[Designation of Document] SPECIFICATION [Title of the Invention] HOT-ROLLED STEEL SHEET AND METHOD OF PRODUCING THE SAME [Technical Field] [0001] The present invention relates to a precipitation strengthening type highstrength hot-rolled steel sheet having superior isotropic workability and a method of -producing the same. —^:^- - — Priority is claimed on Japanese Patent Application No. 2011-089520, filed April 13, 2011, the content of which is incorporated herein by reference. [Background Art] [0002] Recently, in order to reduce the weight of various components for the improvement of fuel efficiency of a vehicle, an application of a reduction in thickness by the strengthening of a steel sheet such as an iron alloy; and a light metal such as an Al alloy is progressed. However, compared to a heavy metal such as steel, a light metal such as an Al alloy has an advantage of high specific strength and a disadvantage of iaving a significantly Jiigher £05t. JCherefore, ihe application is .limited to specific uses. Therefore, in order to reduce the weight of various components at a lower cost over a wider range, a reduction in thickness with the strengthening of a steel sheet is necessary. [0003] Generally, the strengthening of a steel sheet brings about a deterioration in material properties such as formability (workability). Therefore, in the development of a high-strength steel sheet, it is important to increase strength without impairing 1 material properties. In particular, for a steel sheet which is used for vehicle components such as inner plate components, structural components, and suspension components, bendability, stretch flangeability, burring workability, ductility, fatigue resistance, impact resistance (toughness), corrosion resistance, and the like are required according to its use. Therefore, it is important to acheive a high level of balance between these material properties and high strength. [0004] In particular, among automobile components, components which are processed using a sheet material as a base metal and function as a rotator, such as, a drum or a carrier constituting an automatic transmission are important components for transmitting engine output to axle shafts. In order to reduce friction and the like, circularity as a shape and homogeneity in thickness in a circumferential direction are required for these components. Furthermore, since a forming processes such as burring, drawing, ironing, and stretching are used for these components, ultimate deformability which is represented by local elongation is significantly important. [0005] In a steel sheet used for these components, it is preferable that impact -resistance (loiighness), widchis Ihe^jxopertyjof^xompoiient to be difficult to fracture when being attached to a vehicle after foiTnation and then being impacted by collision or the like, is improved. In particular, when use in a cold region is taken into consideration, in order to secure impact resistance at a low temperature, it is preferable that the toughness at a low temperature (low-temperature toughness) is improved. This toughness is defined by vTrs (Charpy fracture appearance transition temperature). Therefore, it is important to increase the above-described impact resistance of a steel material. - 2 [0006] That is, in a thin steel sheet for components which require homogeneity in thickness and include the above-described components, in addition to superior workability, it is required that both plastic isotropy and toughness are simultaneously improved. [0007] Techniques for improving both high strength and various material properties such as formability are as follows." For example, Patent Document 1 discloses a method of producing a steel sheet in which a steel structure contains 90% or greater of ferrite and the balance consisting of bainite; and thus high strength, ductility, and hole extensibility are simultaneously improved. However, regarding a steel sheet which is produced according to the technique disclosed in Patent Document 1, Patent Document 1 does not disclose plastic isotropy at all. Therefore, for example, assuming that this steel sheet is applied to a component, such as a gear wheel, which requires circularity and homogeneity of thickness in a circumferential direction, there is a concern about power reduction by inappropriate vibration or friction loss due to a misaligned component. [ODDS] In addition. Patent Documents 2 and 3 disclose a high-tensile hot-rolled steel sheet having high strength and superior stretch flangeability in which Mo is added for refining precipitates. However, in a steel sheet which is produced according to the . techniques disclosed in Patent Documents 2 and 3, since it is necessary that 0.07% or greater of Mo, which is an expensive alloy element, is added, there is a problem of high production cost. Furthermore, the techniques disclosed in Patent Documents 2 and 3 do not disclose plastic isotropy. Therefore, assuming that this steel sheet is 3 - applied to a component which requires circularity and homogeneity in thickness in a circumferential direction, there is a concern about power reduction by inappropriate vibration or friction loss due to a misaligned component. [0009] Meanwhile, regarding the improvement of plastic isotropy of a steel sheet, that is, the reduction of plastic anisotropy, for example. Patent Document 4 discloses a technique in which endless rolling and lubrication rolling are combined co control an austenite texture of a surface shear layer and thusto reduce the in-plane anisotropy of rvalues (Lankford values). However, in order to perform such lubrication rolling having a low friction coefficient over the entire coil, endless rolling is necessary for preventing engagement failure caused by a slip between a roll caliber tool and a rolled material during rolling. Therefore, in order to apply this technique, there is a large burden because facilities such as a rough bar joining apparatus or a high-speed crop shear are required. [0010] In addition, for example, Patent Document 5 discloses a technique in which a combination of Zr, Ti, and Mo is added; and finish rolling is finished at a high -temperaturejDf 950°C ijr Jugher to reduce the .anisotrojvy of r values at a^trength of 780 MPa grade or higher and thus to improve both stretch flangeability and deep drawability. However, since it is necessary that 0.1% or greater of Mo which is an expensive alloy element, is added, there is a problem of high production cost. [0011] Furthermore, although techniques of improving the toughness of a steel sheet have been progressed in the related art, a hot-rolled steel sheet having high strength and superior plastic isotropy, hole expansibility, and toughness is not disclosed in 4 - Patent Documents 1 to 5. [Prior Art Document] [Patent Document] [0012] [Patent Document 1] Japanese Unexamined Patent Application, First Publication No. H06-293910 [Patent Document 2] Japanese Unexamined Patent Application, First -Publication NO.-2002-322540- -- - —- : [Patent Document 3] Japanese Unexamined Patent Application, First Publication No. 2002-322541 [Patent Document 4] Japanese Unexamined Patent Application, First Publication No. HI0-183255 [Patent Document 5] Japanese Unexamined Patent Application, First Publication No. 2006-124789 [Disclosure of the Invention] [Problem that the Invention is to solve] [0013] Xhcpresentinvention Jias beenjnadein consideration of ihe .above-jdescribed problems. That is, an object thereof is to provide a precipitation strengthening type high-strength hot-rolled steel sheet which has a high tensile strength of 540 MPa grade or higher, can be applied to components requiring workability such as hole expansibility, strict homogeneity in thickness and circularity after processing, and toughness, and has superior isotropic workability (isotropy); and a method capable of stably producing the steel sheet at a low cost. [Means for Solving the Problems] - 5 [0014] In order to solve the above-described problems and to achieve the object, the present invention adopts the following measures. [0015] (1) That is, according to an aspect of the present invention, there is provided a hot-rolled steel sheet including, by mass %, C: a content [C] of 0.02%) to 0.07%), Si: a content [Si] of 0.001% to 2.5%, Mn: a content [Mn] of 0.01% to 4%, Al: a content [Al] of 0.001% to 2%, Ti: a content [Ti] of 0.ai5% to 0.2%, P: a limited content [P] of 0.15%) or less, S: a limited content [S] of 0.03%) or less, N: a limited content [N] of 0.01%) or less, and the balance consisting of Fe and unavoidable impurities, in which the contents [Ti], [N], [S], and [C] satisfy the following expressions (a) and (b); an average pole density of an orientation group {100}<011> to {223}<110>, which is represented by an arithmetic mean of pole densities of orientations {100}<011>, {116}<110>, {114}<110>, {112}<110>, and {223}<110> is 1.0 to 4.0 and apole density of a crystal orientation {332}<113> is 1.0 to 4.8; in a thickness center portion which is a thickness range of 5/8 to 3/8 from the surface of the steel sheet,an average grain size in the thickness center portion is less than or equal to 10 jam and a grain size of a cementite precipitating in-.a^rainJbDjnndaryx)i"Jlie-Steel_sheet is less than or equal to 2 jam; and an average grain size of precipitates containing TiC in grains is less than or equal to 3 nm and a number density per unit area is greater than or equal to IxlO' grains/cm . 0%<([Ti]-[N]x48/14-[S]x48/32) ... (a) 0%<[C]-12/48x([Ti]-[N]x48/14-[S]x48/32)... (b) [0016] (2) In the hot-rolled steel sheet according to (1), the average pole density of the orientation group {100}<011> to {223}<110> may be less than or equal to 2.0 and the pole density of the crystal orientation {332}<113> may be less than or equal to 3.0. [0017] (3) In the hot-rolled steel sheet according to (1), the average grain size may be less than or equal to 7 |j,m. [0018] (4) The hot-rolled steel sheet according to any one of (1) to (3) may further include, by mass%rNb: a content [Nb] of 0.005% to 0.06%rin which the contents [Nb]; [Ti], [N], [S], and [C] satisfy the following expression (c). 0%<[C]-12/48x([Ti]+[Nb]x48/93-[N]x48/14-[S]x48/32) ... (c) [0019] (5) The hot-rolled steel sheet according to (4) may further include one or two or more selected from the group consisting of, by mass%, Cu: a content [Cu] of 0.02% to 1.2%, Ni: a content [Ni] of 0.01% to 0.6%, Mo: a content [Mo] of 0.01% to 1%, V: a content [V] of 0.01% to 0.2%, Cr: a content [Cr] of 0.01% to 2%, Mg: a content [Mg] of 0.0005% to 0.01%, Ca: a content [Ca] of 0.0005% to 0.01%, REM: a content [REM] of 0.0005% to 0.1%, and B: a content [B] of 0.0002% to 0.002%. [0020] (6) The hot-rolled steel sheet according to any one of (1) to (3) may further include one or two or more selected from the group consisting of, by mass%, Cu: a content [Cu] of 0.02% to 1.2%, Ni: a content [Ni] of 0.01% to 0.6%, Mo: a content [Mo] of 0.01% to 1%, V: a content [V] of 0.01% to 0.2%, Cr: a content [Cr] of 0.01% to 2%, Mg: a content [Mg] of 0.0005% to 0.01%, Ca: a content [Ca] of 0.0005% to 0.01%, REM: a content [REM] of 0.0005% to 0.1%, and B: a content [B] of 0.0002% to 0.002%. - 7 [0021] (7) According to another aspect of the present invention, there is provided a method of producing a hot-rolled steel sheet including: heating a steel ingot or a slab including, by mass%, C: a content [C] of 0.02% to 0.07%, Si: a content [Si] of 0.001% to 2.5%, Mn: a content [Mn] of 0.01% to 4%, Al: a content [Al] of 0.001% to 2%, Ti: a content [Ti] of 0.015% to 0.2%, P: a limited content [P] of 0.15% or less, S: a limited content [S] of 0.03% or less, N: a limited content [N] of O.OP/o or less, and the balance consisting of Fe and unavoidable impurities, in which the contents [Ti],[N], [S], and [C] satisfy the following expressions (a) and (b), at SRTmin°C, which is the temperature determined according to the following expression (d), to 1260°C; performing a first hot rolling in which reduction is performed once or more at a rolling reduction of 40% or higher in a temperature range of 1000°C to 1200°C; starting second hot rolling in a temperature range of 1000°C or higher within 150 seconds after the finish of the first hot rolling; performing a reduction in the second hot rolling at least once at a rolling reduction of 30%) or higher so as to obtain a total rolling reduction of 50%) or higher in a temperature range, when a temperature determined by components of the steel sheet according to the following expression (e) is represented by T1°C, (TR30)°Cio (Tl+200)°C;-performing-a thirdJiotJi)Jlingin^iolal-rolliiig reduction is lower than or equal to 30% in which a temperature range of a Ar3 transformation temperature to less than (T1+30)°C; finishing the hot rollings at the Ar3 transformation temperature or higher; performing a primary cooling under conditions of a cooling rate of 50°C/sec or higher, a temperature change of 40°C to 140°C, and a cooling end temperature of (T1+100)°C or lower such that, when a pass of a rolling reduction