steel sheet before being subjected to finishing rolling is cooled as much as possible, (it is cooled to 10 “C / s or more , for example), and the cross section of the part of the steel plate and etched to make the austenite grains appear, are observed under an optical microscope. On that occasion, at a magnification of 50 or more, the austenite grain diameter of 20 visual fields or more is measured by image analysis or by a point counting method. (Second hot rolling) After the roughing lamination process (first hot rolling) is completed, a finishing lamination process is started which is the second hot rolling. The time between the end of the roughing lamination process and the beginning of the finishing lamination process is desirably set to 150 seconds or less. In the finishing lamination process (second hot lamination), the starting temperature of the finishing lamination is desirably set to ΙΟΟΟΌ or more. When the start temperature of the finishing lamination is less than 1000Ό, in each pass of the finishing lamination, the temperature of the lamination to be applied to the raw bar to be laminated is reduced, the reduction is performed in a region of 24/60 non-recrystallization temperature, the texture develops, and thus the isotropy deteriorates. Incidentally, the upper limit of the start temperature of the finishing laminate is not particularly limited. However, when it is 1150 * 0 or more, a blister to be the starting point for a scale defect in the form of a scaly shaft that can occur between the base iron of the steel plate and the surface scale before lamination finish and between passes, so that the start temperature of the finish laminate is desirably less than 1150 * C. In finishing lamination, the temperature determined by the chemical composition of the steel sheet is set to T1, and in a temperature region of not less than T1 + 30 * 0 nor more than T1 + 200Ό, lamination at 30% or more is performed on a pass at least once. In addition, in the finishing lamination, the total reduction ratio is adjusted to 50% or more. Satisfying this condition, in the central portion of the plate thickness, the range being 5/8 to 3/8 in the plate thickness from the surface of the steel plate, the mean value of the pole densities of the {100} orientation group <011> to {223} <110> becomes 5.0 or less and the pole density of the crystal orientation {332} <113> becomes 4.0 or less. This makes it possible to guarantee uniform elongation and the bore expansion capacity of the final product. Here, T1 is the temperature calculated by Expression (1) below. T1 (° C) = 850 + 10 x (C + N) x Mn + 350 x Nb + 250 x Ti + 40 x B + 10xCr + 100xMo + 100 xV - (1) C, N, Mn, Nb, Ti, B, Cr, Mo, and V each represent the content of the element (% by mass). A heavy reduction in the temperature region of not less than T1 + 30 * C nor more than T1 + 200 ° C and a slight reduction less than T1 + 30 ° C subsequently controls the mean pole densities of the guidance group {100 } <011> a {223} <110> and the pole density of the crystal orientation {332} <113> in the central portion of the plate thickness with a range of 5/8 to 3/8 in the plate thickness from the plate surface 25/60 steel, and thus the uniform elongation and expandability of the final product are dramatically improved, as shown in the Examples to be described later. This T1 temperature is obtained empirically. The present inventors learned empirically from experiences that recrystallization in an austenite region of each steel is promoted based on temperature T1. In order to obtain better uniform elongation and hole expansion capacity, it is important to build up tension by step reduction, and the total reduction ratio of 50% or more is essential in finishing lamination. In addition, it is desired to take a reduction to 70% or more and, on the other hand, if a reduction ratio greater than 90% is taken, ensuring the temperature and excessive lamination load are as the added result. When the ratio of total reduction in the temperature region of not less than T1 + 30 ° C or more than T1 + 200 ° C is less than 50%, the lamination tension to be accumulated during hot rolling is not sufficient and the recrystallization of austenite does not progress sufficiently. Therefore, the texture develops and the isotropy deteriorates. When the total reduction ratio is 70% or more, sufficient isotropy can be obtained even if variations applicable to temperature fluctuation or similar are considered. On the other hand, when the total reduction ratio exceeds 90%, it becomes difficult to obtain the temperature region of T1 + 200 ° C or less due to the generation of heat by the work, and also the lamination load increases to cause a risk lamination becomes difficult to perform. In finishing lamination, to promote uniform recrystallization caused by the release of accumulated tension, lamination at 30% or more is performed in a pass at least once at not less than T1 + 30Ό nor greater than T1 + 200X1 Incidentally, to promote uniform recrystallization, it is necessary to suppress the amount of work in a region of temperatures of less than T1 + 30 ° C to the lowest possible. To achieve this, the reduction ratio below T1 + 30 ° C is desirably 30% or less. In terms of precision of the plate thickness and shape of the plate, the 26/60 reduction of 10% or less is desirable. When isotropy is also obtained, the reduction ratio in the region of temperatures below T1 + 30 ° C is desirably 0%. The finishing lamination is desirably finished at T1 + 30 ° C or more. In hot rolling at less than T1 + 30 ° C, granulated austenite grains that are recrystallized once are elongated, thus causing a risk that the isotropy will deteriorate. That is, in the production method of the present invention, in the finishing lamination, recrystallizing the austenite evenly and finely, the texture of the product is controlled and the uniform elongation and the ability to expand the hole are improved. The lamination ratio can be obtained by the actual performances or by calculating the lamination load, measuring the thickness of the sheet, and / or the like. The temperature can actually be measured by a thermometer between the chairs or it can be obtained by calculation simulation considering the heat generation by the work from the speed of the line of the reduction ratio and / or similar. Therefore, it is possible to easily confirm whether the lamination prescribed in the present invention is performed or not. When the hot rolling is finished in Ar 3 or less, the hot rolling becomes a two-phase region of austenite and ferrite, and the accumulation for the guidance group {100} <011> to {223} <110> becomes strong. As a result, uniform elongation and hole expansion capacity deteriorate significantly. In order to make crystal grains thin and suppress elongated grains, the maximum amount of working heat generated at the time of reduction to not less than T1 + 30 ° C nor more than T1 + 200 ° C, that is, the temperature increased by the reduction is desirably suppressed up to 18Ό or less. To achieve this, cooling between chairs or the like is desirably applied. (Cold pre-lamination primary cooling) After the final reduction at a reduction rate of 30% or more is carried out on the finishing laminate, the primary pre-cooling 27/60 cold rolling is started in such a way that the waiting time t seconds satisfies Expression (2) below: t 2.5 x t1 - (2) Here, t1 is obtained by Expression (3) below. t1 = 0.001 x ((Tf - T1) x P1 / 100) 2 - 0.109 x ((Tf - T1) x P1 / 100) + 3.1 - (3) Here, in Expression (3) above, Tf represents the temperature of the steel block obtained after the final reduction at a reduction rate of 30% or more, and P1 represents the reduction ratio of the final reduction to 30% or more. Incidentally, the final reduction at a reduction rate of 30% or more indicates the lamination performed finally between laminations whose reduction rate becomes 30% or more from the laminations in a plurality of passes performed on the finishing lamination. For example, when between laminations in a plurality of passes performed on the finishing laminate, the reduction rate of the lamination performed in the final stage is 30% or more, the lamination performed in the final stage is the final reduction at a reduction rate of 30% or more. In addition, when between laminations in a plurality of passes executed in the finishing lamination, the reduction ratio of the lamination performed before the final step, is 30% or more, and after the lamination performed before the final step (rolling at a rate reduction of 30% or more), the lamination whose reduction rate becomes 30% or more is not performed, the lamination performed before the final step (lamination at a reduction rate of 30% or more) is the reduction at a rate of reduction of 30% or more. In finishing lamination, the waiting time t seconds before the primary cold pre-lamination cooling starts after the final reduction at a reduction rate of 30% or more is performed greatly affects the austenite grain diameter. That is, it greatly affects an equiaxial grain fraction and the gross grain area ratio of the steel plate. When the waiting time t exceeds t1 x 2.5, recrystallization is almost complete, but the crystal grains grow significantly and the hardening of the grain advances and thus the r and elongation values 28/60 are decreased. The waiting time t