of 30% or higher in a temperature range of (T1+30)°C to (T1+200)°C defined as a large reduction pass, a waiting time t (second) from the finish of a final 8 pass of the large reduction pass to the start of cooling satisfies the following expression (f); performing a secondary cooling at a cooling rate of 15°C/sec or higher within 3 seconds from the finish of the primary cooling; and performing a coiling in a temperature range of 550°C to lower than 700°C. 0%<([Ti]-[N]x48/14-[S]x48/32) ... (a) 0%<[C]-12/48x([Ti]-[N]x48/14-[S]x48/32)... (b) SRTmin=7000/{2.75-log([Ti]x[C])}-273 ... (d) Tl=850+10x([€]+[N])x[Mn]+350x[Nb]+250x[Ti]+40x[B]+10x[er]+100x[Mo]+100x [V] ... (e) t<2.5xtl... (f) (wherein tl is represented by the following expression (g)) tl=0.001x((Tf-Tl)xPl/100)^-0.109x((Tf-Tl)xPl/100)+3.1 ... (g) (wherein Tf represents a temperature (°C) after a final reduction at a rolling reduction of 30% or higher, and PI represents the rolling reduction (%) during the final reduction at a rolling reduction of 30% or higher) [0022] (8) In the method of producing a hot-rolled steel sheet according to (7), the primary cooling may-be .performed,between jolling stands and thejsecondary cooling may be performed after passage through a final rolling stand. [0023] (9) In the method of producing a hot-rolled steel sheet according to (7) or (8), the waiting time t (second) may further satisfy the following expression (h). tl to {223}<110>^ndisotropy (1/ Ur | ). FIG. 2 is a diagram illustrating a relationship between a pole density of a crystal orientation {332}<113> and isotropy (1/1 Ar | ) . FIG. 3 is a flowchart illustrating a method of producing a hot-rolled steel sheet according to an embodiment of the present invention. [Embodiements of the Invention] [0031] Embodiments of the present invention will be described in detail. - n Hereinbelow, "mass%" relating to the component composition will be simply referred to as "%". [0032] In order to simultaneously improve isotropy and low-temperature toughness as well as workability, the present inventors have thoroughly investigated a precipitation strengthening type high-strength hot-rolled steel sheet which can be suitably, applied to components requiring workability such as hole expansibility, strict homogeneity in thickness and circularity after processing, and toughness at a low ^ temperature. As a result, the following new findings were obtained. "High strength" described in an embodiment of the present invention represents the tensile strength being greater than or equal to 540 MPa. [0033] In order to improve isotropy (to reduce anisotropy), it is effective to avoid the formation of a transformation texture from non-recrystallized austenite, which is the cause of anisotropy. To that end, it is necessary that recrystaUization of austenite after finish rolling is promoted. As measures for the promotion, it is effective to optimize a rolling pass schedule and increase a rolling temperature during finish rolling. [0034] Meanwhile, in order to improve toughness, refinement of a fracture surface unit of a brittle fracture surface, that is, refinement of a microstructure unit is effective. To that end, it is effective to increase a nucleation sites which act during y (austenite) -^ a (ferrite) transformation. Therefore, it is preferable that a grain boundary and a dislocation density of austenite capable of being the nucleation site are increased. [0035] In order to increase the grain boundary and the dislocation density, it is 12 - preferable that rolling is performed at a temperature which is as lower as possible and which is higher than or equal to an y->a transformation temperature. In other words, it is preferable that austenite is recrystallized to perform y to a transformation in a state where the austenite is kept as non-crystallized state and a non-recrystallization ratio is high. The reason is that recrystallized austenite grains are rapidly grown at a recrystallization temperature and thus are coarsened within an extremely short period of time; and the coarsened austenite grains are coarse in the a phase after the y-^a transformation: —^ — [0036] As described above, with normal hot rolling measures, preferable conditions are contradictory to each other. Therefore, it is considered that the simultaneous improvement of isotropy and toughness is difficult. On the other hand, the present inventors could satisfy a high level of balance between isotropy and toughness and have completed a novel hot rolling method. - [0037] The present inventors have obtained the following findings regarding the relationship between isotropy and texture. [0038] When a steel sheet is processed into a component requiring circularity and homogeneity in thickness in a circumferential direction, in order to obtain circularity and homogeneity which satisfy component properties as processed and without processes of trimming and cutting, it is required that an isotropy index 1/1 Ar | is greater than or equal to 3.5. As illustrated in FIG. 1, in order to control the isotropy index to be greater than or equal to 3.5, in a texture of a steel sheet, it is necessary that an average pole density of an orientation group {100}<011>to {223}<110>ina 13 thickness center portion which is a thickness range of 5/8 to 3/8 from the surface of the steel sheet be 1.0 to 4.0. When this average pole density is greater than 4.0, anisotropy is significantly increased. On the other hand, when the average pole density is less than 1.0, there is a concern about deterioration in hole expansibility due to deterioration in local deformability. In order to obtain a superior isotropy index of 6.0 or greater, it is more preferable that the average pole density of the orientation group {100}<011> to {223}<110> is 2.0. The orientation group {100}<011> to -{223} <110> is represented by an arithmetic mean of orientationsfl 00 }<011 >, " {116}<110>,{114}<110>, {112}<110>,and{223}<110>. Therefore, the average pole density of the orientation group {100}<011> to {223}<110> can be obtained by obtaining an arithmetic mean of pole densities of the orientations {100}<011>, {116}<110>, {114}<110>,{112}<110>, and{223}<110>. When the isotropy index is greater than or equal to 6.0, circularity and homogeneity which satisfy component properties can be obtained as processed even in consideration of variation in a coil. [0039] The above-described isotropy index was obtained by processing a steel sheet into a No. 5 test piece according to JIS Z 2201 and performing a test with a test method -according ioJIS-Z.224J-. When43lastic-strainj:atiDS (r y.alues)in aj-oJling direction, in a direction that forms 45° with respect to the rolling direction, and in a direction (transverse direction) that forms 90° with respect to the rolling direction are defined as rO, r45, and r90, respectively, Ar of the isotropy index 1/1 Ar | is defined as Ar=(r0- 2xr45+r90)/2. | Ar| refers to the absolute value of Ar. [0040] These pole densities of the orientations are measured using an EBSP (Electron Backscattering Diffraction Pattern) method or the like. Specifically, the pole densities 14 i are obtained from a three-dimensional texture calculated based on a pole figure {110} according to a vector method; or from a three-dimensional texture calculated using plural pole figures (preferably, three or more) of pole figures {110}, {100}, {211}, and {310} according to a series expanding method. [0041] Likewise, as illustrated in FIG. 2, in order to control the isotropy index to be greater than or equal to 3.5, in a texture of a steel sheet, it is necessary that a pole -density of acrystal orientation {332}<113> in athickness center portion which is a ^ thickness range of 5/8 to 3/8 from the surface of the steel sheet is 1.0 to 4.8. When this pole density is greater than 4.8, anisotropy is significantly increased. On the other hand, when the pole density is less than 1.0, there is a concern about deterioration in hole expansibility due to deterioration in local deformability. In order to obtain a superior isotropy index of 6.0 or greater, it is more preferable that the pole density of the crystal orientation {332}<113> is less than or equal to 3.0. When the isotropy index is greater than or equal to 6.0, circularity and homogeneity which satisfy component properties can be obtained as processed even in consideration of variation in a coil. The above-described average pole -density of Jhe orientation^group {100}<011> to {223}<110> and the pole density of the crystal orientation {332}<113> have a higher value when a ratio of grains intentionally oriented in a crystal orientation to those oriented in the other orientations is increased. In addition, the less the pole densities, the higher hole expansibility. [0042] ' The pole density is synonimous with X-ray random intensity ratio. The Xray random intensity ratio is the values obtained by measuring the X-ray intensities of 15 a reference sample not having accumulation in a specific orientation and a test sample with an X-ray diffraction method and the like under the same conditions; and dividing the X-ray intensity of the test sample by the X-ray intensity of the reference sample. The pole density can be measured by an X-ray diffraction, EBSP, or ECP (Electron Channeling Pattern) method. For example, the average pole density of the orientation group {100}<011> to {223}<110> is obtained by obtaining pole densities of orientations {100}<011>, {116}<110>, {114}<110>, {112}<110>, and {223}<110> from a three-dimensional texture (0DF) which iscalculated using a plurality of pole figures of pole figures {110}, {100}, {211}, and {310} measured by the abovedescribed methods according to a series expanding method; and obtaining an arithmetic mean of these pole densities. In the measurement, a sample which is provided for the X-ray diffraction, EBSP, or ECP method may be prepared in a manner that the thickness of the steel sheet is reduced to a predetermined thickness by mechanical polishing or the like; strain is removed by chemical polishing, electrolytic polishing, or the like; and the sample is adjusted so that an appropriate surface in a thickness range of 3/8 to 5/8 is obtained as the measurement surface. Regarding a transverse direction, it is preferable that the sample is obtained at a 1/4 position or a 6/4 position from an end portion of the-Steel-sheet. [0043] Of course, when the limitation relating to the above-described pole density is satisfied not only in the thickness center portion but in as many portions having a variety of thicknesses as possible, local deformability is further improved. However, since orientation accumulation in the thickness center portion in a thickness range of 3/8 to 5/8 from the surface of the steel sheet most greatly affects the anisotropy of a product, the material properties of approximately the entire steel sheet can be 16 represented by measuring the thickness center portion which is a thickness range of 5/8 to 3/8 from the surface of the steel sheet. Therefore, the average pole density of the orientation group {100}<011> to {223}<110>; and the pole density of the crystal orientation {332}<113>, in the thickness center portion which is a thickness range of 5/8 to 3/8 from the surface of the steel sheet are defined. [0044] Here, {hkl} represents that, when a sample is prepared according to the above-describedmethod, the normal direction of a sheet plane is parallel to {hkl}; and — the rolling direction is parallel to . Regarding the crystal orientations, generally, orientations perpendicular to a sheet plane are represented by [hkl] or {hkl}; and orientations parallel to the rolling direction are represented by (uvw) or . {hkl} and represent the collective terms for equivalent planes, and [hkl] and (uvw) represent individual crystal planes. That is, since a body-centered structure is targetted in the embodiment, for example, (111), (-111), (1-11), (11-1), (-1-11), (-11-1), (1-1-1), and (-1-1-1) planes are equivalent and cannot be distinguished from each other. In such a case, these orientations are collectively called {111}. Since ODF is also used for representing orientations of the other low-symmetry crystalline structures, individual orientations are generally represented by .[hkl](uvw). -However, in the embodiment, [hkl] (uvw) and {hkl} have the same definition. [0045] Next, the present inventors have investigated about toughness. [0046] As an average grain size is reduced, vTrs is lower, that is, toughness is improved. In a hot-rolled steel sheet according to an embodiment of the present invention, in order to lower vTrs in the thickness center portion than or equal to -20°C, 17 at which the steel plate can be used in a cold region, the average grain size in the thickness center portion is controlled to be less than or equal to 10 \xm. Furthermore, when vTrs is controlled to be lower than or equal to -60°C assuming use in a tough environment, it is more preferable that the average grain size in the thickness center portion is controlled to be less than or equal to 7 |am. [0047] Toughness is evaluated based on vTrs (Gharpy fracture appearance transition temperature) obtained in a V-notch Gharpy impact test.~In the V-notch Gharpy impact test, a test piece is prepared according to JIS Z 2202, and the details thereof follow JIS Z 2242. [0048] As described above, toughness is greatly affected by the average grain size in the thickness center portion of a microstructure. The average grain size in the thickness center portion is measured as follows. A micro sample is cut out from the vicinity of the center portion of the steel sheet in a through-thickness direction; and a grain size and a microstructure of the micro sample are measured using EBSP-OIM (registered trademark; Electron BackScatter Diffraction Pattern-Orientation Image Microscopy). The micro .sample is prepared by polishing with a colloidal silica abrasive for 30 minutes to 60 minutes and is measured according to EBSP under measurement conditions of a magnification of 400 times, an area of 160 |amx256 |am, and a measurement step of 0.5 (j,m. ' [0049] In the EBSP-OIM (registered trademark) method, a highly inclined sample is irradiated with electron beams in a scanning electron microscope (SEM); a Kikuchi pattern formed by backscattering is imaged by a high-sensitive camera; and an image 18 - thereof is processed by a computer, thereby measuring a crystal orientation of the irradiation point within a short period of time. [0050] In the EBSP method, a microstructure and a crystal orientation of a bulk sample surface can be quantitatively analyzed. In the EBSP method, an analysis area can be analyzed in a area capable of being observed with a SEM at a resolution of at least 20 nm although the resolution also depends on a resolution of the SEM. The analysis is performed by mapping an analysis area with several tens of thousands of-— points in a grid shape at regular intervals. In the case of a polycrystalline material, a crystal orientation distribution and a grain size in a sample can be observed. [0051] In the embodiment, among orientation differences of grains, 15°, which is a threshold of a high angle grain boundary generally recognized as a grain boundary, is defined as an orientation difference of a grain boundary for mapping; and grains are visualized based on a mapping image, thereby obtaining the average grain size. That is, "average grain size" refers to the value obtained by EBSP-OIM (registered trademark). {0052] As described above, the present inventors have clarified necessary requirements of a steel sheet for improving isotropy and toughness. [0053] The average grain size, which directly relates to toughness, is refined as a finish rolling end temperature is reduced. However, as controlling factors of isotropy, the average pole density of the orientation group {100}<011> to {223}<110>, which is represented by an arithmetic mean of pole densities of the orientations {100}<011>, - 19 {116}<110>,{114}<110>,{112}<110>, and {223}<110>; and the pole density of the crystal orientation {332}<113> , in the thickness center portion which is a thickness range of 5/8 to 3/8 from the surface of the steel sheet have the opposite relationship to the average grain size with respect to the finish rolling temperature. Therefore, techniques of simultaneously improving both isotropy and low-temperature toughness have not yet to be disclosed. [0054] In order to secure isotropy, the present inventors have investigated a hot rolling method and conditions for simultaneously improving isotropy and toughness by sufficiently recrystallizing austenite after finish rolling and by suppressing the growth of recrystallized grains to the minimum. [0055] In order to recrystallize austenite grains having a deformation texture due to rolling, it is preferable that finish rolling is performed in an optimum temperature range and at a total rolling reduction of 50% or higher. On the other hand, in order to refine a microstructure of a final product, it is preferable that cooling start within a predetermined time after the finish of finish rolling to suppress the growth of j-ecrystallized^ustenite-grains-to thejiiitiimum. [0056] Therefore, when a temperature represented by the above-described expression (e) is represented by Tl, hot rolling is performed at a total rolling reduction R in a temperature range of (TH-30)°C to (T1+200)°C. Then, it is investigated how each of the average pole density of the orientation group {100}<011> to {223}<110> in the thickness center portion which is a thickness range of 5/8 to 3/8 from the surface of the steel sheet; and the average grain size in the thickness center portion are changed - 20 depending on a relationship between a waiting time t from the finish of the hot rolling to the start of cooling and a cooling temperature change, in case that the cooling is performed under conditions of a cooling rate of 50°C/sec or higher, a temperature change of 40°C to 140°C, and a cooling end temperature of (T1+100)°C or lower. R is higher than or equal to 50%. The total rolling reduction (sum of rolling reductions) described in the embodiment has the same definition as a so-called cumulative rolling reduction; and refers to the percentage of, in the above-described rolling of each temperature range, a cumulative rolling amount (a difference between an entry-side —— thickness before an initial pass and an exit-side thickness after a final pass in the above-described rolling of each temperature range) to an entry-side thickness before an initial pass. [0057] As a result, when the waiting time t from the finish of the hot rolling, which is performed at the total rolling reduction R in the temperature range of (T1+30)°C to (T1+200)°C, to the start of the cooling, which is performed imder conditions of a cooling rate of 50°C/sec or higher, a temperature change of 40°C to 140°C, and a cooling end temperature of (T1+100)°C or lower, is within tlx2.5 seconds expressed -byJhejexpression^g). Tlie^vfirage.pole density of the i)xientatiDn-group {100}<011> to {223}<110> and the pole density of the crystal orientation {332}<113> is 1.0 to 4.8; in the thickness center portion which is a thickness range of 5/8 to 3/8 from the surface of the steel sheet is 1.0 to 4.0, and the average grain size in the thickness center portion is less than or equal to 10 |j,m. That is, it is assumed that isotropy and impact resistance, which are the object of the embodiment, are satisfied. [0058] The above-described results show that a range capable of improving both - 21 - isotropy and toughness, that is, a range of simultaneously realizing sufficient recrystallization and refinement of austenite can be achieved with a hot rolling method according to an embodiment of the present invention which will be described below in detail. Furthermore, it was found that, when the average grain size is less than or equal to 7 |j.m, the waiting time t is preferably shorter than t l . In addition, it was found that, when the average pole density of the orientation group {100}<011> to -{223}<110>-is less than or equal to 2.0, the waiting time t is preferably longer than or equal to tl. [0059] Based on the findings obtained by the above-described fundamental investigation, the present inventors have further thoroughly investigated a precipitation strengthening type high-strength hot-rolled steel sheet which can be suitably applied to components requiring workability such as hole expansibility, strict homogeneity in thickness and circularity after processing, and toughness at a low temperature. As a result, the present inventors conceived a hot-rolled steel sheet which satisfies the following conditions; and a method of producing the same. [0060] The reason for limiting chemical compositions of the hot-rolled steel sheet according to the embodiment will be described. [0061] C: a content [C] of 0.02% to 0.07% C segregates on a grain boundary and suppresses fracture surface cracking at an end surface which is formed by shearing and punching. In addition, C is bonded to Nb, Ti, or the like to form a precipitation, and contributes to strength improvement by 22 - precipitation strengthening. In addition, C produces iron carbides such as cementite (FesC) which cause cracking during hole expansion. [0062] When the content [C] of C is less than 0.02%, the strength improvement by precipitation strengthening and the effect of suppressing fracture surface cracking cannot be obtained. On the other hand, when the content [C] of C is greater than 0.07%, iron carbides such as cementite (FesC) which cause cracking dui'ing hole expansion are increased and thus, a hole expansion value and toughness deteriorate. Therefore, the content [C] of C is set to 0.02% to 0.07%. In consideration of strength improvement and ductility improvement, the content [C] is preferably 0.03% to 0.05%. [0063] " Si: a content [Si] of 0.001% to 2.5% Si contributes to an increase in the strength of a base metal. In addition, Si also functions as a deoxidizing agent. When 0.001% or greater of Si is added, the addition effects can be exhibited, and when the addition amount is greater than 2.5%, the effect of increasing the strength is saturated. Therefore, the content [Si] of Si is set to 0.001% to 2.5%. [0D64] From the viewpoints of strength improvement and hole expansibility, when the content [Si] of Si is greater than 0.1%, the precipitation of iron carbides such as cementite in a material structure is suppressed; and the precipitation of fine carbonate precipitates of Nb or Ti is promoted, and contributes to strength improvement and hole expansibility. On the other hand, when the content [Si] of Si is greater than 1%, the effect of suppressing the precipitation of iron carbides is saturated. Therefore, a preferable range of the content [Si] of Si is greater than 0.1% and less than or equal to 23 1%. [0065] Mn: a content [Mn] of 0.01% to 4% Mn contributes to strength improvement by solid solution strengthening and hardening strengthening. However, when the content [Mn] of Mn is less than 0.01%, the addition effects cannot be obtained. On the other hand, when the content [Mn] of Mn is greater than 4%, the addition effects are saturated. Therefore, the content [Mn] - of Mn is set to 0.01 % to 4%. ~ When elements other than Mn are not sufficiently -^ — added in order to suppress hot rolling cracking caused by S, it is preferable that Mn (mass%) is added such that the content [Mn] of Mn and the content [S] of S satisfy an expression of [Mn]/[S]>20. [0066] Along with an increase in content, Mn widens an austenite region temperature to a low temperature side, improves hardenability, and promotes the formation of a continuous cooling transformation structure which is superior in burring (burring workability). Since this effect is difficult to obtain with the addition of 1% or less of Mn, it is preferable that 1% or greater of Mn is added. On the other hand, when -greater.than3,0%x)f Jvlnis^dded, Ihe austenite xejion lemperalure is excessively lowered and thus, it is difficult to produce carbides of Nb or Ti which finely precipitate during ferrite transformation. Accordingly, when a continuous cooling transformation structure is formed, it is preferable that the content [Mn] of Mn is set to 1.0% to 3.0%. It is more preferable that the content [Mn] of Mn is set to 1.0% to 2.5%. [0067] P: a content [P] of greater than 0% and 0.15% or less - 24 - P is an impurity incorporated into molten iron, segregates on a grain boundary, and reduces toughness along with an increase in content. Therefore, it is preferable that the content [P] of P is less. When the content [P] of P is greater than 0.15%, there are adverse effects on workability and weldability. Therefore, the content [P] of P is limited to be less than or equal to 0.15%). In particular, the [P] of P is preferable less than or equal to 0.02%) in consideration of hole expansibility and weldability. Since it is difficult that the content of P becomes 0% because of operational problems, the content [P] of P does not include 0%). — - [0068] S: a content [S] of greater than 0%o and 0.03%) or less S is an impurity incorporated into molten iron, and causes cracking during hot rolling and produces A type inclusions impairing hole expansibility. Therefore, it is preferable that S be reduced to the minimum. However, since a content [S] of S of 0.03%o or less is in an allowable range, the content [S] of S is limited to be less than or equal to 0.03%). When higher hole expansibility is necessary, the content [S] of S is preferably less than or equal to 0.01%) and more preferably less than or equal to 0.005%). Since it is difficult that the content of S becomes 0%) because of operational problems, the content {S]x)f 5.doesnotinclude D%. [0069] N: a content [N] of greater than 0%o and 0.01 %o or less N forms a precipitate with Ti and Nb, and fixes C and reduces Ti and Nb effective for precipitation strengthening. As a result, a tensile strength is reduced. Therefore, it is preferable that N is reduced to the minimum, but a content [N] of S of 0.0 l%o or less is in an allowable range. However, nitrides