seconds also satisfies Expression (2a) below, thus making it possible to suppress preferentially the growth of the crystal grains. Consequently, although the recrystallization does not proceed sufficiently, it is possible to sufficiently improve the elongation of the steel sheet and improve the fatigue property simultaneously. t <t1 - (2a) At the same time, the waiting time t seconds also satisfies Expression (2b) below, so that the recrystallization advances sufficiently and the crystal orientations are made random. Therefore, it is possible to sufficiently improve the elongation of the steel sheet and greatly improves the isotropy simultaneously. t1 t t1 x 2.5 ··· (2b) Here, as shown in FIG. 1, in a continuous hot rolling line 1, steel block bar (plate) heated to a predetermined temperature in the heating furnace is laminated in a roughing mill 2 and in a finishing mill 3 sequentially to be a steel plate hot rolled 4 having a predetermined thickness, and the hot rolled steel sheet 4 is transported on an exit table 5. In the production method of the present invention, in the roughing lamination process (first hot rolling) performed in the laminator roughing 2, rolling at a reduction rate of 20% or more is carried out on the steel block (plate) one or more times in the temperature range of not less than 1000 “C nor more than 1200 ° C. The raw bar laminated to a predetermined thickness in the roughing laminator 2 in this way is then laminated in the finishing lamination (it is subjected to the second hot lamination) through a plurality of lamination chairs 6 of the finishing laminator 3 to be the plate hot-rolled steel 4. Then, on finishing laminator 3, rolling at 30% or more is performed in one pass at least once in the temperature region of no less than the temperature 29/60 Τ1 + 30 ° C and no more than T1 + 200 ° C. In addition, in the finishing laminator 3, the total reduction rate becomes 50% or more. In addition, in a finishing lamination process, after the final reduction at a reduction rate of 30% or more has been carried out, the primary cold pre-lamination cooling is started in such a way that the waiting time t seconds satisfies the Expression (2) above or Expression (2 a ) or (2b) above. The initiation of this primary cold pre-lamination cooling is carried out by cooling nozzles between two of the respective lamination chairs 6 of the finishing laminator 3, or cooling nozzles 11 arranged on the output table 5. For example, when the final reduction at a reduction rate of 30% or more is performed only on the laminating chair 6 arranged in the front step of the finishing laminator 3 (on the left side of FIG. 1, on the back side of the laminate) and the lamination whose reduction rate becomes 30% or more is not carried out on the lamination chair 6 arranged in the rear step of the finishing laminator 3 (on the right side of FIG. 1, on the back side of the lamination), if the cooling starts cold pre-lamination primer is performed by the cooling nozzles 11 arranged on the output table 5, a case in which the waiting time t seconds does not satisfy Expression (2) above or Expressions (2a) and (2b) above is sometimes provoked. In such a case, the primary cold pre-lamination cooling is initiated by the cooling nozzles between the chairs 10 arranged between the respective two of the lamination chairs 6 of the finishing laminator 3. In addition, for example, when the final reduction at a reduction rate of 30% or more is carried out on the laminating chair 6 arranged in the rear step of the finishing laminator 3 (on the right side of FIG. 1, on the side after the lamination) ), although the start of the primary cold pre-lamination cooling is carried out by the cooling nozzles 11 arranged on the output table 5, there is sometimes the case that the waiting time t seconds can satisfy Expression (2) above or Expressions (2a) and (2b) above. In such a case, the primary cold pre-lamination cooling can also be initiated by the cooling nozzles 11 arranged on the 30/60 output 5. Needless to say, as the performance of the final reduction at a reduction ratio of 30% or more is completed, the primary cold pre-lamination cooling can also be initiated by the cooling nozzles between the chairs 10 arranged between two of the respective laminating chairs 6 of the finishing laminator 3. Then, in this primary cold pre-lamination cooling, the cooling is performed which, at an average cooling rate of 50X3 / s or more, the temperature change (temperature drop) takes no less than 40X3 or more than 140X3. When the temperature change is less than 40X3, the recrystallized austenite grains grow and the low temperature toughness deteriorates. The temperature change is adjusted to 40X3 or more, thus making it possible to suppress the hardening of the austenite grains. When the temperature change is less than 40 ° C, the effect cannot be achieved. On the other hand, when the temperature change exceeds 140X3, the recrystallization becomes insufficient to make it difficult to obtain the desired random texture. In addition, an effective ferrite phase for elongation is also not easily obtained and the hardness of a ferrite phase becomes high, and thus uniform elongation and bore expansion capacity also deteriorates. In addition, when the change in temperature is greater than 140X3, an excess beyond / beyond the temperature of the Ar 3 transformation point is likely to be caused. In the event that, even due to the transformation from recrystallized austenite, as a result of the improvement in the selection of variants, the texture is formed and the isotropy consequently decreases. When the average cooling rate in primary cold pre-lamination cooling is less than 50X3 / s, as exposed, the recrystallized austenite grains grow and the low temperature toughness deteriorates. The upper limit of the average cooling rate is not determined in particular, but in terms of the shape of the steel sheet, 200X3 / s or less is considered to be adequate. In addition, to suppress grain growth and obtain 31/60 the most excellent low temperature nacity, a cooling device between passes or similar is desirably used to bring the heat generation through the work between the respective finishing laminate chairs to 18Ό or less. The lamination rate (reduction ratio) can be obtained by the actual performances or by calculating the lamination load, measuring the thickness of the sheet, and / or similar. The temperature of the steel block during rolling can actually be measured by a thermometer placed between the chairs, or it can be obtained by simulation considering the heat generation by working from the line speed. The reduction ratio, and / or the like, or can be obtained by both methods. In addition, as explained previously, to promote uniform recrystallization, the amount of work in the temperature region of less than T1 + 30 ° C is desirably as small as possible and the rate of reduction in the temperature region of less than T1 + 30 ° C is desirably 30% or less. For example, in the case where the finishing laminator 3 on the continuous hot rolling line 1 shown in FIG. 1, when passing through one or two or more of the rolling chairs 6 arranged on the side of the front step (on the right side of FIG. 6, on the rear side of the lamination), the steel sheet is in the region of temperatures of no less than T1 + 30 ° C or more than T1 + 200 ° C, and when passing through one or two or more of the lamination chairs 6 arranged on the side of the subsequent rear step (on the right side in FIG. 6, on the rear side of the the steel sheet is in the region of temperatures of less than T1 + 30 ° C, when the steel sheet passes through one or two or more of the lamination chairs 6 arranged on the side of the subsequent rear step (on the side right of Figure 1, on the back side of the lamination), although the reduction is not performed or is performed, the reduction rate below T1 + 30 ° C is desirably 30% or less in total. In terms of precision of the thickness of the steel sheet and the shape of the steel sheet, the reduction rate below T1 + 30 ° C is desirably a reduction of 10% or less in total. When isotropy is also obtained, the rate of reduction 32/60 in the region of temperatures below T1 + 30 ° C is desirably 0%. In the production method of the present invention, the lamination speed is not particularly limited. However, when the lamination speed on the side of the final chair of the finishing lamination is less than 400 mpm, γ grains grow to be crude, regions where ferrite can precipitate to obtain ductility are reduced, and thus ductility is susceptible to deteriorate. Although the upper lamination speed limit is not particularly limited, the effect of the present invention can be achieved, but it is 1800 mpm or less due to equipment restriction. Therefore, in the finishing lamination process, the lamination speed is desirably not less than 400 mpm or more than 1800 mpm. (Cold pre-lamination secondary lamination) In the production method of the present invention, it is preferred that after primary cold pre-lamination cooling, secondary cold pre-lamination cooling should be performed to control the structure. The secondary pre-cold rolling pattern is also important. Secondary cold pre-lamination cooling is desirably performed within three seconds after the primary cold pre-lamination cooling. When the time to start secondary cold