of Ti or Nb which precipitate at a high temperature are easily coarsened, causes brittle fracture, and - 25 reduces low-temperature toughness. Therefore, in order to further improve toughness, the content [N] is preferably less than or equal to 0.006%. From the viewpoint of aging resistance, the content [N] is more preferably less than or equal to 0.005%. Since it is difficult that the content of N becomes 0% because of operational problems, the content [N] of S does not include 0%. [0070] Ah a content [Al] of 0.001% to 2% - 0.001% or greater of AHs added for molten steel deoxidation in a refining process of steel. However, a large amount of addition causes an increase in cost, the upper limit is set to 2%. When a large amount of Al is added, the amount of nonmetal inclusions increases and ductility and toughness deteriorate. Therefore, from the viewpoints of ductility and toughness, the content [Al] is preferably less than or equal to 0.06%. The content [Al] is more preferably less than or equal to 0.04%. [0071] Like Si, Al suppresses the precipitation of iron carbides such as cementite in a structure. In order to obtain this effect, it is preferable that 0.016% or greater of Al is added. Therefore, a content [Al] of Al is more preferably 0.016% to 0.04%. [0072] Ti: a content [Ti] of 0.015% to 0.2% Ti is one of the most important elements in the embodiment. During cooling after the finish of rolling, or during y-^a transformation after coiling, Ti precipitates finely and improves the strength by precipitation strengthening. In addition, Ti fixes C as a carbide to form TiC and thus suppresses the formation of cementite which is disadvantageous for burring workability. [0073] - 26 Furthermore, Ti precipitates as TiS when a billet is heated during a hot rolling process, suppresses the precipitation of MnS which forms a drawn inclusion, and reduces a total sum M of length of inclusion in a rolling direction. In order to obtain these addition effects, it is necessary that at least 0.015%o of Ti is added. It is preferable that 0.1 %> or greater of Ti be added. [0074] On the other hand, when greater than 0.2% of Ti is added, the addition effects are saturated, the effect of suppressing recrystallization is excessively exhibited,- and thus isotropy deteriorates. Therefore, the content [Ti] of Ti is set to 0.015% to 0.2%. The content [Ti] is more preferably 0.1 %> to 0.16%. [0075] 0%<[Ti]-[N]x48/14-[S]x48/32 ... (a) S and N form precipitates such as TiN or TiS with Ti in a higher temperature range than that of C. Therefore, in order to fix C, which is the base element of carbides such as cementite impairing hole expansibility, and to secure TiC contributing to precipitation strengthening, a relationship between the content [S] of S, a content [N] of N and the content [Ti] of Ti satisfies the expression (a). [007^] 0%<[C]-12/48x([Ti]-[N]x48/14-[S]x48/32)... (b) In the expression (b), [C], [Ti], [N], and [S] represent the content of C, the content of Ti, the content of N, and the content of S, respectively. When the hotrolled steel sheet according to the embodiment does not contain Nb, the right side of the expression (b) is the expression expressing the C content which can remain as a solid-soluted C after the precipitation of TiC. The right side of the expression (b) being less than or equal to 0%) represents the solid-soluted C being not present in a - 27 - grain boundary. When the solid-soluted C is not present, an intergranular strength deteriorates relative to an intragranular strength and thus, fracture surface cracking occurs. Therefore, the right side of the expression (b) is set to be greater than 0%. [0077] The upper limit of the expression (b) is not particularly limited, but is preferably less than or equal to 0.045% so as to make an appropriate amount of C remain and to control a cementite grain size to be less than or equal to 2 jim. When the cementite-grain size is less than or equaHo~l;6p.m7the upper limit of the expression (b) is more preferably less than or equal to 0.012%. On the other hand, when the upper limit of the expression (b) is greater than 0.045%, the cementite grain size increases and thus, there is a concern about deterioration in hole expansibility. Therefore, the upper limit of the expression (b) is preferably less than or equal to 0.045%. [0078] The above-described chemical elements are base components (base elements) of the steel according to the embodiment. A chemical composition in which the base components are controlled (contained or limited); and a balance thereof is iron and jonavoidableimpurities, is a basic compjasition-accorduag to the £mbodiment. However, in addition to this basic composition (instead of a part of Fe of the balance), the steel according to the embodiment may optionally further contain the following chemical elements (optional elements). Even when these optional elements are unavoidably (for example, the content of each optional element is less than the lower limit) incorporated into the steel, the effects of the embodiment do not deteriorate. [0079] Nb: a content [Nb] of 0.005% to 0.06% 28 During cooling after the finish of rolling, or after coiling, Nb precipitates finely and improves the strength by precipitation strengthening. In addition, Nb fixes C as a carbide and thus suppresses the formation of cementite which is disadvantageous for burring workability. [0080] Furthermore, Nb has a function of reducing the average grain size of the steel sheet and contributes to the improvement in low-temperature toughness. In order to obtain these addition effects, it is necessary that the content [Nb] of Nb is greater than or equal to 0.005%). It is preferable that the content [Nb] of Nb is greater than 0.01%. By setting the lower limit of the content [Nb] of Nb to 0.005%), the grain size can be reduced. As a result, there are no adverse effects on low-temperature toughness and the degree of freedom in rolling temperature setting can be improved. [0081] On the other hand, when the content [Nb] of Nb is greater than 0.06%, a temperature range of a non-recrystallization region during a hot rolling process is widened, a large amount of rolling texture in the non-recrystallized state remains after the finish of hot rolling, and thus isotropy deteriorates. Therefore, the content [Nb] of Nbis-set to 0.005% to 0.06%. The^ontent [NbJ ofNbisj)referably 0.01% to 0.02%. [0082] 0%<[C]-12/48x([Ti]+[Nb]x48/93-[N]x48/14-[S]x48/32) ... (c) When the hot-rolled steel sheet according to the embodiment contains Nb, it is necessary that{C], [Ti], [Nb] (content of Nb), [N}, aiid [S] satisfy the expression (c) instead of the expression (b). In the expression (c), an expression of [Nb]x48/93 is added into the parentheses of the expression (b). The technical implication of the expression (c) is the same as that of the expression (b). 29 [0083] Optionally, the hot-rolled steel sheet according to the embodiment may further contain one or two or more selected from the group consisting of Cu, Ni, Mo, V, Cr, Mg, Ca, REM (Rare Earth metal), and B. Hereinbelow, the reason for limiting the composition of each element will be described. [0084] Gu,Ni, Mo, V, and Gr are elements which improve the strength of the hotrolled steel sheet by precipitation strengthening or solid solution strengthening. [0085] When a content [Cu] of Cu is less than 0.02%); a content [Ni] of Ni is less than 0.01%; a content [Mo] of Mo is less than 0.01%; a content [V] of V is less than 0.01%; or a content [Cr] of Cr is less than 0.01%), the addition effect cannot be sufficiently obtained. On the other hand, when the content [Cu] of Cu is greater than 1.2%; the content [Ni] of Ni is greater than 0.6%); the content [Mo] of Mo is greater than 1%; the content [V] of V is greater than 0.2%); or the content [Cr] of Cr is greater than 2%, the addition effect is saturated and the economic efficiency deteriorates. [0086] Therefore, when one or two or more selected from the group consisting of Cu, Ni, Mo, V, and Cr are added, it is preferable that the content [Cu] of Cu is 0.02%) to 1.2%; the content [Ni] of Ni is 0.01% to 0.6%; the content [Mo] of Mo is 0.01% to 1%; the content [V] of V is 0.01% to 0.2%; and the content [Cr] of Cr is 0.01% to 2%. [0087] Mg, Ca, and REM (Rare Earth Metal) controls non-metal inclusions, which are origin of the fracture and deteriorates workability, and improves workability. When a 30 content [Mg] of Mg, a content [Ca] of Ca, or a content [REM] of REM is less than 0.0005%, the addition effect is not obtained. On the other hand, when the content [Mg] of Mg is greater than 0.01%, the content [Ca] of Ca is greater than 0.0 P/o, or the content [REM] of REM is greater than 0.1%), the addition effect is saturated and the economic eflficiency deteriorates. Therefore, it is preferable that the content [Mg] of Mg be 0.0005% to 0.01%; the content [Ca] of Ca be 0.0005% to 0.01%; and the content [REM] of REM be 0.0005% to 0.1%. [0088]— -— - -— B: a content [B] of 0.0002% to 0.002% Like C, B segregates ona grain boundary and is effective for increasing intergranular strength. That is, in addition to the solid-soluted C, the solid-soluted B segregates on a grain boundary and effectively acts for preventing fracture surface cracking. Even when C precipitates in grains as TiC, B can compensate for a reduction of C in a grain boundary by segregating the grain boundary. [0089] In order to compensate for the reduction of C in a grain boundary, it is necessary that at least 0.0002% of B be added. 0.0002% or greater of B and the solidsoluted £)^ery£ Jo 4)rev£nt iiracture^urfece xracking. When the -content [BJ of E is greater than 0.002%), like Nb, there is a concern that the recrystallization of austenite during hot rolling may be suppressed; the formation of a y^^a transformation texture from non-recrystallized austenite may be promoted; and isotropy may deteriorate. Therefore, the content [B] of B is set to 0.0002% to 0.002%. [0090] In addition, B improves hardenability and promotes the formation of a continuous cooling transformation structure as a micro structure which is preferable for - 3 1 - burring workability. In order to obtain the effect, the content [B] of B is preferably greater than or equal to 0.001%. On the other hand, in a cooling process after continuous casting, B causes slab cracking. From the point of view of the above, the content [B] of B is preferably less than or equal to 0.0015%. The content [B] of B is preferably 0.001 % to 0.0015%. [0091] The hot-rolled steel sheet according to the embodiment may further contain one or two or more,-for atotal content of 1% or less, selected from the group consisting of Zr, Sn, Co, Zn, and W within a range not impairing properties as unavoidable impurities. However, since there is a concern about defects during hot rolling, a content of Sn is preferably less than or equal to 0.05%. [0092] Next, metallurgical factors relating to a microstructure and the like of the hotrolled steel sheet according to the embodiment will be described. [0093] Grain-boundary cementite which affects hole expansibility will be described. Hole expansibility is affected by voids which cause cracking during punching or jshearing- ^oids-arfiibniied wJienaxfamfrntite^jhase, wliichjjrecipitatesin^parentphase grain boundary, has a given level of grain size relative to parent-phase grains; and an excess amount of stress concentrates on parent-phase grains in the vicinity of grain boundaries. [0094] When the cementite grain size is less than or equal to 2 |j,m, cementite grains are small relative to parent-phase grains and, dynamically, stress concentration does not occur. Therefore, the formation of voids is difficult. As a result, hole - 32 - expansibility and toughness are improved. Therefore, a grain-boundary cementite grain size (average grain size of cementite precipitating in a grain boundary) is controlled to be less than or equal to 2 ^m. The grain-boundary cementite grain size is preferably less than or equal to 1.6 |.im. In the embodiment, the average grain size of the grain-boimdary cementite precipitating in a grain boundary is obtained by preparing a transmission electron microscope sample at a 1/4-thick portion of a sample which is cut out from a 1/4-width or 3/4-width position ofa sample steel; and observing the transmission electron - microscope sample with a transmission electron microscope on which a field emission gun (FEG) having an accelerating voltage of 200 kV is mounted. By analyzing a diffraction pattern, it is confirmed that a precipitate observed in the grain boundary is cementite. In this investigation, the grain-boundary cementite grain size is defined as the average value of measured values obtained by measuring all the grain sizes of grain-boundary cementite observed in a single visual field. [0095] In general, the grain-boundary cementite grain size increases as a coiling temperature of the steel sheet increases. However, when the coiling temperature is iugherJhaQiar equal to a predeteimiaediempfirature, ihere i s ^ lendency that the^rainboundary cementite grain size becomes rapidly smaller. In particular, in a steel sheet containing at least one of Ti and Nb, the reduction of the grain-boundary cementite grain size is significant in the temperature range. In order to control the grainboundary cementite grain size to be less than or equal to 2 |j,m, it is necessary that the coiling temperature be higher than or equal to 550°C. The reason why the cementite grain size is reduced by an increase in coiling temperature is considered to be as follows. - 33 [0096] A precipitation temperature of cementite in the a phase (ferrite phase) has a nose region. The nose region can be explained as a balance between the nucleation which uses supersaturation of C in the a phase as a driving force and the grain growth of FesC in which a rate is controlled by diffusion of C and Fe. When the coiling temperature is lower than a temperature of the nose region, the supersaturation of C is great and the driving force of the nucleation is high. However, since the coiling temperature is low, diffusion is almost not performed. Therefore, the precipitation of cementite is suppressed both in grain boundaries and in grains. In addition, even if cementite precipitates, the grain size thereof is small. [0097] On the other hand, when the coiling temperature is higher than the temperature of the nose region, the solubility of C is increased and the driving force of the nucleation is reduced. However, a diffusion length is long. Therefore, the density is reduced, but the grain size of cementite is increased. [0098] When a carbide-forming element such as Ti or Nb is contained, a precipitation nose region of Ti or Nbin Jhe a phase is present on-aldgher temperature side Ihan Ihat of a precipitation nose region of cementite. Therefore, C is lost by the precipitation of carbides such as Ti or Nb and both the precipitation amount and grain size of cementite are reduced. [0099] Next, precipitation strengthening will be described. In the embodiment, Ti is mainly used as a precipitation strengthening element. The present inventors investigated a steel containing Ti about a relationship between the average grain size 34 and density of precipitates (hereinbelow, referred to as "TiC precipitates") containing TiC and a tensile strength. ^ [0100] . The grain size and density of the TiC precipitates are measured using a threedimensional atom probe method. An acicular sample is prepared from a sample of a measurement target by cutting and electropolishing and, optionally, by a combination of electropolishing and focused ion-beam milling. In the three-dimensional atom probe measurement, cumulative data canbe reconstructed to obtain an actual — distribution image of atoms in a real space. That is, a number density of the TiC precipitates is obtained from the volume of the three-dimensional distribution image of the TiC precipitates and the number of TiC precipitates. [0101] The grain size of the TiC precipitates can be obtained by calculating a diameter from the number of atoms constituting the observed TiC precipitates and a lattice constant of TiC, assuming that the shape of the precipitates is spherical. Arbitrarily, diameters of 30 or more TiC precipitates are measured and the average value thereof is obtained. [0102] A sample is processed into a No. 5 test piece according to JIS Z 2201 and a tensile test for a hot-rolled steel sheet is performed according to JIS Z 2241. [0103] If the chemical composition is constant, the average grain size and the density of the precipitates containing TiC have an almost inverse relationship with each other. In order to obtain a increase in tensile strength of 100 MPa by precipitation strengthening, it is necessary for the average grain size of the precipitates containing - 35 Tie to be smaller than or equal to 3 nm; and the density thereof be greater than or equal to 1 x 10 grains/cm . When the precipitates containing TiC are coarse, toughness may deteriorate or fracture surface cracking is likely to occur. [0104] A microstructure of a parent-phase of the hot-rolled steel sheet according to the embodiment is not particularly limited. However, when the tensile strength is greater than or equal to 780 MPa grade, a continuous cooling transformation structure "(Zw) is preferable. Even in this case, the microstructure of the parent-phase of the hot-rolled steel sheet may contain polygonal ferrite (PF) having a volume fraction of 20% or lower in order to simultaneously improve both workability and ductility represented by uniform elongation. Incidentally, the volume fraction of the microstructure refers to the area fraction in a measurement visual field. [0105] The continuous cooling transformation structure (Zw) described in the embodiment refers to, as disclosed in "Recent Study relating to Bainite structure and Transformation Action of Low-Carbon Steel -the Final Report of Bainite Research Committee-" (Bainite Research Committee, Society of Basic Research, The Iron and . 5teel Jnstitute .of Japan; 1994), a microstructure defined-as ^Iransformaticm-structure in the intermediate state between a microstructure containing polygonal ferrite and pearlite produced by a diffusion mechanism; and martensite produced by a shearing mechanism without diffusion. [0106] That is, as described as an optical microscopic structure in pp. 125 to 127 of the above-described reference document, the continuous cooling transformation structure (Zw) is defined as a microstructure which mainly contains Bainitic Ferrite 36 (a°B), Granular bainitic Ferrite (aB), and Quasi-polygonal Ferrite (aq) and may further contain a small amount of retained austenite (yr) and Martensite-Austenite (MA). [0107] Like polygonal ferrite (PF), an internal structure of aq does not appear by etching, but the shape thereof is acicular. Therefore, aq is clearly distinguished from PF. aq refers to a grain in which, when the peripheral length of a target grain is represented by Iq and the equivalent circle diameter thereof is represented by dq, the ratio (Iq/dq) thereof satisfies an expression of lq/dq>3.5. [0108] The continuous cooling transformation structure (Zw) of the hot-rolled steel sheet according to the embodiment is defined as a micro structure containing one or two or more selected from a°B, aB, aq, yr, and MA. A total amount of yr and/or MA is less than or equal to 3%. [0109] The structure can be determined by etching using a nital reagent and observation using an optical microscope. However, there is a case where the continuous cooling Iransformationjslructure ^Ziw) jnay be difficult -to determine hy etching using a nital reagent and observation using an optical microscope. In this case, EBSP-OIM (registered trademark) is used for determination. For example, ferrite, bainite, and martensite which have a bcc structure can be identified using a KAM (Kernel Average Misorientation) method equipped with EBSP-OIM (registered trademark). In the KAM method, a calculation is performed for each pixel in which orientation differences between pixels are averaged using, among measurement data, a first approximation of six adjacent pixels of pixels of a regular hexagon, a second 37 - approximation of 12 pixels thereof which is further outside, or a third approximation of 18 pixels thereof which is further outside; and the average value is set to a center pixel value. By performing this calculation so as not to exceed a grain boundary, a map representing orientation changes in grains can be created. This map shows the strain distribution based on local orientation changes in grains. Furthermore, a condition for calculating orientation differences between adjacent pixels in EBSP-OIM (registered trademark) is set to the third approximation and these orientation differences are set to be less than or equal to 5°."In the abovedescribed third approximation of orientation differences, when the calculated value is greater than 1°, the pixel is defined as the continuous cooling transformation structure (Zw); and when the calculated value is less than or equal to 1°, the pixel is defined as ferrite. The reason is as follows: since polygonal pro-eutecitoid ferrite transformed at a high temperature is produced by diffusion transformation, a dislocation density is low, a strain in grains is small, and differences between crystal orientations in grains are small; and as a result of various investigations which have been performed by the present inventors, it was found that the ferrite volume fraction obtained by observation using an optical microscope approximately matched with the area fraction obtained by the third approximationx)fjarientatioiijdifference5 of 1° inlhe JCAM jnethod. [0110] In the EBSP-OIM (registered trademark) method, a highly inclined sample is irradiated with electron beams in a scanning electron microscope (SEM); and a Kikuchi pattern formed by backscattering is imaged by a high-sensitive camera. Then, an image thereof is processed by a computer, and thereby a crystal orientation of the irradiation point can be measured within a short period of time. [0111] 38 In the EBSP method, a microstructure and a crystal orientation of a bulk sample surface can be quantitatively analyzed. An analysis area can be analyzed in an area capable of being observed with a SEM at a resolution of at least 20 nm although the resolution also depends on the resolution of the SEM. [0112] The analysis using the EBSP-OIM (registered trademark) method is performed by mapping an analysis area with several tens of thousands of points in a grid shape at regular intervalsr In the case of a polycrystalline material,-a crystal orientation distribution and a grain size in a sample can be observed. In the hot-rolled steel sheet according to the embodiment, an orientation difference of each packet is set to 15° for mapping; and a structure which can be determined based on a mapping image may be defined as the continuous cooling transformation structure (Zw) for convenience. [0113] Next, the reason for limiting conditions for a method of producing a hot-rolled steel sheet according to an embodiment of the present invention (hereinbelow, referred to as "production method according to the embodiment") will be described. [0114] Inlhe production xnethod according to the embodiment, a method of producing a steel piece which is perfomied before a hot rolling process is not particularly limited. That is, in the method of producing a steel piece, a process of preparing an ingot is performed using a blast furnace, a converter furnace, an electric furnace, or the like; various kinds of secondary smelting processes may be performed to adjust components and thus to obtain the desired chemical composition; and a casting process may be performed with a method such as normal continuous casting, ingot casting, or thin slab casting. - 39 - [0115] When a slab is obtained by continuous casting, the high-temperature slab may be directly fed into a hot rolling mill; or may be cooled to room temperature once and heated again in a heating furnace for hot rolling. As a raw material, scrap may be used. [0116] The slab obtained according to the above-described production method is heated in a slab heating process before the hot rollingprocess.—At this time, heating is^ performed in a heating furnace at a temperature higher than or equal to a minimum slab reheating temperature SRTmin°C calculated according to the following expression (d). SRTmin=7000/{2.75-log([Ti]x[C])}-273 . . . ( d) [0117] the expression (d) is the expression to obtain the solution temperature of a carbonitride of Ti from a product of the content [Ti] (%) of Ti and the content [C] (%)., of C. Conditions for obtaining a composite precipitate of TiNbCN are determined according to the content of Ti. That is, when the content of Ti is small, TiN alone jdoesjiotpxecipitate. [0118] When the slab heating temperature is higher than or equal to the temperature SRTmin°C which satisfies the expression (d), the tensile strength of the steel sheet is significantly improved. The reason is considered to be as follows. [0119] In order to obtain the desired tensile strength, it is effective to use precipitation strengthening with Ti and/or Nb. In a slab before heating, coarse - 40 - t carbonitrides such as TiN, NbC, TiC, and NbTi (CN) precipitate. In order to effectively obtain the effect of precipitation strengthening withNb and/or Ti, it is necessary that these coarse carbonitrides are temporarily and sufficiently dissolved in a base metal during the slab heating process. [0120] Most of carbonitrides of Nb and/or Ti are dissolved at a solution temperature of Ti. The present inventors found that, in order to obtain the desired tensile strength, nt is necessary that a slab is heated to the-solution temperature SRTmin°C of Ti in the slab heating process. [0121] TiN, Tic, and NbN-NbC have literature values for solubility product. In particular, since TiN precipitates at a high temperature, it is assumed that TiN is difficult to dissolve by low-temperature heating according to the embodiment. However, the present inventors found that, although TiN was not completely dissolved, most of TiC was substantially dissolved with only the solutionizing of thereof. [0122] When a precipitate, which is considered to be a composite precipitate of IiNb(.CN),is -observed Ihrough replica-observation x)f a Jxansmission electron microscope, concentrations of Ti, Nb, C, and N are changed in a center portion in which precipitation occurs at a high temperature and a shell portion in which precipitation occurs at a relatively low temperature. That is, the concentrations of Ti and N are high in the center portion, whereas the concentrations of Nb and C are high in the shell portion. [0123] The reason is as follows: TiNb(CN) is a MC type precipitate having a NaCl - 41 - structure, and in TiC, Ti is coordinated to an M site and C is coordinated to a C site; however, depending on temperatures, Ti may be substituted with Nb and C may be substituted with N. [0124] The same shall be applied to TiN. Even at a temperature at which TiC is completely dissolved, TiN contains Ti at a site fraction of 10% to 30%. Therefore, technically, TiN is completely dissolved at a temperature which is higher than or equal - to a temperature at which TiN is completely dissolved.