pre-lamination after primary cold pre-lamination exceeds three seconds, the austenite grains become crude and strength and elongation decrease. In cold pre-lamination secondary cooling, cooling is performed to a cooling stop temperature of 600Ό or less at an average cooling rate of 10 to 300O / s. When the stop temperature of this secondary cold pre-lamination cooling is greater than 600Ό and the cooling rate of the secondary cold pre-lamination cooling is less than ΙΟΌ / s, there is the possibility that the oxidation of the surface will advance and the surface the steel plate deteriorates. When the average cooling rate exceeds SOOQ / s, the transformation of martensite is promoted to dramatically increase resistance, 33/60 resulting in the subsequent cold lamination becoming difficult to perform. (Coiling) After being obtained in this way, the hot rolled steel sheet can be wound up to 6000 or less. When the winding temperature exceeds 6000, the area ratio of the ferrite structure increases and the area ratio of bainite does not become 5% or more. To bring the bainite area ratio to 5% or more, the winding temperature is preferably adjusted to 600 * 0 or less. (Cold rolling) An original hot-rolled sheet produced as described above is pickled as needed to be subjected to cold rolling at a reduction rate of not less than 30% and not more than 70%. When the reduction ratio is 30% or less, it becomes difficult to cause recrystallization in heating and subsequent retention, resulting in the fact that the fraction of equiaxial grain decreases and also the crystal grains after heating become crude. When more than 70% lamination is performed, the texture at the time of heating is developed, and thus the anisotropy becomes strong. Therefore, the rate of reduction is adjusted to 70% or less. (Heating and retention) The steel sheet that has been subjected to cold rolling which has been subjected to cold rolling (a cold rolled steel sheet) is subsequently heated to a temperature range of 700 to 9000 and is maintained for no less than 1 second or more than 1000 seconds in the region of temperatures from 700 to 900 * 0. By heating and retaining, work hardening is removed. When the steel sheet after cold rolling is heated to a temperature range of 700 to 900 ° C in this way, the average heating rate of not less than room temperature or more than 650 * 0 is adjusted to HR1 (O / s) expressed by Expression (5) below, and an average heating rate of more than 650 * 0 up to the temperature range of 700 to 900 ° C is adjusted to HR2 (° C / s) expressed by 34/60 Expression (6) below. HR1 0.3 ... (5) HR2 0.5 x HR1 ... (6) Hot lamination is carried out under the condition described above, and also primary cooling after hot lamination is carried out, thus fine-tuning the crystal grains and randomizing the orientation of the crystal grains are achieved. However, due to the cold rolling performed later, the strong texture develops and the texture becomes liable to remain on the steel plate. As a result, the r-values and the elongation of the steel plate decrease and the isotropy decreases. Thus, it is desired to take the texture that developed in the cold rolling to disappear as much as possible by properly carrying out the heating to be carried out after the cold rolling. To achieve this, it is necessary to divide the average heating rate of the heating into two stages expressed by Expressions (5) and (6) above. The detailed reason why the texture and properties of the steel plate are improved by this two-stage heating is not clear, but it is thought that this effect is related to the recovery of the displacement introduced at the time of cold rolling and recrystallization. That is, the driving force of recrystallization to occur on the steel sheet by heating is the tension accumulated on the steel sheet by cold rolling. When the average rate of heating HR1 in the temperature range of not less than room temperature or more than 650 * Ό is small, the displacement introduced by cold rolling recovers and recrystallization does not occur. As a result, the texture that developed at the time of cold rolling remains as it is and properties such as isotropy deteriorate. When the average rate of heating HR1 in the temperature range of not less than room temperature nor more than 650 ° C is less than 0.3 * C / s, the displacement introduced by the cold mining recovers, resulting in the strong texture formed at the time of cold rolling remains. Therefore, it is necessary to adjust the average rate of heating HR1 in the temperature range of not less than the ambient temperature 35/60 or more than 650 * 0 to 0.3 (* C / s) or more. On the other hand, when the average HR2 heating rate of more than 650 ° C up to the temperature range of 700 to 900 ° C is large, the ferrite that exists in the steel sheet after cold rolling does not recrystallize and the ferrite does not recrystallized in a state of being worked remains. When steel containing 0.01% or more of particular C is heated to a region of two phases of ferrite and austenite, the formed austenite blocks the growth of the recrystallized ferrite, and thus the non-recrystallized ferrite becomes more likely to remain. This non-recrystallized ferrite has a strong texture, so as to adversely affect properties such as r values and isotropy, and this non-recrystallized ferrite contains many displacements, thereby drastically deteriorating ductility. Therefore, in the temperature range of more than 650 * 0 at is the temperature range of 700 to 900 ° C, the average rate of heating HR2 needs to be 0.5 x HR1 (° C / s) or less. In addition, when the heating temperature is less than 700 * 0 or the holding time in the temperature range 700 to 900 * 0 is shorter than '1 second, the reverse transformation of the ferrite does not proceed sufficiently and, in the subsequent cooling , the bainite phase cannot be obtained, resulting in sufficient strength not being obtained. On the other hand, when the heating temperature is greater than 900 * 0 or the retention time in the temperature range of 700 to 900 ° C is greater than 1000 seconds, the crystal grains become raw and the grain area ratio of crystal each having a grain diameter of 200 μπι or more increases. (Primary cooling after cold rolling) After heating and holding, primary cooling is performed after cold rolling to a temperature range of 580 to 750 ° C at an average cooling rate of 12 ° C / s or less. When the finishing temperature of the primary cooling after cold rolling exceeds 750 ° C, the transformation of ferrite is promoted to make it impossible to obtain 5% or more of bainite in terms of area ratio. When the 36/60 average cooling rate of that primary cooling after cold rolling exceeds 12 ° C / s and the end temperature of the primary cooling after cold rolling is less than 580 * 0, the growth of the ferrite grain does not advance sufficiently to make impossible to get 5% or more of ferrite in terms of an area ratio. (Secondary cooling after cold rolling) After primary cooling after cold rolling, secondary cooling after cold rolling is carried out up to the temperature range of 350 to 500 ° C at an average cooling rate of 4 to 300 * C / s. When the average cooling rate of the secondary cooling after cold rolling is less than 4 ° C / s or the secondary cooling after cold rolling is finished at a temperature of over 500 * C, the perlite transformation advances excessively to create a possibility that 5% or more of bainite cannot be obtained after all in terms of an area ratio. In addition, when the average cooling rate of secondary cooling after cold rolling and greater than 300 * C / s or secondary cooling after cold rolling is finished at a temperature of less than 350 ° C, the transformation of martensite advances and there is a risk that the martensite area ratio becomes greater than 1%. (Heat treatment of aging) Subsequent to secondary cooling after cold rolling, an aging heat treatment is carried out in a temperature range of not less than 350 ° C or more than 500 ° C. The retention time in this temperature range is set to t2 seconds, satisfying Expression (4) below according to an aging treatment temperature T2 or higher. However, taking into account the applicable temperature range of Expression (4), the maximum value of t2 is adjusted to 400 seconds. Yog (t2) = 0.0002 (T2 - 425) 2 + 1.18 ... (4) Incidentally, in this heat treatment of aging, retention does not mean only isothermal retention, and it is sufficient if the steel sheet is retained in the temperature range of not less than 350 ° C nor 37/60 more than 500 ° C. For example, the steel sheet can be cooled once to 35-0Ό and then heated to 500Ό, or the steel sheet can also be cooled to 500Ό and then cooled to 350Ό. Incidentally, even when a surface treatment is performed on the high-strength cold-rolled steel sheet of the present invention, the effect of improving the hole expansion capacity does not disappear, and, for example, a hot-dip galvanized layer, or a bonded hot dip galvanized layer can be formed on the surface of the steel sheet. In the event that the effect of the present invention can be obtained even when any between electrodeposition, hot dip coating, deposition coating, organic coating film formation, film lamination, treatment with organic salts / inorganic salts, treatment without chrome, etc., is performed. In addition, the steel sheet