- However, in a component system having a relatively small amount of Ti, substantially, the solution temperature may be set to the lower limit of the dissolution temperature of TiC precipitates. [0125] When the heating temperature is lower than SRTmin°C, carbonitrides of Nb and/or Ti are not sufficiently dissolved in a base metal. In this case, during cooling after the finish of rolling, or after coiling, precipitation strengthening in which the effect of increasing strength is obtained by Nb and/or Ti finely precipitating as carbides cannot be used. Therefore, the heating temperature in the slab heating process is set to be higher than or equal to SRTmin°C calculated according to the expression (d). [0126] When the heating temperature in the slab heating process is higher than 1260°, yield deteriorates due to scale-off". Therefore, the heating temperature is set to be lower than or equal to 1260°C. Therefore, the heating temperature in the slab heating process is set to the minimum slab reheating temperature SRTmin°C, calculated according to the expression (d), to 1260°C. When the heating temperature is lower than 1150°C, the operation efficiency significantly deteriorates due to schedule problems. Therefore, the heating temperature is preferably higher than or equal to 42 1150°C. [0127] The heating time in the slab heating process is not particularly limited. However, in order to sufficiently progress the dissolution of carbonitrides of Nb and/or Ti, it is preferable heating is continued for 30 minutes or longer after the heating temperature is reached. However, a case where a slab after casting is directly fed for rolling at a high temperature is not limited thereto. [0128]-- - - - - A rough rolling process of performing rough rolling (first hot rolling) on a slab, which is extracted from a heating furnace within a short time (for example, within 5 minutes, preferably, within 1 minute) after the slab heating process, starts to obtain a rough bar. [0129] Rough rolling (first hot rolling) finishes at a temperature of 1000°C to 1200°C. When the rough rolling end temperature is lower than 1000°C, a hot deformation resistance is increased during rough rolling, which brings about operational problems during rough rolling. [0130] When the rough rolling end temperature is higher than 1200°C, the average grain size is increases, which causes deterioration in toughness. Furthermore, since secondary scales produced during rough rolling are excessively grown, there may be problems during descaling which is subsequently performed or during scale removal in finish rolling. When the rough rolling end temperature is higher than 1150°C, inclusion are drawn, which may cause deterioration in hole expansibility. Therefore, the rough rolling end temperature is preferably lower than or equal to 1150°C. 43 » [0131] When a rolling reduction of rough rolling is low, the average grain size is large and toughness deteriorates. When the rolling reduction is higher than or equal to 40%, the grain size is uniform and small. On the other hand, when the rolling reduction is higher than 65%, inclusion are drawn, which may cause deterioration in hole expansibility. Therefore, the rolling reduction is preferably lower than or equal to 65%. - [0132] In order to refine the average grain size of the hot-rolled steel sheet, an austenite grain size after rough rolling, that is, before finish rolling (second hot rolling) is important. It is preferable that the austenite grain size before finish rolling is smaller. From the viewpoint of grain refining and homogenizing, the austenite grain size is preferably less than or equal to 200 |a.m. To obtain the austenite grain size which is less than or equal to 200 \im., rolling is performed at least once at a rolling reduction of 40% or higher during rough rolling (first hot rolling). [0133] In order to more efficiently obtain the effects of grain refining and Jtiomogenizing, Iheaustenite^rain^izeis jnore preferably Jess than-Or equal to 100 ^un. To that end, it is more preferable that rolling be performed 2 or more times at a rolling reduction of 40% or higher during rough rolling (first hot rolling). However, when rough rolling is performed more than 10 times, there are concerns about a reduction in temperature and excessive production of scale. [0134] As described above, a reduction in austenite grain size before finish rolling is effective for promoting the recrystallization of austenite during subsequent finish - 44 rolling. [0135] The reason is considered to be that an austenite grain boundary after rough rolling (that is, bef3re finish rolling) functions as a recrystallization nucleus during finish rolling. Therefore, the average grain size of the hot-rolled steel sheet can be refined by controlling a waiting time, from finish rolling to the start of cooling, cooling conditions, and the like, described below,in a state where the austenite grain size - during rough rolling is reduced;—In order to measure the austenite grain size after rough rolling, th^ steel sheet is cooled as rapidly as possible, for example, at a cooling rate of 10°C/sec or higher, a structure of a cross-section of the steel sheet is etched to make the austenite grain boundary stand out, and the measurement is performed using an optical microscope. At this time, 20 or more visual fields are observed at a magnification of 50 times or more and measured with an image analysis or cutting method. [0136] During rolling (second hot rolling and third hot rolling) which is performed after rough rolling, endless rolling may be performed in which the rough bar obtained during rou^h roUiiig i s j oined between the rough xo.lling_process (first Jiol jollhig) and the finish hot rolling process (second hot rolling); and rolling is continuously performed. At this time, the rough bar may be temporarily coiled in the coil state, may be stored in a cover having, optionally, a heat insulation function, may be uncoiled again, and may be joined. [0137] In addition, during finish rolling (second hot rolling), there may be a case in which it is preferable that temperature changes in the rolling direction, the transverse 45 - i direction, and the through-thickness direction of the rough bar is controlled to be small. In this case, optionally, a heating apparatus capable controlling the temperature changes in the rolling direction, the transverse direction, and the through-thickness direction of the rough bar may be provided between a rough rolling mill and a finish rolling mill or between stands of finish rolling to heat the rough bar. [0138] Examples of heating means include various kinds of heating measures such as -gas heating7 electrical heating, and induction heating.—Any well-known measures may be used as long as it can control the temperature changes in the rolling direction, the transverse direction, and the through-thickness direction of the rough bar to be small. [0139] As the heating measures, induction heating having industrially superior temperature control response is preferable. In particular, plural transverse induction heating apparatuses capable of shifting in the transverse direction is more preferable because it can appropriately control a temperature distribution in the transverse direction according to the width of the sheet. As the heating measures, a heating apparatus in which the plural transverse induction heating apparatuses and a solenoid induction heating apparatus which is superior Jorieating over the entire width of the sheet are combined is most preferable. [0140] When the temperature is controlled using these heating apparatuses, it is necessary that the heating amount is controlled. In this case, the internal temperature of the rough bar cannot be actually measured. Therefore, a temperature distribution of the rough bar in the rolling direction, the transverse direction, and the throughthickness direction when the rough bar reaches the heating apparatus is estimated - 46 ^ based on previously measured data of a charge slab temperature, a time for which a slab is present in a furnace, a heating ftimace atmosphere temperature, a heating furnace extraction temperature, and a transport time of a table roller. It is preferable that the heating amount be controlled using the heating apparatus based the estimated values. [0141] The heating amount is controlled as follows using the induction heating apparatus." The induction heating apparatus (transverse-induction heating apparatus) generates a magnetic field in the inside thereof when an alternating current flows through a coil. Due to the electromagnetic induction action, an eddy current in a direction opposite to that the coil current is generated in a conductor, provided in the coil, in a circumferential direction perpendicular to a magnetic flux. Due to the Joule heat thereof, the conductor is heated. [0142] The eddy current is most intensively generated on the inside surface of the coil and is exponentially reduced toward the inside (this phenomenon is referred to as the skin effect). As a frequency is lower, a current penetration depth is greater and a Jieating^attem, wliichisainiforminalhicknessjdirejcliDJi,is obtained. As a frequency is higher, a current penetration depth is less and a heating pattern, which has a peak on the surface layer and has a small amount of overheating in a thickness direction, is obtained. [0143] Accordingly, in the transverse induction heating apparatus, heating in the rolling direction and the transverse direction of the rough bar can be performed in the same method as that of the related art. - 47 - [0144] During heating in the through-thickness direction, the penetration depth can be changed by changing the frequency of the transverse induction heating apparatus; and the temperature density can be made uniform by controlling the heating pattern in the through-thickness direction. In this case, a frequency-variable induction heating apparatus is preferably used, but the frequency may be changed by controlling a capacitor. -"- [0145]—" - - - When the heating amount is controlled using the induction heating apparatus, plural inverters having different frequencies may be provided to change respective heating amounts and to thus obtain a heating pattern necessary in the thickness direction. During induction heating, when an air gap with a heating target is changed, the frequency is changed. Therefore, in order to control the heating amount using the induction heating apparatus, an air gap with a heating target may be changed to change the frequency and to thus obtain the desired heating pattern. [0146] For example, as described in "Databook on Fatigue Strength of Metallic Materials" (The Society of Materials Science, Japan), the fatigue strength of a hotrolled or pickled steel sheet has a relationship with the maximum height Ry (corresponding to Rz according to JIS B0601:2001) on the steel sheet surface. Therefore, it is preferable that the maximum height Ry on the steel sheet surface after finish rolling is less than or equal to 15 )j,m (15 |j,mRy, 12.5mm, In 12.5mm). In order to obtain this surface roughness, during descaling, it is preferable that a condition of "Impact Pressure P of High-Pressure Water on Steel Sheet SurfacexFlow Rate L>0.003" is satisfied. - 48 p [0147] In order to prevent the reproduction of scales after descaling, it is preferable that finish rolling is performed within 5 seconds after descaling. After the finish of rough rolling, finish rolling (second hot rolling) starts. A time from the finish of rough rolling to the start of finish rolling is set to be within 150 seconds. When the waiting time from the finish of rough rolling to the start of finish rolling is longer than 150 seconds, the average grain size in the steel sheet is increased and thus, toughness "deteriorates. The lower limit is not particularly limited, but is preferably longer than or equal to 10 seconds when recrystalhzation is completely finished after rough rolling. [0148] During finish rolling, a finish rolling start temperature is set to be higher than or equal to 1000°C. When the finish rolling start temperature is lower than 1000°C, in each finish rolling pass, a rolling temperature, at which the rough bar as the rolling target is heated, is reduced, rolling is performed in a non-recrystallization temperature range, a texture is developed, and isotropy deteriorates. [0149] The upper limit of the finish rolling start temperature is not particularly limited. However, when Ihe upper limit is higher Ihan .or jsqual to 1150°£, l)£foie finish rolling and between passes, there is a concern about a blister which causes spindle scales between ferrite of the steel sheet and a surface scale. Therefore, the finish rolling start temperature is preferably lower than 1150°C. [0150] During finish rolling, when a temperature determined by components of the steel sheet is represented by Tl, in atemperature range of (T1+30)°C to (T1+200)°C, rolling is preformed at least once at a rolling reduction of 30% or higher so as to obtain 49 a total rolling reduction of 50% or higher; and then hot rolling is finished at (T1+30)°C or higher. Tl described herein represents the temperature which is calculated from the contents of respective elements according to the following expression (e). [0151] Tl=850+10x([C]+[N])x[Mn]+350x[Nb]+250x[Ti]+40x[B]+10x[Cr]+100x[Mo]+100x [V] ... (e) In the expression (e), the content of a chemical element (chemical component) —which is not contained in the steel sheet is calculated as 0%. ' ---— [0152] This temperature Tl was empirically obtained. The present inventors empirically found that recrystallization was promoted in an austenite range based on the temperature Tl. However, in the expression (e), the content of a chemical element (chemical component) which is not contained in the steel sheet is calculated as 0%. [0153] When the total rolling reduction in the temperature range of (T1+30)°C to (T1+200)°C is lower than 50%, rolling strain accumulating during hot rolling is not 3uflQciejit,lhej-ecryjstallizatiDJQ of austenite doesjiol^ufiQcienlly advance, _a texture j s developed, isotropy deteriorates, and there is a concern that a sufficient grain refining effect cannot be obtained. Therefore, the total rolling reduction during finish rolling is set to be higher than or equal to 50%. When the total rolling reduction is higher than or equal to 70%, sufficient isotropy can be obtained even in consideration of variation caused by temperature changes and the like, that is more preferable. [0154] On the other hand, when the total rolling reduction is higher than 90%, it is 50 - difficult to maintain a temperature range of (T1+200)°C or lower due to deformation heating and the like. In addition, a rolling load is increased and rolling is difficult. [0155] In order to promote uniform recrystallization by releasing accumulated strain, rolling is performed at least once at a rolling reduction of 30% or higher in one pass during rolling in which the total rolling reduction in the temperature range of (T1+30)°C to (T1+200)°C is 50% or higher. [0156]--"- —' " After the finish of second hot rolling, in order to promote uniform recrystallization, it is preferable that the processing amount of the rolling in a temperature range of a Ar3 transformation temperature to less than (Tl-i-30)°C is suppressed to the minimum. To that end, a total rolling reduction during rolling (third hot rolling) in the temperature range of the Ar3 transformation temperature to less than (T1+30)°C is limited to be lower than or equal to 30%). From the viewpoint of precision in sheet thickness and the shape of the sheet, a rolling reduction of 10%) or lower is preferable. When isotropy is further required, a rolling reduction of 0%) is preferable. 10157] All the processes of first to third hot rolling are finished at the Ar3 transformation temperature or higher. During hot rolling in a temperature range of less than the Ar3 transformation temperature, dual phase rolling is performed and ductility deteriorates due to a residual deformed ferrite structure. Preferably, the hot rolling end temperature is higher than or equal to T1°C. [0158] When a pass of a rolling reduction of 30% or higher in a temperature range of 51 (T1+30)°C to (T1+200)°C is defined as a large reduction pass, primary cooling is performed under conditions of a cooling rate of 50°C/sec or higher, a temperature change of 40°C to 140°C, and a cooling end temperature of (T1+100)°C or lower such that a waiting time t (second) from the finish of a final pass of the large reduction pass to the start of cooling satisfies the following expression (f). When the waiting time t until the start of cooling is longer than 2.5xtl seconds, recrystallized austenite grains are maintained at a high temperature, the grains are grown, and toughness deteriorates. During the first cooling, it is preferable that cooling is performed between rolling ^^^^^^ stands so as to cool the steel sheet with water as rapidly as possible after rolling. When a measuring apparatus such as a thermometer or a thickness meter is provided on a rear surface of a final rolling stand, the measurement is difficult due to steam and the like generated when cooling water is applied thereto. Therefore, it is difiicult to provide a cooling apparatus immediately after the final rolling stand. It is preferable that second cooling is performed at a run-out table, which is provided after passage through the final rolling stand, so as to precisely control a precipitation state of a precipitate and a structure fraction of a microstructure in a narrow range. The cooling apparatus at the run-out table is suitable for controlling the above-described jnicrostructure because feedback can be contrDlled through software by eJectrical signals which are output from a controller including plural water cooling valves controlled by solenoid valves. t<2.5xtl... (f) (wherein tl is represented by the following expression (g)) tl=0.001x((Tf-Tl)xPl/100)^-0.109x((Tf-Tl)xPl/100)+3.1 ... (g) (wherein Tf represents the temperature (°C) after final reduction at a rolling reduction of 30% or higher, and PI represents the rolling reduction (%) during the final reduction - 52 - at a rolling reduction of 30% or higher) It was found that it is more preferable that the waiting time t is set to the time after the finish of the final pass of the large reduction pass, instead of the time after the finish of hot rolling, because substantially preferable recrystalhzation ratio and recrystallization grain size are obtained. As long as the waiting time until the start of cooling is as described above, any one of primary cooling and third hot rolling may be performed first. [01^9] - - — - - The growth of recrystallized austenite grains can be fiirther suppressed by limiting the cooling temperature change to 40°C to 140°C. Furthermore, the development of a texture can be further suppressed by more efficiently controlling variant selection (avoidance of variant limit). When the temperature change during primary cooling is lower than 40°C, recrystallized austenite grains are grown and lowtemperature toughness deteriorates. On the other hand, when the temperature change is higher than 140°C, there is a concern about overshooting of the temperature chanege in a temperature range of the Ar3 transformation temperature or lower. In this case, even when transformation is performed from recrystallized austenite, as a result of ejfficient control of variation selection, a texture is f oxmed and isotrojpy deterioi-ates. In addition, when a steel sheet temperature at the time of finish of cooling is higher than (Tl+100)°C, the cooling effect is not sufficiently obtained. The reason is as follows: even if primary cooling is performed after the final pass under appropriate conditions, when the steel sheet temperature at the time of finish of cooling is higher than (T1+100)°C, there is a concern that grains may be grown and austenite grains may be significantly coarsened. [0160] - 5 3 - When the cooling rate during primary cooling is lower than 50°C/sec, recrystallized austenite grains are grown and low-temperature toughness deteriorates. On the other hand, the upper limit of the cooling rate is not particularly limited, but is preferably lower than or equal to 200°C/sec from the viewpoint of the shape of the steel sheet. [0161] When the waiting time t until the start of cooling is limited to be shorter than tl, the growth of grains is suppressed and superior toughness can be obtained. [0162] When the waiting time t until the start of cooling is limited to satisfy an expression of tl o 2 2 3 o . a • 2 1— 2 : < 00 D. CO - o _ i LU LU H CO S o O 00 -• < LU £ 00 O o Oi in o CJ CO CO CM o 1 o Csl O O d o o o o o o o o o CD o o o o o o o o o o d> o CD o o o o o o o o - • 1 — o r^ CO 1 — o CD CM o o o CO CM o d CO o o d .._ o to CO LO CM" • f < (_ ~ CO CO •o* d Oi r^ CO od 1 o o o o d o o o o d o o o o d o o o o d o o d o o d o o d CO o d CO o d • * , CO o d CO CX3 O d y— •ao o d ^ o d ^ o o d p - o d o o Csi tD 1 — d m CO o d 2 _ l fe LU O UJ 9 to p LU CC LU C 00 o Q- > 0 0 2 < 1- o i n o o d o i n o d 1 o o o o d o o o o d o o o o d o o o o d o o d o o d o o d CO o d o o d r^ CO o d • * C*J T d CO CO o o d i n CM O d "So o d C l o o d f ^ CM ^' CO en d CD CO o d O i ^ 2 1 S LU O m Q 00 LT 1- O S^ m CO o D- g; < 1- ~ CO o d o r^ CO _d o CM o o d i j O O O O d o o o o d o o o o d o o o d o p d o o d oo • > ! - d o o d o o d o o -o d CM o • 1 — d in CO o o d ^— "o * d CM o o d o CO o d T f C3i d ,_ p '— ^ • * o d D. 1 :S LU O a Q W P LU CC LU t 00 O CL •> o o z < 1- i n CO o d en o CM d 1 o o o o d o o o o d o o o o d o o o o d o o d o 1 — d o o d o o d o o d CO o d o •^ d r^ ^o o d i n oo d CM o o d i ^ o d CM i n CM CM CM T - ^ • * CO o d O _ | & LU O UJ Q CO p I1I-I Og QW: Sz 00 O CL g O o 2 < i_ - r^ OJ CM • o d r^ CM O ..- d 1 o o o o d o o o o d o o o o d o o o o d ,_ C31 d o o d o o d o o d o o d CM Csl -o d • * CO o d r- a. z 1 ^ m o o d • * CO (^ d 1 o o o c d o o C3 o d o o o o d o o o o d o o d CD o d o o d o o d o o d o o -o d CM en d o m o o d o m rd o o d o o d • T en CM' ,-_ o d CD Tj- O d CO LU 1 - 00 Z LU LU ^a. >z ,_ o • * o d • * i n .. o d 1 o o o o d o o o o d CD O O O d CO o o o d o o d o o d o o d CD o d o o d o o o d o eg o d a> o o o d CO o o d o p d O) o o d o CM d o Cvl CM • * • * p d 1 - O CO - J < LU a^ oo O o CD •"1- • * o d CD o _ O - d 1 o o o o d o o o o d o o o o d i n o o o d o o d o o d o o d o o d o o d o o -o d o o d o CM O O d • * CM O d o o d T _ o d CM p ^ m r^ d m •"3- o d = 1 z O CO UJ 2^ lU 5 00 O o CM p o CO CO r f d 1 o o o o d o o o o d o o o o d o o o o d o o d o o d o o d o o d o o d o o o d o r^ 1 — d z So O CO UJ 2^ w o o CO • * CO o d i n o o d 1 1 o o o o d o CD o CD d o o o o d o o o o d o o d o o d o o d o o d o o d o o „CD d CD o d CO i n o o d T _ CM O d o o d CO CD CD d - CO co_ T—" i n CD d CO CO o d g a TABLE 2-1 c^ STEEL ACCORDING TO PRESENT INVENTION STEEL FOR COMPARISON STEEL ACCORDING TO PRESENT INVENTION STEEL FOR COMPARISON STEEL ACCORDING TO PRESENT INVENTION STEEL FOR COMPARISON STEEL FOR COMPARISON STEEL FOR COMPARISON STEEL FOR COMPARISON STEEL FOR COMPARISON STEEL NO. 1 2 3 4 5 6 7 8 9 10 METALLURGICAL FAbTORS (1) A B D D D D D D D D (2) 1200 1234 1137 1137 1137 1137 1137 1137 1137 1137 (3) 638 723 720 720 720 720 720 720 720 720 (A) 48'8 573 57b 57b 57b 57b 57b 57b 57b 57b T1 CO) 895 903 887 887 887 887 887 887 887 887 PRODUCTION CONDITIONS HEATING TEMPERATURE CONDITIONS (5) 1260 1260 1230 1120 1230 1230 1230 1230 1230 1260 (6) 45 45 45 45 5 45 45 45 45 45 FIRST H O T ROLLING (7) 2 2 1 1 1 0 1 1 1 1 (8) 45/45 45/45 50 50 50 - 50 50 50 50 (9) 100 100 180 110 140 240 140 140 140 140 (10) 1080 1080 1050 1010 1050 1065 1050 1050 1050 1050 (11) 60 60 60 30 60 60 180 60 60 30 SECOND HOT ROLLING i Ul2) 1050 1050 |1040 1000 1030 1040 1010 :1040 910 ill 10 (13) 90 90 93 93 93 93 93 45 93 93 Tf (°C) 990 990 980 930 970 980 950 980 850 1050 PI (%) 40 40 35 35 35 35 35 35 35 35 (14) 1 1 2 2 2 2 2 2 2 2 (15) 15 12 15 15 15 15 15 15 15 15 CO 00 (DCOMPONENT (2)S0LUTI0N TEMPERATUpltE (°C) (3)Ar3 TRANSFORMATION TEMPERATURE (°C) (4)Ar1 TRANSFORMATION TEMPERATURE (°C) (5)HEATING TEMPERATURE CO (6)RETEMTI0N TIME (MIN) (7)NUMBER OF ROLLING OF 40% OR HIGHER AT 1000°C OR HIGHER (8)R0LLING REDUCTION (%) OF 40% OR HIGHER AT 1000°C OR HIGHER (%) (9) r GRAIN SIZE (um) (10) ROLLING END TEMPERATURE (°C) (11) TIME (SEC) UNTIL START OF FINISH ROLUNG (12) ROLLING START TEMPERATURE (°C) (13) TOTAL ROLLING REDUCTION (%) (14) NUMBER OF PASSES AT ROLLING REDUCTION OF 30% OR HIGHER (15) MAXIMUM TEMPERATURE INCREASE (°C) BETWEEN PASSES 4ft <3^ \BLE 2-2 STEEL FOR COMPARISON STEEL ACCORDING TO PRESENT INVENTION STEEL ACCORDING TO PRESENT INVENTION STEEL FOR COMPARISON STEEL FOR COMPARISON STEEL FOR COMPARISON STEEL FOR COMPARISON STEEL FOR COMPARISON STEEL FOR