according to the present invention can be applied not only for curved formations, but also for combined formation composed mainly of folding work such as folding, bulging and stamping. When hot dip galvanizing is performed on the steel sheet of the present invention, a bonding treatment can be performed after galvanizing. The bonding treatment is carried out in a temperature range of 450 to 600 ° C. When the temperature of the bond treatment is less than 450Ό, the bond does not advance sufficiently, and when it exceeds 600 * 0, on the other hand, the bond advances a lot and the corrosion resistance deteriorates. Therefore, the bonding treatment is carried out in the region of temperatures from 450 to 600 ° C. Example In the following, examples of the present invention will be explained. Incidentally, the sample conditions are the sample conditions employed to shape the applicability and effects of the present invention, and the present invention is not limited to those example conditions. The present invention can employ several conditions as long as the objective of the present invention is achieved without departing from the spirit of the invention. Compo 38/60 chemical sections of the respective steels used in the examples are shown in Table 1. The respective production conditions are shown in Tables 2 and 3. In addition, structural constitutions and mechanical properties of the respective types of steel under the production conditions in Tables 2 and 3 are shown in Tables 4 and 5. Incidentally, each data underlined in the Tables indicates that the numerical value is outside the range of the present invention or is outside the range of a preferred range of the present invention. In addition, in Table 2 to Table 5, the letters A to T and the letters a to I that are added to the steel types indicate that they are components of Steels A to T and a to I in Table 1 respectively. The results of the tests will be explained using the steels of invention A to T and using the comparative steels a to h, which have the chemical compositions shown in Table 1. Incidentally, in Table 1, each numerical value of the chemical compositions means% in pasta. These steels were cast in the state, or were heated to a temperature range of 1000 to 1300Ό after being cooled to room temperature, and subsequently subjected to hot rolling, cold rolling, and cooling under conditions shown in Table 2 and Table 3. In hot rolling, initially in roughing rolling which is the first hot rolling, rolling was performed one or more times at a reduction rate of 40% or more in a temperature region of not less than 1000Ό nor greater than 12 00Ό. However, for types A3, E3 and M2, in roughing rolling, rolling at a reduction rate of 40% or more in one pass was not performed. The number of times of reduction in a reduction ratio of 40% or more and each reduction ratio (%) in the rough rolling, and the austenite grain diameter (pm) after the rough rolling (before the finishing lamination) ) are shown in Table 2. Incidentally, the temperature T1 (Ό) and the temperature Ac 1 (* C) of the respective types of steel are shown in Table 2. After the rough lamination is finished, the lamination ends 39/60 which is the second hot rolling was performed. In finishing lamination, lamination at a reduction rate of 30% or more was performed in one pass at least once in a temperature region of not less than T1 + 30 ° C or more than T1 + 200 ° C, and in a temperature range of less than T1 + 30 * 0, the rate of reduction to such has been adjusted to 30% or less. Incidentally, in finishing lamination, lamination at a reduction rate of 30% or more in one pass was performed in a final pass in the region of temperatures of not less than T1 + 30 ° C or more than T1 + 200 ° C. However, for steel types A4, A5, A6 and B3, rolling at a reduction rate of 30% or more was not carried out in the region of temperatures of no less than T1 + 30 ° C nor more than T1 + 200 ° Ç. In addition, for types P2 and P3 steels, the total reduction rate in the temperature range of less than T1 + 30 ° C was greater than 30%. In addition, in finishing lamination, the total reduction rate has been adjusted to 50% or more. However, for steel types A4, A5, A6, B3, and C3, the total reduction rate in the temperature region of not less than T1 + 30 ° C nor more than T1 + 200 ° C was less than 50% . Table 2 shows, in the finishing lamination, the reduction rate (%) in the final pass in the region of temperatures of not less than T1 + 30 ° C nor more than T1 + 200 ° C and the reduction rate in a pass in one step prior to the final pass (ratio of reduction in one pass before the end) (%). In addition, Table 2 shows, in the finishing lamination, the total reduction rate (%) in the temperature region of not less than T1 + 30 * C nor more than T1 + 200 ° C, the temperature (° C) after the reduction in the final pass in the region of temperatures of not less than T1 + 30 ° C nor more than T1 + 200 ° C, and a maximum amount of working heat generation (° C) at the time of reduction in the region of temperatures of not less than T1 + 30 ° C nor more than T1 + 200 ° C. After the final reduction in the temperature region of not less than T1 + 30 ° C or more than T1 + 200 ° C was carried out on the finishing laminate, the primary cold pre-lamination cooling was started 40/60 before a waiting time t seconds exceeding 2.5 x t1. In primary cold pre-lamination cooling, the average cooling rate has been adjusted to 50 ° C / s or more. In addition, the temperature change (the amount of temperature cooled) in the primary cold pre-lamination cooling was adjusted to fall within a range of not less than 40% or more than 140Ό. However, in relation to type J2 steel, the primary cold pre-rolling cooling was started after the waiting time t seconds exceeded 2.5 x t1 since the final reduction in the temperature region of not less than T1 + 30 ° C nor greater than T1 + 200 ° C in the finishing laminate. In relation to type T2 steel, the temperature change (amount of temperature cooled) in the primary cold pre-rolling cooling was less than 40Ό, and in relation to the type of steel T3, the average cooling rate in the primary cooling cold pre-lamination was less than õOO / s. Table 2 shows t1 (seconds) of the respective types of steel, the waiting time t (seconds) from the final reduction in the temperature region of not less than T1 + 30 ° C nor greater than T1 + 200 ° C until the beginning primary cold pre-lamination cooling in finishing lamination, t / t1, temperature change (amount cooled) (Ό) in primary cold pre-lamination cooling, and the average cooling rate (O / s) in primary cold pre-lamination cooling. After the primary cold pre-lamination cooling, the secondary cold pre-lamination cooling was performed. After the primary cold pre-lamination cooling, the secondary cold pre-lamination cooling started in up to three seconds. In addition, the secondary cold pre-lamination cooling, the cooling was performed until the cooling stop temperature of 600 “C or less at an average cooling rate of 10 to 300 ° C / s, the winding was performed at 600 * C or less, and original cold-rolled sheets having a thickness of 2 to 5 mm were obtained. However, in relation to type D3 steel, three seconds passed before the secondary cold pre-lamination cooling was started after the primary cold pre-lamination cooling. Furthermore, in relation to the 41/60 type D3 steel, the average cooling rate of secondary cold pre-rolling cooling was greater than 300 * C / s. In addition, in relation to type E3 steel, the cooling stop temperature of the secondary cold pre-rolling cooling (coiling temperature) was greater than 600Ό. Table 2 shows, for the respective types of steel, the time (seconds) until the start of the secondary cold pre-lamination cooling after the primary cold pre-lamination cooling, the average cooling rate (* C / s) secondary cold pre-lamination cooling, and the cooling stop temperature (* C) of secondary cold pre-lamination cooling (coiling temperature). Then, the original hot-rolled sheets were stripped and then subjected to cold rolling at a reduction rate of not less than 30% or more than 70%. However, in relation to steel type T4, the reduction rate of cold rolling was less than 30%. In addition, in relation to steel type T5, the reduction rate of cold rolling was greater than 70%. Table 3 shows the reduction ratio (%) of the cold rolling of the respective types of steel. After cold rolling, heating was performed to a temperature range of 700 to 900Ό and retention was performed for no less than 1 second or more than 1000 seconds. In addition, when the heating was carried out to the temperature range of 700 to 900 ° C, the average heating rate HR1 (° C / s) of not less than room temperature nor more than 650 * C was set to 0, 3 or more (HR1 ü 0.3), and an average HR2 heating rate (* C / s) of more than 650 * C to 700 to 900 * C has been adjusted to 0.5 x HR1 or less (HR2 0, 5 x HR1). However, in relation to steel type A1, the heating temperature was higher than 900 * C. Regarding steel type Q2, the heating temperature was less than 700 * C. Regarding steel type Q3, heating and holding time were less than 1 second. Regarding the type of steel Q4, the heating and the retention time were more than 1000 seconds. In addition, in relation to steel type T6, the average rate of heating HR1 was less than 0.3 (* C / s). In relation to type T7 steel, the average rate of 42/60 HR2 heating (* C / s) was greater than 0.5 x HR1. Table 3 shows the heating temperature (° C) and the average heating rates HR1 and HR2 (° C / s) of the respective types of steel. After heating and retention, primary cooling after cold rolling was performed to a temperature range of 580 to 750 * 0 at an average cooling rate of 12 ° C / s or less. However, in relation to type A2 steel, the average cooling rate in primary cooling after cold rolling was greater than 12 * C / s. In addition, for type A2 steel, the primary cooling stop temperature after cold rolling was less than 580 * 0, and for K1 type steel, the primary cooling stop temperature after cold rolling was greater than 740 * 0. Table 3 shows, of the respective types of steel, the average cooling rate (* C / s) and the cooling stop temperature (* C) in primary cooling after cold rolling. Subsequently to the primary cooling of the cold post-lamination, secondary cooling was performed after the cold rolling to the temperature region of 350 to 500 * 0 at an average cooling rate of 4 to 300 * C / s. However, in relation to steel type A5, the average cooling rate of secondary cooling after cold rolling was less than 4 * O / s. In relation to steel type P4, the average cooling rate of secondary cooling after cold rolling was greater than 300 * C / s. In addition, for type A2 steel, the secondary cooling stop temperature after cold rolling was greater than 500 * 0, and for G1 type steel, the secondary cooling stop temperature after cold rolling was less than 350 * 0. Table 3 shows the average cooling rate (* C / s) in secondary cooling after the cold rolling of the respective types of steel. Subsequently to secondary cooling after cold rolling, an aging heat treatment (OA) was performed at the stop temperature of secondary cooling after cold rolling. The temperature range of this thermal aging treatment (OA) (secondary cooling stop temperature after cold rolling) 43/60 has been adjusted to not less than 350 * C or more than 500 * 0. In addition, the aging treatment time (OA) was adjusted to not less than 12 seconds or more than 400 seconds. However, in relation to steel type A2, the temperature of the heat treatment of aging was greater than 500 * 0, and in relation to steel type G1, the temperature of the heat treatment of aging was less than 350 * 0. In addition, in relation to steel type D1, the aging treatment time was less than 12 seconds, and in relation to steel types C2 and G1, the aging treatment time was greater than 400 seconds. Table 3 shows the heat treatment temperature of aging (* C), t2 (seconds), and the treatment time (seconds) of the respective types of steel. After the thermal treatment of aging, the 0.5% skin pass lamination was performed and the material evaluation was performed. Incidentally, in type S1 steel, a hot dip galvanizing treatment was carried out. In type T1 steel, a bonding treatment was carried out in a temperature range of 450 to 600 ° C after galvanizing. Table 4 shows area ratios (structural fractions) (%) of ferrite, bainite, perlite, martensite and austenite retained in a metallic structure of the respective types of steel and, of the respective types of steel, the average diameter (mean value) of the crystal grains (μιτι), and the ratio, in the crystal grains, of the length dL in the lamination direction to the length dt in the direction of the thickness of the plate dL / dt. Table 5 shows, of the respective types of steel, the average value of the pole densities of the {100} <011> to {223} <110> orientation group and the polar density of the {332} <113> crystal orientation in a central portion of the plate thickness with a range of 5/8 to 3/8 in the plate thickness from the surface of the steel plate. Incidentally, the structural fraction was evaluated by the structural fraction before skin pass lamination. In addition, Table 5 shows as mechanical properties of the respective types of steel, the tensile strength TS (MPa), the uniform elongation u-EI (%), and the bore expansion ratio λ (%) as an index of the local deformation capacity. Table 5 shows rC, rl_, r30, and r60 each being the value r. 44/60 Incidentally, the tensile test was based on the JIS Z 2241. The bore expansion test was based on the Japan Iron and Steel Federation standard JFS T1001. The pole density of each crystal orientation was measured using the EBSP previously described at an inclination of 0.5 μιη 5 in a region of 3/8 to 5/8 in the thickness of the sheet of a cross section parallel to the lamination direction . In addition, as indices of uniform elongation and hole expansion capacity, TS x EL has been adjusted to 8000 (MPa%) or more, and desirably adjusted to 9000 (MPa%) or more, and TS x λ has been adjusted to 30000 (MPa%) or more, preferably 10 adjusted to 40,000 (MPa%) or more, and even more preferably to 50,000 (MPa%) or more. Table 1 (Part 1) T1 / C Ç Si Mn P s Al N 0 Si + AI fi THE 851 0.070 0.08 1.30 0.015 0.004 0.040 0.0026 0.0032 0.12 - B 851 0.070 0.08 1.30 0.015 0.004 0.040 0.0026 0.0032 0.12Ç 865 0.080 0.31 1.35 0.012 0.005 0.016 0.0032 0.0023 0.33D 865 0.080 0.31 1.35 0.012 0.005 0.016 0.0032 0.0023 0.33AND 858 0.060 0.87 1.20 0.009 0.004 0.038 0.0033 0.0026 0.91F 858 0.060 0.30 1.20 0.009 0.004 0.500 0.0033 0.0026 0.80G 865 0.210 0.15 1.62 0.012 0.003 0.026 0.0033 0.0021 0.18 0.021 H 865 0.210 0.90 1.62 0.012 0.003 0.026 0.0033 0.0021 0.93 0.021 I 861 0.035 0.67 1.88 0.015 0.003 0.045 0.0028 0.0029 0.72 - J 886 0.035 0.67 1.88 0.015 0.003 0.045 0.0028 0.0029 0.72 0.1 K 875 0.180 0.48 2.72 0.009 0.003 0.050 0.0036 0.0022 0.53 - L 892 0.180 0.48 2.72 0.009 0.003 0.050 0.0036 0.0022 0.53 - M 892 0.060 0.11 2.12 0.010 0.005 0.033 0.0028 0.0035 0.14 0.036 N 886 0.060 0.11 2.12 0.010 0.005 9.033 0.0028 0.0035 0.14 0.089 0 903 0.040 0.13 1.33 0.010 0.005 0.038 0.0032 0.0026 0.17 0.042 P 903 0.040 0.13 1.33 0.010 0.005 0.038 0.0036 0.0029 0.17 0.042 Q 852 0.180 0.50 0.90 0.008 0.003 0.045 0.0028 0.0029 0.55R 852 0.190 0.30 1.30 0.080 0.002 0.030 0.0032 0.0022 0.33s 852 0.180 0.21 1.30 0.010 0.002 0.650 0.0032 0.0035 0.86T 880 0.035 0.02 1.30 0.010 0.002 0.035 0.0023 0.0033 0.06 0.12 The 856 0.450 0.52 1.33 0.260 0.003 0.045 0.0026 0.0019 0.57B 1376 0.072 0.15 1.42 0.014 0.004 0.036 0.0022 0.0025 0.19ç 851 0.110 0.23 1.12 0.021 0.003 0.026 0.0025 0.0023 0.26d 1154 0.250 0.23 1.56 0.024 0.120 0.034 0.0022 0.0023 0.26and 854 0.250 0.23 1.54 0.020 0.002 0.038 0.0026 0.0032 0.27f 854 0.250 0.21 1.54 0.020 0.002 0.034 0.0026 0.0023 0, .24g 853 0.220 0.20 1.53 0.015 0.004 0.031 0.0028 0.0026 0.23H 852 0.180 2.30 0.90 0.008 0.003 0.045 0.0028 0.0022 0.35 45/60 Table 1 (Part 2 / Nb B Mg Rem Here Mo Cr Ni w THE 0.00 -- - B 0.00 0.005- - Ç 0.04 -- - D 0.04 -- 0.002 AND 0.02 -0.02 - F 0.02 -0.02 - G 0.00 0.002 - 0.03 0.35 H 0.00 0.002 - 0.03 0.35 -I 0.02 - 00.0015 - J 0.02 - 00.0015 - K - - 0- 0.1 L 0.05 - 00.002 0.1 M 0.089 0.001 N 0.036 0.001 0 0.121 9E-04 P 0.121 9E-04 Q - 0.004 0.1 R 0.1sTTheB 15 ç PJ5 d 5.0 andf9H Table 1 (Part 3) Zr At V Ass Co Sn Pb Y Hf NOTE THE - Invention steel B - Invention steel ÇInvention steel DInvention steel ANDInvention steel FInvention steel GInvention steel HInvention steel I 0.03 Invention steel J 0.03 Invention steel K 0.1 Invention steel L 0.1 Invention steel M - 0Invention steel N - - 0 Invention steel 46/60 0 0 - - - - 0 - - - Invention steel P 0 Invention steel QInvention steel RInvention steel s 0 Invention steel T - 0.0020.2Invention steel TheComparative steel BComparative steel çComparative steel d 2.5 Comparative steel and 1 Comparative steel f 43 Comparative steel g pjComparative steel H -Comparative steel Table 2 (part 1) Steel type B.C1/0 T1 0 No. of times of reduction to 40% or more to not less than 1000 * 0 or more than 12000 Reduction ratio to 40% or more to not less than 1000 * 0 or more than 12000 Grain diameter of austenite m Reduction ratio to T1 + 30 * 0 to T1 + 2000 /% Maximum working heat generation at reduction T1 + 300 to T1 + 2000 /% /% TO 1 711 851 1 50 140 85 15 A2 711 851 2 45/40 85 80 5 A3 711 851 0290 65 18 A4 711 851 2 45/45 90 45 18 A5 711 851 2 45/40 85 45 18 A6 711 851 2 45/40 90 43 18 B1 711 851 1 50 145 85 15 B2 711 851 2 45/40 85 75 5 B3 711 851 2 45/40 85 44 18 C1 718 865 2 45/40 80 79 15 C2 718 865 2 45/45 80 76 18 C3 718 865 2 45/45 80 44 15 D1 718 865 2 45/45 80 82 15 D2 718 865 2 45/45 80 67 18 D3 718 865 2 40/40/40 60 76 18 E1 735 735 2 45/45 90 67 13 E2 735 735 0 45/45 90 85 14 E3 735 735 2320 65 13 F1 719 719 2 45/40 90 67 13 F2 719 719 2 45/40 90 85 14 F3 719 719 2 45/40 95 67 13 G1 716 716 2 45/45 95 85 14 G2 716 716 3 40/45 95 65 12 H1 738 865 2 40/40/40 55 65 16 11 722 861 1 45/40 95 75 17 47/60 12 722 861 1 50 130 65 18 13 722 861 2 70 140 85 40 Π 722 886 1 45/40 85 65 17 j2 722 886 1 50 125 65 18 j3 722 886 3 50 125 65 18 Κ1 708 875 3 40/40/40 65 75 18 L1 708 892 3 40/40/40 70 65 18 Μ1 704 892 0 40/40/40 65 75 10 M2 704 892 3390 65 30 Ν1 704 886 2 40/40/40 65 75 10 01 713 903 2 45/45 75 85 15 02 713 903 2 45/45 120 65 12 Ρ1 713 903 2 45/45 70 85 13 Ρ2 713 903 2 45/40 80 78 14 Ρ3 713 903 2 45/45 80 68 18 Ρ4 713 903 2 45/45 90 84 15 Q1 728 852 2 45/45 80 85 10 02 728 852 1 45/40 95 76 18 Q3 728 852 1 50 145 84 14 04 728 852 1 50 130 66 17 R1 733 852 2 45/45 80 85 12 R2 733 852 2 45/45 75 85 12 R3 733 852 2 45/45 80 65 13 R4 733 852 2 45/45 70 85 12 S1 715 852 2 45/45 80 75 12 S2 715 852 2 45/45 65 75 12 S3 715 852 2 45/45 80 70 16 S4 715 852 2 45/45 85 75 12 Τ1 710 880 2 45/45 75 70 12 Τ2 710 880 2 45/45 75 70 12 Τ3 710 880 2 45/45 110 75 12 Τ4 710 880 2 45/45 80 75 14 Τ5 710 880 2 45/45 75 65 12 Τ6 710 880 2 45/45 85 75 15 Τ7 710 880 2 45/45 75 80 12 to 1 724 855b1 712 1376 c1 718 851 d1 798 1154 e'1 713 850 f1 713 850 gi 712 950 h1 780 852 48/60 Table 2 (part 2) Steel type TF Temperature after final reduction to 30% or more / G Pass reduction ratio before end aT1 + 30 * Caté T1 + 200 * 0 / * C Final pass reduction ratio to T1 + 30 * 0 to T1 + 200 * C / *% Reduction ratio in the reduction in the region of temperatures below T1 30 * C / *% t1 Waiting time for the start of the primary cold pre-lamination cooling after the end of the final lamination at 30% or more ./s TO 1 935 40 40 0 0.57 0.68 A2 891 40 35 0 1.77 2.12 A3 930 30 30 0 1.08 1.29 A4 925 20 20 10 1.70 2.05 A5 930 20 20 10 1.63 1.95 A6 935 20 20 10 1.55 1.86 B1 935 40 40 0 0.57 0.68 B2 892 35 35 0 1.75 2.09 B3 930 20 20 10 1.63 1.96 C1 945 37 37 0 0.76 0.91 C2 920 40 31 0 1.54 1.85 C3 1080 10 30 0 0.23 0.27 D1 950 40 37 0 0.67 0.80 D2 922 31 31 0 1.50 1.80 D3 922 40 31 0 1.50 1.80 E1 955 31 31 0 0.73 0.87 E2 933 40 40 0 0.73 0.88 E3 930 30 30 0 1.21 2.31 F1 955 31 31 0 0.73 1.38 F2 933 40 40 0 0.73 1.39 F3 955 31 31 0 0.73 1.38 G1 935 40 40 0 0.84 1.59 G2 875 30 30 10 2.79 5.30 H1 970 30 30 0 0.66 1.26 11 961 40 30 0 0.73 1.39 I2 922 30 30 0 1.44 2.73 I3 860 40 40 20 3.14 6.91 ii 960 30 30 0 1.17 2.58 j2 920 30 30 0 2.09 10.30 j3 920 30 30 0 2.09 4.60 K1 990 40 30 0 0.53 1.17 L1 990 30 30 0 0.77 1.69 M1 943 35 35 0 1.46 3.21 M2 942 20 40 0 1.32 2.90 N1 940 35 35 0 1.40 3.09 01 985 40 40 0 0.61 1.34 02 880 30 30 20 3.92 8.62 P1 1012 40 40 0 0.25 0.56 P2 944 38 38 40 0.76 0.93 P3 924 30 30 35 1.50 1.82 49/60 Ρ4 930 40 40 0 0.73 0.89 Q1 958 40 40 0 0.28 0.62 02 962 40 30 0 0.73 1.40 Q3 938 42 40 0 0.57 0.69 04 925 31 32 0 1.44 2.75 R1 996 40 40 0 0.14 0.31 R2 990 40 40 0 0.13 0.10 R3 996 35 35 0 0.15 0.10 R4 999 40 40 0 0.15 0.11 S1 958 30 40 0 0.28 0.62 S2 958 30 40 0 0.28 0.18 S3 960 35 35 0 0.41 0.37 S4 959 30 40 0 0.27 0.21 T1 985 30 35 0 0.44 0.98 T2 984 30 35 0 0.46 1.02 T3 984 35 35 0 0.46 1.02 T4 984 30 40 0 0.30 0.66 T5 983 35 35 0 0.48 1.05 T6 984 30 40 0 0.30 0.66 T7 982 30 35 0 0.49 1.08 to 1 b1 c1FRACTURE OCCURRED DURING LAMINATION d1THE HOT e'1 f1 £ L · h1 Table 2 '3rd part) Steel type trt1 Primary cooling quantity rc cold pre-lamination Cold pre-lamination primary cooling rateC / s Time to start secondary pre-lamination cooling, / s Secondary cold pre-lamination cooling rateC / s Bobbin temperature / C TO 1 1.20 85 71 3.0 185.0 426 A2 1.20 95 60 3.0 190.0 427 A3 1.20 100 60 4.0 140.0 413 A4 1.20 125 60 3.0 220.0 477 A5 1.20 130 60 3.0 10.0 328 A6 1.20 115 58 3.0 83.0 596 B1 1.20 110 60 3.0 225.0 312 B2 1.20 90 69 3.0 189.0 434 B3 1.20 130 60 3.0 75.0 335 50/60 C1 1.20 90 60 2.0 130.0 423 C2 1.20 100 60 3.0 200.0 426 C3 1.20 110 55 2,- 210.0 329 D1 1.20 110 60 3.0 200.0 496 D2 1.20 90 75 3.0 110.0 452 D3 1.20 95 70 38.0 320.0 514 E1 1.20 80 73 3.0 215.0 477 E2 1.20 75 70 3.0 105.0 518 E3 1.90 100 71 3.0 135.0 660 F1 1.90 80 70 3.0 210.0 477 F2 1.90 110 70 3.0 200.0 518 F3 1.90 100 100 3.0 158.0 484 G1 1.90 90 70 3.0 165.0 448 G2 1.90 125 70 3.0 160.0 494 H1 1.90 110 70 3.0 77.0 416 11 1.90 110 79 3.0 188.0 546 I2 1.90 110 70 3.0 75.0 443 I3 2.20 90 70 3.0 175.0 521 | 1 2.20 95 70 2.0 160.0 465 j2 4.93 100 63 3.0 70.0 532 j3 2.20 235 70 3.0 78.0 380 K1 2.20 90 70 3.0 165.0 437 L1 2.20 90 70 3.0 75.0 375 M1 2.20 125 74 3.0 145.0 378 M2 2.20 80 70 3.0 166.0 394 N1 2.20 100 65 3.0 186.0 431 01 2.20 110 65 2.0 100.0 335 02 2.20 90 50 3.0 95.0 384 P1 2.20 95 65 3.0 104.0 435 P2 1.23 95 55 2.0 135.0 425 P3 1.22 95 75 3.0 105.0 455 P4 1.22 75 77 3.0 210.0 510 Q1 2.20 110 65 3.0 75.0 482 02 1.92 115 80 3.0 192.0 549 Q3 1.21 105 65 3.0 221.0 316 04 1.91 105 75 3.0 78.0 448 R1 2.20 90 65 3.0 180.0 410 R2 0.80 90 75 3.0 180.0 410 R3 0.70 90 65 2.5 145.0 420 R4 0.75 90 65 3.0 180.0 425 S1 2.20 90 53 3.0 180.0 401 S2 0.65 90 65 3.0 140.0 401 S3 0.90 90 65 2.0 160.0 430 S4 0.80 90 69 3.0 140.0 435 T1 2.20 95 75 2.0 180.0 359 T2 2.20 25 75 2.0 180.0 356 T3 2.20 95 30 2.0 167.0 478 51/60 T4 2.20 95 75 2.0 166.0 359 T5 2.20 95 68 2.5 180.0 440 T6 2.20 95 75 2.0 187.0 362 T7 2.20 95 75 3.0 180.0 355 a1 b1 c1 d1 e'1 f1 gi h1 Table 3 (part 1) Steel type Cold rolling ratio (%) HR1 (O / s) HR2 (€ / s) Heating temperature (C) Retention time at heating temperature (s) Primary cooling rate after cold rolling (üs) TO 1 34 7.0 2.5 956 168 11 A2 38 2.6 0.9 750 131 44 A3 42 0.9 0.3 800 142 10 A4 39 5.3 1.8 834 104 12 A5 41 7.9 2.8 778 121 11 A6 52 1.8 0.6 770 128 11 B1 60 8.8 3.1 776 149 11 B2 60 8.8 3.1 820 113 10 B3 41 8.8 3.1 792 91 12 C1 47 4.4 1.5 840 157 11 C2 32 8.8 3.1 830 146 11 C3 60 8.8 3.1 808 174 12 D1 32 7.0 2.5 780 46 10 D2 31 1.8 0.6 886 176 11 D3 38 3.5 1.2 843 145 9 E1 48 0.9 0.3 867 111 10 E2 50 7.0 1.7 774 114 9 E3 33 7.9 1.9 756 150 12 F1 48 1.8 0.4 867 163 10 F2 50 0.9 0.2 780 66 9 F3 33 8.8 2.1 760 118 10 G1 43 8.8 2.1 808 123 12 G2 60 6.2 1.5 768 99 11 H1 44 3.5 0.8 794 117 10 11 34 7.0 1.7 895 158 10 I2 40 4.4 1.1 856 68 12 I3 38 1.8 0.4 880 168 12 Π 35 5.3 1.3 775 127 9 j2 57 6.2 1.5 783 111 10 J3 66 6.2 1.5 846 180 9 52/60 K1 44 6.2 1.5 770 103 9 L1 52 8.8 2.1 775 136 9 M1 40 7.0 2.5 780 152 11 M2 35 0.9 0.3 870 110 11 N1 31 7.9 2.9 850 142 12 01 54 1.8 0.6 756 131 11 02 47 7.9 2.9 790 166 12 P1 33 8.8 3.2 850 124 12 P2 46 4.3 1.5 842 158 11 P3 30 1.7 0.6 888 175 11 P4 51 7.1 1.7 775 113 9 Q1 55 7.0 2.7 899 157 10 02 35 7.0 1.7 588 159 10 Q3 62 8.9 3.1 778 Pan 11 04 41 4.4 1.1 857 1360 12 R1 37 5.3 2.0 883 158 11 R2 44 6.2 2.3 873 67 11 R3 37 0.9 0.3 870 99 10 R4 36 0.9 0.3 854 111 11 S1 50 1.8 0.7 766 101 11 S2 48 8.8 3.3 770 119 12 S3 49 7.0 2.7 780 87 11 S4 50 0.9 0.3 765 95 9 T1 47 1.8 0.7 760 121 12 T2 47 6.2 2.3 880 54 12 T3 44 0.9 0.3 776 74 11 T4 14 1.8 0.7 890 91 12 T5 89 8.8 3.3 774 130 9 T6 47 02 0.1 768 138 10 T7 43 1.8 1.6 761 85 12 to 1 b1 c1 d1 e'1 f1 gi h1 Table 3 (part 2) Steel type Primary cooling stop temperature after cold rolling (fC) Secondary cooling rate after cold rollingW Temperature in OA(Ό) Retention time at 0A(s) t2(s) Presence / absence of galvanizing Connection temperature (C) TO 1 650 50 480 226 61 ABSENCE - A2 5] 0 50 480 226 61 ABSENCE - A3 740 50 370 226 61 ABSENCE - 53/60 Α4 655 50 370 226 61 ABSENCEΑ5 639 3 570 230 400 ABSENCEΑ6 700 50 372 220 55 ABSENCEΒ1 689 50 450 185 20 ABSENCEΒ2 688 49 450 185 20 ABSENCEΒ3 632 50 440 182 17 ABSENCEC1 727 49 450 185 20 ABSENCEC2 682 48 317 550 400 ABSENCEC3 681 49 480 226 61 ABSENCED1 673 49 480 36 61 ABSENCED2 659 49 326 276 400 ABSENCED3 588 50 405 183 18 ABSENCEE1 694 49 406 183 18 ABSENCEE2 737 49 380 203 38 ABSENCEE3 700 49 415 181 16 ABSENCEF1 694 48 406 183 18 ABSENCEF2 737 48 444 183 18 ABSENCEF3 666 48 410 182 17 ABSENCEG1 598 49 265 575 400 ABSENCEG2 679 50 458 190 25 ABSENCEH1 702 48 363 254 89 ABSENCE11 636 50 456 189 24 ABSENCEI2 707 48 356 301 136 ABSENCEI3 591 49 365 244 79 ABSENCEj1 733 48 373 218 53 ABSENCEj2 725 50 459 191 26 ABSENCEj3 737 49 370 226 61 ABSENCEK1 760 49 434 181 16 ABSENCEL1 657 50 416 181 16 ABSENCEM1 730 48 441 182 17 ABSENCEM2 612 49 385 197 32 ABSENCEN1 588 49 476 215 50 ABSENCE01 660 50 477 218 53 ABSENCE02 647 49 406 183 18 ABSENCEP1 593 49 459 191 26 ABSENCEP2 726 49 452 185 20 ABSENCEP3 660 49 325 276 400 ABSENCEP4 740 358 379 203 38 ABSENCEQ1 746 49 450 185 20 ABSENCE02 635 50 455 189 24 ABSENCEQ3 690 50 449 185 20 ABSENCE04 705 48 357 301 136 ABSENCER1 719 50 466 198 33 ABSENCER2 725 49 477 218 53 ABSENCER3 718 50 476 215 50 ABSENCER4 719 48 420 180 15 ABSENCES1 652 50 450 185 20 PRESENCE WITHOUT CONNECTION 54/60 S2 662 47 449 185 20 ABSENCES3 670 50 458 190 25 ABSENCES4 668 48 452 186 21 ABSENCET1 642 49 422 180 15 PRESENCE 585 T2 670 49 378 207 42 ABSENCET3 655 50 376 211 46 ABSENCET4 657 50 446 184 19 ABSENCET5 660 49 389 192 27 ABSENCET6 735 48 467 199 34 ABSENCET7 732 49 389 192 27 ABSENCEto 1 OCCURREDb1 FRACTUREc1 DURINGd1 THE LAMINATIONe'1 THE HOTf1 gi h1 Table 4 (Part I) Steel type Phenite fraction (%) Bainite fraction (%) Perlite fraction (%) Fraction of martensite(%) Retained γ fraction (%) TO 1 57.2 39.5 3.1 0.1 0.1 A2 2.0 9 £ 4 0.2 0.3 0.1 A3 59.2 40.0 0.1 0.4 0.3 A4 62.9 36.0 0.2 0.6 0.3 A5 56.2 33.4 0.1 10J 0.2 A6 61.6 38.0 0.1 0.1 0.2 B1 60.6 39.0 0.1 0.1 0.2 B2 55.0 44.0 0.1 0.7 0.2 B3 60.7 37.0 0.1 0.9 1.3 C1 64.0 35.0 0.1 0.6 0.3 C2 60.0 43 0.1 0.8 34.8 C3 65.4 33.0 0.4 0.9 0.3 D1 53.8 6.0 0.1 39JJ 0.3 D2 58.0 38.0 3.1 0.8 0.1 D3 42.3 57.0 0.1 0.5 0.1 E1 55.5 41.9 2.1 0.4 0.1 E2 53.1 42.7 4.0 0.0 0.2 E3 67.2 28.0 3.7 0.9 0.2 F1 55.5 41.9 1.5 0.9 0.2 F2 53.1 43.0 3.1 0.5 0.3 F3 53.3 44.7 1.5 0.3 0.2 G1 57.4 2Í 0.2 402 0.2 G2 59.8 35.0 3.7 0.3 0.2 H1 56.2 40.0 3.2 0.5 0.1 11 50.9 46.0 2.7 0.2 0.2 I2 67.9 30.0 1.3 0.5 0.3 55/60 13 56.7 40.0 2.4 0.6 0.3 j1 52.8 45.0 1.5 0.5 0.2 j2 58.0 40.0 1.7 0.1 0.2 j3 53.1 43.0 3.5 0.2 0.2 K1 90J 22 u 0.1 0.1 L1 47.3 52.1 0.2 0.3 0.1 M1 64.2 35.0 0.3 0.4 0.1 M2 53.9 43.0 2.8 0.2 0.2 N1 56.4 39.0 4.1 0.3 0.2 01 59.1 38.0 3.3 0.4 0.2 02 62.1 33.0 4.3 0.4 0.2 P1 56.9 40.0 2.7 0.3 0.1 P2 64.0 35.0 0.1 0.6 0.3 P3 58.0 38.0 3.1 0.8 0.1 P4 43.2 12 0.1 55J 0.3 Q1 59.7 38.0 2.1 0.1 0.1 02 862 2.2 114 0.2 0.2 Q3 78.9 15 0.1 19.3 0.2 04 67.9 30.0 1.3 0.5 0.3 R1 63.3 34.5 2.0 0.1 0.1 R2 63.1 35.2 1.3 0.2 0.2 R3 61.8 35.7 2.1 0.2 0.2 R4 58.9 38.9 1.9 0.1 0.2 S1 57.4 40.0 2.4 0.1 0.1 S2 59.4 39.2 1.1 0.2 0.1 S3 58.8 39.0 1.9 0.1 0.2 S4 52.9 45.2 1.6 0.1 0.2 T1 61.6 36.0 2.2 0.1 0.1 T2 61.5 36.5 1.8 0.1 0.1 T3 61.0 38.0 0.8 0.1 0.1 T4 56.9 40.3 2.1 0.4 0.3 T5 61.4 37.9 0.4 0.2 0.1 T6 60.6 38.6 0.5 0.2 0.1 T7 59.0 39.8 9.5 0.4 0.3 to 1b1c1 OCCURRED d1 FRACTURE e'1 DURING f1 THE LAMINATION gi THE HOT h1 Table 4 (part 2) Steel type Diameter (pm) dL (pm) dT (pm) Expression 3 dL / dt Note TO 1 230.0 235.9 213.8 1.1 COMPARATIVE STEEL A2 5.8 5.4 3.2 1.7 COMPARATIVE STEEL A3 102 9.6 9.6 1.0 COMPARATIVE STEEL 56/60 Α4 8J) 7.6 2.3 3J COMPARATIVE STEEL Α5 8J) 7.6 1.9 40 COMPARATIVE STEEL Α6 19 7.5 0.8 9J) COMPARATIVE STEEL Β1 5.3 4.9 2.7 1.8 STEEL OF THE PRESENT INVENTION Β2 5.8 5.4 2.5 2.1 STEEL OF THE PRESENT INVENTION Β3 8J) 7.6 1.8 41 COMPARATIVE STEEL C1 5.5 5.1 2.6 1.9 STEEL OF THE PRESENT INVENTION C2 6.1 5.7 2.4 2.3 COMPARATIVE STEEL C3 5.7 5.3 2.5 2.1 COMPARATIVE STEEL D1 5.4 5.0 2.0 2.6 COMPARATIVE STEEL D2 6.1 6.9 4.6 1.5 STEEL OF THE PRESENT INVENTION D3 110 11.8 7.8 1.5 COMPARATIVE STEEL E1 6.0 6.8 3.3 2.1 STEEL OF THE PRESENT INVENTION E2 5.3 6.1 3.3 1.8 STEEL OF THE PRESENT INVENTION E3 1CL9 11.7 7.8 1.5 COMPARATIVE STEEL F1 6.0 6.8 5.6 1.2 STEEL OF THE PRESENT INVENTION F2 5.3 6.1 3.2 1.9 STEEL OF THE PRESENT INVENTION F3 6.0 6.8 3.9 1.7 STEEL OF THE PRESENT INVENTION G1 5.3 6.1 3.2 1.9 COMPARATIVE STEEL G2 6.4 7.2 7.0 1.0 COMPARATIVE STEEL H1 6.0 6.8 3.0 2.2 STEEL OF THE PRESENT INVENTION 11 6.1 6.9 3.3 2.1 STEEL OF THE PRESENT INVENTION I2 6.2 7.0 2.5 2.8 STEEL OF THE PRESENT INVENTION I3 8J 9.1 4.5 2.0 COMPARATIVE STEEL j1 6.1 6.0 2.7 2.2 STEEL OF THE PRESENT INVENTION j2 9j) 8.9 4.1 2.2 COMPARATIVE STEEL j3 6.2 6.1 5.0 1.2 COMPARATIVE STEEL K1 6.0 5.9 3.4 1.7 COMPARATIVE STEEL L1 6.0 6.3 3.6 1.7 STEEL OF THE PRESENT INVENTION M1 5.6 5.9 2.0 2.9 STEEL OF THE PRESENT INVENTION M2 8J 8.6 5.7 1.5 COMPARATIVE STEEL N1 5.6 5.9 2.9 2.0 STEEL OF THE PRESENT INVENTION 01 5.1 5.4 3.2 1.7 STEEL OF THE PRESENT INVENTION 02 8J 8.6 2.4 3.6 COMPARATIVE STEEL P1 5.1 5.4 2.1 2.5 STEEL OF THE PRESENT INVENTION P2 2.5 2.8 0.6 47 COMPARATIVE STEEL P3 2.8 2.9 0.7 41 COMPARATIVE STEEL P4 5.3 6.1 3.3 1.8 COMPARATIVE STEEL Q1 5.2 5.5 2.4 2.3 STEEL OF THE PRESENT INVENTION 02 6.1 6.9 3.3 2.1 COMPARATIVE STEEL Q3 5.3 4.9 2.7 1.8 COMPARATIVE STEEL 04 220.5 221.0 220.0 2.8 COMPARATIVE STEEL R1 5.1 5.4 2.1 2.6 STEEL OF THE PRESENT INVENTION R2 4.1 4.4 1.8 2.5 STEEL OF THE PRESENT INVENTION R3 4.2 4.5 1.9 2.4 STEEL OF THE PRESENT INVENTION R4 4.0 4.3 1.9 2.3 STEEL OF THE PRESENT INVENTION S1 5.2 5.5 3.3 1.7 STEEL OF THE PRESENT INVENTION 57/60 S2 4.0 4.3 1.7 2.5 STEEL OF THE PRESENT INVENTION S3 4.0 4.3 2.0 2.2 STEEL OF THE PRESENT INVENTION S4 4.1 4.4 1.6 2.8 STEEL OF THE PRESENT INVENTION T1 5.5 5.8 3.5 1.7 STEEL OF THE PRESENT INVENTION T2 8J 8.9 2.4 32 COMPARATIVE STEEL T3 8.5 8.8 2.5 3Jj COMPARATIVE STEEL T4 9j) 9.3 0.9 10J) COMPARATIVE STEEL T5 4.0 4.3 1.9 2.3 COMPARATIVE STEEL T6 3.8 4.1 1.8 2.3 COMPARATIVE STEEL T7 4.4 4.7 2.8 1.7 COMPARATIVE STEEL to 1COMPARATIVE STEEL b1 COMPARATIVE STEEL c1 COMPARATIVE STEEL d1 COMPARATIVE STEEL e'1 COMPARATIVE STEEL f1 COMPARATIVE STEEL gi COMPARATIVE STEEL h1 COMPARATIVE STEEL Table 5 (part 1 ' Steel type TS (Mpa) u-EL(%) EL(%) λ (%) Average pole density value of the guidance group {100} <011> to {223} <110> Pole density of crystal orientation {332} <113> TO 1 645 10 12 44.0 2.9 2.6 A2 560 6 9 36.0 1.7 2.0 A3 830 11 15 86.6 2.9 2.4 A4 751 12 18 44.0 1.8 2.4 A5 886 14 20 43.0 2.9 2.4 A6 779 13 18 39.0 2.9 2.4 B1 804 13 18 91.7 1.5 1.7 B2 914 14 19 82.8 2.1 2.6 B3 797 13 18 45.0 3.7 1.6 C1 737 12 18 95.4 1.7 2.5 C2 814 13 22 65.2 2.4 2.8 C3 708 12 17 96.6 1.9 2.7 D1 1083 11 15 48.0 2.7 3.0 D2 855 13 19 85.4 1.7 1.6 D3 1168 15 22 55.0 1.9 1.9 E1 904 14 19 82.6 2.1 2.5 E2 956 14 20 78.5 1.8 2.2 E3 668 12 17 90.0 3.3 3.4 F1 900 14 19 83.4 1.4 1.3 F2 954 14 20 78.4 2.1 2.1 F3 947 14 20 80.4 4.3 2.0 G1 1073 9 13 62.6 1.6 2.6 G2 817 13 19 39.0 5i2 4.5 H1 891 14 19 82.4 2.2 2.7 11 997 14 20 75.9 2.5 2.2 58/60 12 657 12 17 99.5 3.1 3.1 13 881 14 29 46.0 2.3 1.6 j1 959 14 20 78.9 2.0 2.7 j2 854 13 19 44.0 2.5 2.4 j3 953 14 20 39.0 4.8 4.3 K1 365 16 22 32.0 1.5 2.2 L1 853 12 17 85.9 1.5 2.2 M1 727 12 17 95.5 2.9 3.6 M2 936 14 20 38.0 4.1 0.9 N1 883 14 19 82.9 1.9 2.6 01 852 13 19 85.8 1.8 2.0 02 764 13 18 41.0 5j6 44 P1 873 13 19 84.1 2.2 3.3 P2 1051 9 10 26.1 6J 5.8 P3 1042 9 10 25.8 6.0 £ 5 P4 1113 6 7 23.1 1.8 2.2 Q1 818 13 19 88.9 2.3 2.7 02 485 12 13 55.0 2.5 2.2 Q3 568 10 11 51.2 1.5 1.7 04 657 11 12 34.0 3.1 3.1 R1 752 13 18 93.3 2.6 3.1 R2 1080 13 24 74.0 2.6 3.0 R3 1073 17 24 73.7 2.5 2.9 R4 1060 16 23 74.3 2.3 2.6 S1 868 13 19 85.8 1.6 2.1 S2 1020 16 22 77.0 2.0 2.4 S3 1050 16 23 74.9 1.9 2.3 S4 1020 15 21 75.2 1.5 1.8 T1 780 13 18 92.1 1.8 1.9 T2 720 12 17 39.0 52 46 T3 735 12 17 41.0 5j5 43 T4 986 15 21 36.0 5J 44 T5 998 16 22 35.0 6.2 5J T6 898 14 20 32.0 6J 46 T7 880 6 9 33.0 62 4Z to 1 b1 OCCURREDc1 FRACTUREd1 DURINGe'1 ALAMINATIONf1 THE HOTgi Table 5 (part 2) Steel type rC rL r30 r60 Note TO 1 0.79 0.84 1.10 1.10 COMPARATIVE EXAMPLE A2 0.74 0.79 1.06 1.04 COMPARATIVE EXAMPLE A3 0.74 0.79 0.97 0.98 COMPARATIVE EXAMPLE 59/60 Α4 0J8 0J53 121 131 COMPARATIVE EXAMPLE Α5 0.74 0.79 0.97 0.98 COMPARATIVE EXAMPLE Α6 0.74 0.79 0.97 0.98 COMPARATIVE EXAMPLE Β1 0.71 0.76 1.03 1.02 EXAMPLE OF THIS IKNVENTION Β2 0.71 0.76 1.07 1.05 EXAMPLE OF THIS IKNVENTION Β3 0.54 0 £ 9 127 122 COMPARATIVE EXAMPLE C1 0.71 0.76 1.03 1.02 EXAMPLE OF THIS IKNVENTION C2 0.71 0.76 1.05 1.04 COMPARATIVE EXAMPLE C3 0 ^ 4 0J9 122 1.01 COMPARATIVE EXAMPLE D1 0.71 0.76 1.03 1.02 COMPARATIVE EXAMPLE D2 0.71 0.76 1.05 1.04 EXAMPLE OF THIS IKNVENTION D3 0.71 0.76 1.05 1.04 COMPARATIVE EXAMPLE E1 0.72 0.77 1.07 1.06 EXAMPLE OF THIS IKNVENTION E2 0.72 0.77 1.09 1.07 EXAMPLE OF THIS IKNVENTION E3 0.72 0.77 1.06 1.04 COMPARATIVE EXAMPLE F1 0.72 0.77 1.07 1.05 EXAMPLE OF THIS IKNVENTION F2 0.72 0.77 1.08 1.07 EXAMPLE OF THIS IKNVENTION F3 0.85 0.90 1.44 1.35 EXAMPLE OF THIS IKNVENTION G1 0.71 0.76 1.03 1.02 COMPARATIVE EXAMPLE G20J4 123 118 COMPARATIVE EXAMPLE H1 0.70 0.75 1.02 1.02 EXAMPLE OF THIS IKNVENTION 11 0.72 0.77 1.07 1.05 EXAMPLE OF THIS IKNVENTION I2 0.74 0.79 1.11 1.09 EXAMPLE OF THIS IKNVENTION I3 0.74 0.79 1.09 1.09 COMPARATIVE EXAMPLE j1 0.72 0.77 1.07 1.06 EXAMPLE OF THIS IKNVENTION j2 0.74 0.79 1.09 1.09 COMPARATIVE EXAMPLE j3 0 £ 5 0J60 1.09 1.09 COMPARATIVE EXAMPLE K1 0.70 0.75 1.05 1.04 COMPARATIVE EXAMPLE L1 0.71 0.76 1.06 1.04 EXAMPLE OF THIS IKNVENTION M1 0.70 0.75 1.04 1.03 EXAMPLE OF THIS IKNVENTION M2 0.88 0.93 1.04 1.03 COMPARATIVE EXAMPLE N1 0.70 0.75 1.05 1.04 EXAMPLE OF THIS IKNVENTION 01 0.70 0.75 1.03 1.02 EXAMPLE OF THIS IKNVENTION 02 0J55 0.60 146 137 COMPARATIVE EXAMPLE P1 0.71 0.76 1.04 1.03 EXAMPLE OF THIS IKNVENTION P2 0.49 0J4 151 121 COMPARATIVE EXAMPLE P3 0 ^ 8 0/55 149 125 COMPARATIVE EXAMPLE P4 0.72 0.77 1.09 1.07 COMPARATIVE EXAMPLE Q1 0.71 0.76 1.04 1.03 EXAMPLE OF THIS IKNVENTION 02 0.72 0.77 1.07 1.05 COMPARATIVE EXAMPLE Q3 0.71 0.76 1.03 1.02 COMPARATIVE EXAMPLE 04 0.74 0.79 1.11 1.09 COMPARATIVE EXAMPLE R1 0.71 0.76 1.04 1.03 EXAMPLE OF THIS IKNVENTION R2 0.69 0.74 1.03 1.04 EXAMPLE OF THIS IKNVENTION R3 0.77 0.82 1.02 1.02 EXAMPLE OF THIS IKNVENTION R4 0.72 0.77 1.04 1.03 EXAMPLE OF THIS IKNVENTION S1 0.71 0.76 1.05 1.04 EXAMPLE OF THIS IKNVENTION 60/60 S2 0.72 0.77 1.05 1.03 EXAMPLE OF THIS IKNVENTION S3 0.71 -0.76 1.02 1.03 EXAMPLE OF THIS IKNVENTION S4 0.78 0.83 1.08 1.04 EXAMPLE OF THIS IKNVENTION T1 0.71 0.76 1.07 1.05 EXAMPLE OF THIS IKNVENTION T2 0 £ 2 0 £ 7 147 139 COMPARATIVE EXAMPLE T3 0 £ 3 OJ58 145 137 COMPARATIVE EXAMPLE T4 0 ^ 5 0J0 144 140 COMPARATIVE EXAMPLE T5 0 ^ 8 0 ^ 3 157 142 COMPARATIVE EXAMPLE T6 0 ^ 5 0J0 162 141 COMPARATIVE EXAMPLE T7 0 £ 7 0jB2 159 144 COMPARATIVE EXAMPLE to 1 COMPARATIVE EXAMPLE b1 COMPARATIVE EXAMPLE c1 COMPARATIVE EXAMPLE d1 COMPARATIVE EXAMPLE e'1 COMPARATIVE EXAMPLE f1 COMPARATIVE EXAMPLE _ COMPARATIVE EXAMPLE Industrial Applicability As previously described, according to the present invention, it is possible to provide a high-strength cold-rolled steel sheet that does not have a large anisotropy, even when Nb, Ti and / or similar are added and has excellent uniform elongation and ability to bore expansion. Thus, the present invention is an invention having high industrial applicability. Explanation of codes continuous hot rolling line roughing laminator finishing laminator hot rolled steel plate exit table rolling chair cooling nozzle between chairs cooling nozzle 11
权利要求:
Claims (15) [1] 1. High strength cold rolled steel sheet having excellent uniform elongation and hole expansion capacity, characterized by the fact that it consists of: in mass%, C: 0.01 to 0.4%; Si: 0.001 to 2.5%; Mn: 0.001 to 4.0%; P: 0.001 to 0.15%; S: 0.0005 to 0.03%; Al: 0.001 to 2.0%; N: 0.0005 to 0.01%; and O: 0.0005 to 0.01%; in which Si + Al is limited to less than 1.0%, and optionally, one type or two or more types between, in mass%, Ti: 0.001 to 0.2%, Nb: 0.001 to 0.2%, B: 0.0001 to 0.005%, Mg: 0.0001 to 0.01%, Rem: 0.0001 to 0.1%, Ca: 0.0001 to 0.01%, Mo: 0.001 to 1.0%, Cr: 0.001 to 2.0%, V: 0.001 to 1.0%, Ni: 0.001 to 2.0%, Cu: 0.001 to 2.0%, Zr: 0.0001 to 0.2%, W: 0.001 to 1.0%, As: 0.0001 to 0.5%, Co: 0.0001 to 1.0%, Sn: 0.0001 to 0.2%, Petition 870180145419, of 10/29/2018, p. 10/20 [2] 2/7 Pb: 0.001 to 0.1%, Y: 0.001 to 0.10%, and Hf: 0.001 to 0.10%, and the balance being composed of iron and the inevitable impurities, 5 where in a central portion of the plate thickness being a range of 5/8 to 3/8 in the plate thickness from the surface of the steel plate, the average value of pole densities of the orientation group {100} <011> to {223} <110> represented by the respective crystal orientations of 10 {100} <011>, {116} <110 >, {114} <110>, {113} <110>, {112} <110>, {335} <110>, and {223} <110> is 5.0 or less, and the pole density of the orientation crystal {332} <113> is 4.0 or less, the metal structure contains 5 to 80% ferrite, 5 to 80% bainite, and 1% or less martensite in terms of area ratio and total mar15 tensite, perlite, and retained austenite is 5% or less, and an r (rC) value in a direction perpendicular to the rolling direction is 0.70 or more, and an r (r30) value in a direction 30 ° from lamination direction is 1.10 or less. 2. High strength cold-rolled steel sheet having excellent uniform elongation and hole expansion capacity, according to claim 1, characterized by the fact that the r (rL) value in the rolling direction is 0.70 or more, and the r (r60) value in a 60 ° direction from the rolling direction is 1.10 or less. [3] 3. High strength cold rolled steel sheet having excellent uniform elongation and hole expansion capacity, according to claim 1, characterized by the fact that, in the metallic structure, the average volume of the crystal grains is 7 μιτι or less, and the average value of a ratio of the crystal grains, the length dL in the lamination direction to the length dt in the direction of the plate thickness: dL / dt 3.0 or me30 nos. [4] 4. High strength cold rolled steel sheet having excellent uniform elongation and hole expansion capacity, according Petition 870180145419, of 10/29/2018, p. 11/20 3/7 with claim 1, characterized by the fact that, on the surface, hot dip galvanizing is carried out. [5] 5. High strength cold rolled steel sheet has excellent uniform elongation and hole expansion capacity, according to claim 4, characterized by the fact that, after hot dip galvanizing, a bonding treatment is carried out at 450 to 600 ° C. [6] 6. Method of producing a high-strength cold-rolled steel sheet having excellent uniform elongation and bore expansion capacity, as defined in any one of claims 1 to 5, characterized by the fact that it comprises: in a steel block consisting of: in% in assa, C: 0.01 to 0.4%; Si: 0.001 to 2.5%; Mn: 0.001 to 4.0%; P: 0.001 to 0.15%; S: 0.0005 to 0.03%; Al: 0.001 to 2.0%; N: 0.0005 to 0.01%; and O: 0.0005 to 0.01%; in which Si + Al is limited to less than 1.0%, and optionally, one type or two or more types between, in mass%, Ti: 0.001 to 0.2%, Nb: 0.001 to 0.2%, B: 0.0001 to 0.005%, Mg: 0.0001 to 0.01%, Rem: 0.0001 to 0.1%, Ca: 0.0001 to 0.01%, Mo: 0.001 to 1.0%, Cr: 0.001 to 2.0%, V: 0.001 to 1.0%, Petition 870180145419, of 10/29/2018, p. 12/20 4/7 Ni: 0.001 to 2.0%, Cu: 0.001 to 2.0%, Zr: 0.0001 to 0.2%, W: 0.001 to 1.0%, As: 0.0001 to 0.5%, Co: 0.0001 to 1.0%, Sn: 0.0001 to 0.2%, Pb: 0.001 to 0.1%, Y: 0.001 to 0.10%, and Hf: 0.001 to 0.10%, and the balance being composed of iron and the inevitable impurities, perform a first hot lamination in which lamination at a reduction rate of 40% or more is performed once or more in a range temperatures of not less than 1000 ° C or more than 1200 ° C; adjust the austenite grain diameter to 200 pm or less by a first hot rolling; perform a second hot lamination in which lamination at a rate of reduction of 30% or more is performed in a pass at least once in a temperature region of not less than a temperature T1 + 30 ° C or more than T1 + 200 ° C determined by Expression (1) below; adjust the total reduction ratio in the second hot rolling to 50% or more; perform the final reduction at a reduction rate of 30% or more on the second hot rolling and then start the primary pre-cold rolling in such a way that the waiting time t seconds satisfies Expression (2) below; adjust the average cooling rate in the primary cooling to 50 * C / s or more and perform the primary cooling so that the temperature change is in a range of not less than 40 * C or more than 140O; Petition 870180145419, of 10/29/2018, p. 13/20 5/7 perform cold rolling at a reduction rate of not less than 30% or more than 70%; perform the heating up to a temperature range of 700 to 900 ° C and perform the retention for no less than 1 second or more than 1000 seconds; perform primary cooling after cold rolling to a temperature range of 580 to 750 * C at an average cooling rate of 12 * C / s or less; perform secondary cooling after cold rolling to a temperature range of 350 to 500 ° C at an average cooling rate of 4 to 300 ° C / s; and perform an aging heat treatment in which retention is performed for not less than t2 seconds satisfying Expression (4) below for not more than 400 seconds in a temperature region of not less than 350 ° C or more than 500 ° C : T1 (° C) = 850 + 10 x (C + N) x Mn + 350 x Nb + 250 x Ti + 40 x B + 10xCr + 100xMo + 100 xV ··· (1) here, C, N, Mn, Nb , Ti, B, Cr, Mo, and V each represent the content of the elements (% by mass): t 2.5 x t1 ··· (2) here, t1 is obtained by Expression (3) below: t1 = 0.001 x ((Tf-T1) x P1 / 100) 2 -0.109 x ((Tf-T1) x P1 / 100) + 3.1 ··· (3) here, in Expression (3) above, Tf represents the temperature of the steel block obtained after the final reduction at a reduction ratio of 30% or more, and P1 represents the reduction ratio of the final reduction to 30% or more: Yog (t2) = 0.0002 (T2 - 425) 2 + 1.18 ... (4) here, T2 represents an aging treatment temperature, and the maximum value of t2 is set to 400. [7] 7. Production method of high-strength cold-rolled steel sheet having excellent uniform elongation and hole expansion capacity, according to claim 6, characterized by the fact that Petition 870180145419, of 10/29/2018, p. 14/20 6/7 also includes: after performing primary cold pre-lamination cooling, perform secondary cold pre-lamination cooling to a cooling stop temperature of 600 ° C or less at an average cooling rate of 10 to 300 * C / s before to perform the first cold mining, and to laminate at 600 * 0 or less to obtain a cold rolled steel sheet. [8] 8. Production method of high-strength cold-rolled steel sheet having excellent uniform elongation and bore expansion capacity, according to claim 6, characterized by the fact that the total reduction ratio in a temperature range of less that T1 + 30 ° C is 30% or less. [9] 9. Production method of high strength cold rolled steel sheet having excellent uniform elongation and hole expansion capacity, according to claim 6, characterized by the fact that the waiting time t seconds also satisfies the Expression (2a ) below: t <t1 - (2a) [10] 10. Production method of high strength cold rolled steel sheet having excellent uniform elongation and hole expansion capacity, according to claim 6, characterized by the fact that the waiting time t seconds also satisfies the Expression (2b ) below: t1 t t1 x 2.5 - (2b) [11] 11. Production method of high strength cold rolled steel sheet having excellent uniform elongation and hole expansion capacity, according to claim 6, characterized by the fact that the primary cooling after cold rolling starts between laminating chairs. [12] 12. Production method of high-strength cold-rolled steel sheet having excellent uniform elongation and hole expansion capacity, according to claim 6, characterized by the fact that when heating is carried out to a temperature region of 700 at 900 ° C after cold rolling, an average heating rate Petition 870180145419, of 10/29/2018, p. 15/20 7/7 ment of not less than ambient temperature or greater than 650Ό is set to HR1 (* C / s) expressed by Expression (5) below, and the average heating rate of more than 650Ό up to 70 0 * C at 900 * 0 is adjusted to HR2 (* C / s) expressed by Expression (6) below: 5 HR1 0.3 ... (5) HR2 0.5 x HR1 ... (6) [13] 13. Production method of high-strength cold-rolled steel sheet having excellent uniform elongation and hole expansion capacity, according to claim 6, characterized by the fact that 10 further comprises: perform hot dip galvanizing on the surface. [14] 14. Production method of high-strength cold-rolled steel sheet having excellent uniform elongation and hole expansion capacity, according to claim 13, characterized by the fact that [15] 15 which further comprises: carry out a bonding treatment at 450 to 600 ° C after the execution of hot dip galvanizing.
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法律状态:
2018-07-31| B07A| Technical examination (opinion): publication of technical examination (opinion)| 2019-02-05| B09A| Decision: intention to grant| 2019-03-19| B16A| Patent or certificate of addition of invention granted|Free format text: PRAZO DE VALIDADE: 20 (VINTE) ANOS CONTADOS A PARTIR DE 19/04/2012, OBSERVADAS AS CONDICOES LEGAIS. | 2019-11-12| B25D| Requested change of name of applicant approved|Owner name: NIPPON STEEL CORPORATION (JP) |
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申请号 | 申请日 | 专利标题 JP2011-095254|2011-04-21| JP2011095254|2011-04-21| PCT/JP2012/060634|WO2012144567A1|2011-04-21|2012-04-19|High-strength cold-rolled steel sheet with highly even stretchabilty and excellent hole expansibility, and process for producing same| 相关专利
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