COMPARISON STEEL FOR COMPARISON STEEL NO. 11 12 13 14 15 16 17 18 19 20 (1) D D D D D D D D D D METALLURGt'OAL FACTORS (2) 1137 1137 1137 1137 1137 1137 1137 1137 1137 1137 (35 72b 72b 72b 72b 72b 72b 72b 72b 1 72b 1 72b 1 (4) 570 570 570 570 570 570 570 570 570 570 T1 (°C) 887 887 887 887 887 887 887 887 887 887 PRODUCTION CONDITIONS HEATING TEMPERATURE CONDITIONS (5) 1230 1230 1230 1230 1230 1230 1230 1230 1230 1230 (6) 45 45 45 45 45 45 45 45 45 45 FIRST H O T ROLLING (7) (8) 50 50 50 50 50 50 50 50 50 50 (9) 140 140 140 140 140 140 140 140 140 140 (10) 1050 1050 1050 1050 1050 1050 1050 1050 1050 1050 (11) 60 60 60 60 60 60 60 60 60 60 SECOND HOT ROLLING i :(i2) 1040 1 I 1 ^040 i 1040 1040 1040 ^040 )040 1040 1040 1040 (13) 93 93 93 93 93 93 93 93 93 93 Tf CO 980 980 980 980 980 980 980 980 980 980 PI (%) - 35 35 35 35 35 35 35 35 35 (14) 0 2 2 2 2 2 2 2 2 2 (15) 15 25 15 15 15 15 15 15 15 15 00 (DCOMPONENT (2)S0LUTI0N TEMPERATUF^fe (°C) {3)Ar3 TRANSFORMATION TEMPERATURE (°C) (4)Ar1 TRANSFORMATION TEMPERATURE (°C) (5)HEATING TEMPERATURE (°G) (6)RETEr|TI0N TIME (MIN) (7)NUMBER OF ROLLING OF 40% OR HIGHER AT 1000°C OR HIGHER (8)R0LUNG REDUCTION (%) OF 40% OR HIGHER AT 1000°C OR HIGHER (%) (9) r GRAIN SIZE (/i m) (10) ROLLING END TEMPERATURE (°C) (11) TIME (SEC) UNTIL START OF FINISH ROLLING (12) ROLLING START TEMPERATURE (°C) (13)V0TAL ROLLING REDUCTION (%) (14) NUMBER OF PASSES AT ROLLING REDu6tlON OF 30% OR HIGHER (15) MAXIMUM TEMPERATURE INCREASE (°C) BETWEEN PASSES TABLE 3-1 C3^ - STEEL ACCORDING TO PRESENT INVENTION STEEL ACCORDING TO PRESENT INVENTION STEEL ACCORDING TO PRESENT INVENTION STEEL FOR COMPARISON STEEL FOR COMPARISON STEEL ACCORDING TO PRESENT INVENTION STEEL FOR COMPARISON STEEL FOR COMPARISON STEEL FOR COMPARISON STEEL FOR COMPARISON STEEL NO. 21 22 23 24 25 26 27 28 29 30 METALLlJtRGICAL FACTORS (1) c E F G H I J K L M (2) 1101 1094 981 - 1100 1024 764 - 1225 1177 (3) 798 779 833 825 813 751 699 800 730 648 (4) 648 629 683 675 663 601 549 650 580 498 Tl (°C) 896 875 866 851 858 876 865 852 909 924 PRODUCTION CONDITIONS HEATING TEMPERATURE CONDITIONS (5) 1200 1200 1200 1200 1200 1200 1200 1200 1230 1230 (6) 60 60 60 60 60 60 60 60 60 60 FIRST H O T ROLLING (7) 3 3 3 3 3 3 3 3 3 3 (8) 40/40/40 40/40/40 40/40/40 40/40/40 40/40/40 40/40/40 40/40/40 40/40/40 40/40/40 40/40/40 (9) 70 70 70 70 70 70 70 70 70 70 (10) 1100 1100 1100 1100 1100 1100 1100 1100 1100 1100 (1:1) i 90 i j 90 1 so 90 90 90 do 90 90 90 SECOND HOT ROLLING (12) 1050 1030 1020 1010 1010 1020 1010 1000 1050 1050 (13) 89 89 89 89 89 89 89 89 89 89 Tf (°C) 990 970 960 950 950 960 950 940 990 990 PI (%) 32 32 32 32 32 32 32 32 32 32 (14) 3 3 3 3 3 3 3 3 3 3 (15) 12 12 12 12 12 12 12 12 12 12 en CO (DCOMPONENT (2)S0LUTI0N TEMPERATUF^E (°C) (3)Ar3 TRANSFORMATION TEMPERATURE (°C) (4)Ar1 TRANSFORMATION TEMPERATURE (°C) (5)HEATING TEMPERATURE (°C) (6)RETErN|+I0N TIME (MIN) (7)NUMBER OF ROLLING OF 40% OR HIGHER AT 1000°C OR HIGHER (8)R0LUNG REDUCTION (%) OF 40% OR HIGHEN AT 1000°C OR HIGHER (%) (9) y GRAIN SIZE (u m) (10) ROLLING END TEMPERATURE (°C) (11) TIME (SEC) UNTIL START OF FINISH ROLLING (12) ROLLING START TEMPERATURE (°C) (13) TOTAL ROLLING REDUCTION (%) (14) NUMBER OF PASSES AT ROLLING REDUdtlON OF 30% OR HIGHER (15) MAXIMUM TEMPERATURE INCREASE (°C) BETWEEN PASSES a < J r^ TABLE 3-2 STEEL ACCORDING TO PRESENT INVENTION STEEL ACCORDING TO PRESENT INVENTION STEEL ACCORDING TO PRESENT INVENTION STEEL ACCORDING TO PRESENT INVENTION STEEL ACCORDING TO PRESENT INVENTION STEEL ACCORDING TO PRESENT INVENTION STEEL ACCORDING TO PRESENT INVENTION STEEL FOR COMPARISON STEEL FOR COMPARISON STEEL FOR COMPARISON STEEL NO. 31 32 33 34 35 36 37 38 39 40 METALLURGICAL FACTORS (1) N 0 P Q R S T T U y (2) 1129 1099 1092 1186 968 1193 933 933 875 1134 m l\6 8d6 745 ih ih eh 8)l 1 8)l M 8^3 (4) 566 656 595 571 613 526 721 721 619 683 T1 (°C) 885 894 924 903 876 900 855 855 853 893 PRODUCTION CONDITIONS HEATING TEMPERATURE CONDITIONS (5) 1230 1230 1230 1200 1230 1250 1250 1250 1250 1250 (6) 60 60 60 60 60 40 40 40 40 40 FIRST HOT ROLLING (7) 3 3 3 3 3 2 2 2 2 2 (8). 40/40/40 40/40/40 40/40/40 40/40/40 40/40/40 45/45 45/45 45/45 45/45 45/45 (9) 70 70 70 70 70 90 90 90 90 90 (10) 1100 1180 1100 1100 1100 1075 1075 1075 1075 1075 (11) 90 90 90 90 90 120 120 120 120 120i SECOND HOT ROLLING (12) 1030 1140 1050 1050 1040 1030 1030 1030 1030 1030 (13) 89 89 89 89 89 55 70 70 70 70 Tf CO) 970 980 990 990 980 970 970 970 970 970 PI (%) 32 32 32 32 32 45 45 45 45 45 (14) 3 3 3 3 3 2 2 2 2 2 (15) 12 12 12 12 12 10 10 10 10 10 o> CO (DCOMPONENT (2)S0LUTI0N TEMPERATURE (°C) (3)Ar3 TRANSFORMATION TEMPERATURE (°C) (4)Ar1 TRANSFORMATION TEMPERATURE (°C) (5)HEATING TEMPERATURE (°C) (6)RETEN+I0N TIME (MIN) (7)NUMBER OF ROLLING OF 40% OR HIGHER AT 1000°C OR HIGHER (8)R0LUNG REDUCTION (%) OF 40% OR HIGHEIR AT 1000°C OR HIGHER (%) (9) y GRAIN SIZE (/i m) (10) ROLLING END TEMPERATURE (°C) (11) TIME (SEC) UNTIL START OF FINISH ROLUNG (12) ROLLING START TEMPERATURE (°C) (13) TOTAL ROLLING REDUCTION (%) (14) NUMBER OF PASSES AT ROLLING REDudtlON OF 30% OR HIGHER (15) MAXIMUM TEMPERATURE INCREASE (°C) BETWEEN PASSES TABLE 4-1 STEEL FOR COMPARISON STEEL ACCORDING TO PRESENT INVENTION STEEL FOR COMPARISON STEEL ACCORDING TO PRESENT INVENTION STEEL FOR COMPARISON STEEL ACCORDING TO PRESENT INVENTION STEEL FOR COMPARISON STEEL FOR COMPARISON STEEL FOR COMPARISON STEEL FOR COMPARISON STEEL NO. 41 42 43 44 45 46 47 48 49 50 METALLURGICAL FACTORS (1) w A B D D D D D D D (2) 888 1200 1234 1137 1137 1137 1137 1137 1137 1137 (3) 633 fe38 723 720 720 ^20 720 720 720 720 (4) 683 488 573 570 570 570 570 570 570 570 T1 CO 855 895 903 887 887 887 887 887 887 887 HEATING TEMPERATURE CONDITIONS (5) 1250 1260 1260 1230 1120 1230 1230 1230 1230 1230 (6) 40 45 45 45 45 5 45 45 45 45 (7) 2 2 2 1 1 1 0 1 1 1 PRODUCTION CONDITIONS FIRST H O T ROLLING (8) 45/45 45/45 45/45 50 50 50 - 50 50 50 (9) 90 100 100 140 110 140 240 140 140 140 (10) 1075 1080 1080 1050 1010 1050 1065 1050 1050 1050 (11) 120 60 60 60 30 60 60 180 60 60 SECOND HOT ROLLING (12) 1030 1050 1050 1040 1000 1030 1040 1010 1040 910 (13) 70 90 90 93 93 93 93 93 45 93 Tf (°C) 970 990 990 980 930 970 980 950 980 850 PI (%) 45 40 40 35 35 35 35 35 35 35 (14) 2 1 1 2 2 2 2 2 2 2 (15) 10 15 12 15 15 15 15 15 15 15 00 (DCOMPONENT (2)S0LUTI0N TEMPERATUFIE (°C) (3)Ar3 TRANSFORMATION TEMPERATURE (°C) (4)Ar1 TRANSFORMATION TEMPERATURE (°C) (5)HEATING TEMPERATURE (°G) (6)RETE[>JtlON TIME (MIN) (7)NUMBER OF ROLLING OF 40% OR HIGHER AT 1000°C OR HIGHER (8)R0LLING REDUCTION (%) OF 40% OR HIGHEIR AT 1000°C OR HIGHER (%) (9) r GRAIN SIZE (jU m) (10) ROLLING END TEMPERATURE (°C) (11) TIME (SEC) UNTIL START OF FINISH ROLLING (12) ROLLING START TEMPERATURE (°C) (13) TOTAL ROLLING REDUCTION (%) (14) NUMBER OF PASSES AT ROLLING REDud+ION OF 30% OR HIGHER (15) MAXIMUM TEMPERATURE INCREASE (°C) BETWEEN PASSES TABLE 4-2 STEEL FOR COMPARISON STEEL FOR COMPARISON STEEL FOR COMPARISON STEEL FOR COMPARISON STEEL FOR COMPARISON STEEL FOR COMPARISON STEEL FOR COMPARISON STEEL FOR COMPARISON STEEL FOR COMPARISON STEEL FOR COMPARISON STEEL NO. 51 52 53 54 55 56 57 58 59 60 METALLURGICAL FACTORS (1) D D D D D D D D D D (2) 1137 1137 1137 1137 1137 1137 1137 1137 1137 1137 (3) 720 720 720 720 720 720 720 720 720 720 (4) 570 570 570 570 570 570 570 570 570 570 T1 ("C) 887 887 887 887 887 887 887 887 887 887 PRODUCTION CONDITIONS HEATING TEMPERATURE CONDITIONS (5) 1260 1230 1230 1230 1230 1230 1230 1230 1230 1230 (6) 45 45 45 45 45 45 45 45 45 45 FIRST H O T ROLLING (7) 1 1 1 1 1 1 1 1 1 1 (8) 50 50 50 50 50 50 50 50 50 50 (9) .140 140 140 140 140 140 140 140 140 140 (10) 1050 1050 1050 1050 1050 1050 1050 1050 1050 1050 (11) 30 60 60 60 60 60 60 60 60 60 SECOND HOT ROLLING (12) 1110 1040 1040 1040 1040 1040 10^0 1040 1 ioko io4o (13) 93 93 93 93 93 93 93 93 93 93 Tf (-0) 1050 980 980 980 980 980 980 980 980 980 P1 (%) 35 - 35 35 35 35 35 35 35 35 (14) 2 0 2 2 2 2 2 2 2 2 (15) 15 15 25 15 15 15 15 15 15 15 ylj^' oo oo (DCOMPONENT (2)S0LUTI0N TEMPERATURE (°C) (3)Ar3 TRANSFORMATION TEMPERATURE (°C) (4)Ar1 TRANSFORMATION TEMPERATURE (°C) (5)HEATING TEMPERATURE (°C) (6)RETEf^tlON TIME (MIN) (7)NUMBER OF ROLLING OF 40% OR HIGHER AT 1000°C OR HIGHER (8)R0LLING REDUCTION (%) OF 40% OR HIGHEN AT 1000°C OR HIGHER (%) (9) y GRAIN SIZE (/i m) (10) ROLlliNG END TEMPERATURE CO (11) TIME (SEC) UNTIL START OF FINISH ROLUNG (12) ROLLING START TEMPERATURE (°C) (13) TOTAL ROLLING REDUCTION (%) (14) NUMBER OF PASSES AT ROLLING REDudtlON OF 30% OR HIGHER (15) MAXIMUM TEMPERATURE INCREASE (°C) BETWEEN PASSES ^ TABLE 5-1 STEEL FOR COMPARISON STEEL ACCORDING TO PRESENT INVENTION STEEL ACCORDING TO PRESENT INVENTION STEEL ACCORDING TO PRESENT INVENTION STEEL FOR COMPARISON STEEL FOR COMPARISON STEEL ACCORDING TO PRESENT INVENTION STEEL FOR COMPARISON STEEL FOR COMPARISON STEEL FOR COMPARISON STEEL NO. 61 62 63 64 65 66 67 68 69 70 METALLURGICAL FACTORS (1) D C E F G H 1 J K L (2) . 1137 1101 1094 ^81 - .1100 lb24 )64 - 1225 (3) 720 798 779 833 825 813 751 699 800 730 (4) 570 648 629 683 675 663 601 549 650 580 T1 (°C) 887 896 875 866 851 858 876 865 852 909 PRODUCTION CONDITIONS HEATING TEMPERATURE CONDITIONS (5) 1230 1200 1200 1200 1200 1200 1200 1200 1200 1230 (6) 45 60 60 60 60 60 60 60 60 60 FIRST H O T ROLLING i i t (7) 1 3 3 3 3 3 3 3 3 3 (8) 50 40/40/40 40/40/40 40/40/40 40/40/40 40/40/40 40/40/40 40/40/40 40/40/40 40/40/40 (9) 140 70 70 70 70 70 70 70 70 70 (10) 1050 1100 1100 1100 1100 1100 1100 1100 1100 1100 i (11) i 60 90 :90 90 90 90 90 90 90 90 SECOND HOT ROLLING (12) 1040 1050 1030 1020 1010 1010 1020 1010 1000 1050 (13) 93 89 89 89 89 89 89 89 89 89 Tf CO 980 990 970 960 950 950 960 950 940 990 PI (%) 35 32 32 32 32 32 32 32 32 32 (14) 2 3 3 3 3 3 3 3 3 3 (15) 15 12 12 12 12 12 12 12 12 12 ^wy CO oo (DCOMPONENT (2)S0LUTI0N TEMPERATUI^E (°C) (3)Ar3 TRANSFORMATION TEMPERATURE (°C) (4)Ar1 tRANSFORMATION TEMPERATURE (°C) (5)HEATING TEMPERATURE (°C) (6)RETENTI0N TIME (MIN) (7)NUMBER OF ROLLING OF 40% OR HIGHER AT lOOO^C OR HIGHER (8)R0LLING REDUCTION (%) OF 40% OR HIGHsh AT 1000°C OR HIGHER (%) (9) r GRAIN SIZE (// m) (10) ROLLING END TEMPERATURE (°C) (11) TIME (SEC) UNTIL START OF FINISH ROLLING (12) ROLLING START TEMPERATURE (°C) (13) TOTAL ROLLING REDUCTION (%) (14) NUMBER OF PASSES AT ROLLING REDUdTION OF 30% OR HIGHER (15) MAXIMUM TEMPERATURE INCREASE (°C) BETWEEN PASSES o TABLE 5-2 STEEL FOR COMPARISON STEEL ACCORDING TO PRESENT INVENTION STEEL ACCORDING TO PRESENT INVENTION STEEL ACCORDING TO PRESENT INVENTION STEEL ACCORDING TO PRESENT INVENTION STEEL ACCORDING TO PRESENT INVENTION STEEL ACCORDING TO PRESENT INVENTION STEEL ACCORDING TO PRESENT INVENTION STEEL FOR COMPARISON STEEL FOR COMPARISON STEEL FOR COMPARISON STEEL FOR COMPARISON STEEL NO. 71 72 73 74 75 76 77 78 79 80 81 82 METALLURGICAL FACTORS (1) M N 0 P Q R S T T U V w (2) il77 1l29 1099 1092 1l86 968 1l93 933 933 375 1134 has (3) 648 716 806 745 721 763 676 871 871 769 833 833 (4) 498 566 656 595 571 613 526 721 721 619 683 683 T1 CO 924 885 894 924 903 876 900 855 855 853 893 855 PRODUCTION CONDITIONS HEATING TEMPERATURE CONDITIONS (5) 1230 1230 1230 1230 1230 1230 1250 1250 1250 1250 1250 1250 (6) 60 60. 60 60 35 60 40 40 40 40 40 40 FIRST H O T ROLLING | (7) 3 3 r 3 3 3 2 2 2 ^ 2 2 (8) 40/40/40 40/40/40 40/40/40 40/40/40 40/40/40 40/40/40 45/45 45/45 45/45 45/45 45/45 45/45 (9) 70 70 70 70 70 70 90 90 90 90 90 90 (10) 1100 1100 1100 1100 1100 1100 1075 1075 1075 1075 1075 1075 ! (11) 90 9b 90 90 90 140 120 120 120 ^io 1210 120 SECOND H O T ROLLING (12) 1050 1030 1040 1050 1050 1040 1030 1030 1030 1030 1030 1030 (13) 89 89 89 89 89 89 55 70 70 70 70 70 Tf (°C) 990 970 980 990 990 980 970 970 970 970 970 970 PI (%) 32 32 32 32 32 32 45 45 45 45 45 45 (14) 3 3 3 3 3 3 2 2 2 2 2 2 (15) 12 12 12 12 12 12 10 10 10 10 10 10 ^ oo (DCOMPONENT (2)S0LUTI0N TEMPERATUf^E (°C) (3)Ar3 TRANSFORMATION TEMPERATURE (°C) (4)Ar1 tRANSFORMATION TEMPERATURE (°C) (5)HEATING TEMPERATURE (°C) (6)RETEl'iTI0N TIME (MIN) (7)NUMBER OF ROLLING OF 40% OR HIGHER AT 1000°C OR HIGHER (8)R0LLING REDUCTION (%) OF 40% OR HIGHEN AT 1000°C OR HIGHER (%) (9) y GRAIN SIZE (.fim) (10) ROLLING END TEMPERATURE (°C) (11) TIME (SEC) UNTIL START OF FINISH ROLLING (12) ROLLING START TEMPERATURE CC) (13) TOTAL ROLLING REDUCTION (%) (14) NUMBER OF PASSES AT ROLLING REDU6TI0N OF 30% OR HIGHER (15) MAXIMUM TEMPERATURE INCREASE (°C) BETWEEN PASSES TABLE 6 TO {223K110> (5)P0LE DENSITY OF CRYSTAL ORIENTATION {332K113> (6)TiC SIZE (nm) (7)TiC DENSITY (GRAINS/ctfi^) i tlf" CO TABLE 11 STEEL NO. 21 22 23 24 25 26 27 28 29 30 31 32 33 34 35 36 37 38 39 , 40 MICROSTRUCTURE ' (1) F+Zw Zw F+Zw F+P F+P F F F+P F+Zw Zw F+Zw F+Zw F+Zw Zw F+Zw F+Zw F+Zw F+Zw F+Zw F+Zw (2) 6.0 7.0 7.0 8.5 7.0 7.0 10.0 8.5 5.0 4.5 5.5 6.0 7.0 6.5 7.0 7.0 5.0 6.0 5.5 6.0 (3) 1.4 1.3 1.7 3.1 4.6 0.6 - 5.1 1.6 1.9 1.9 1.6 1.4 1.8 1.7 1.6 1.7 1.8 1.9 0.7 (4) 2.2 2.5 2.5 2.5 4.0 2.5 2.5 3.1 4.1 6.0 2.5 2.4 2.4 2.3 2.3 3.4 3.9 5.0 3.7 3.5 (5) 3.1 3.4 3.4 3.4 4.8 3.4 3.4 4.0 4.9 5.7 3.4 3.3 3.3 3.2 3.2 4.2 4.6 5.6 4.5 4.3 (6) 1.8 2.5 1.7 - 2.6 1.6 6.0 - 1.9 2.0 2.1 3.0 2.6 2.3 1.8 2.0 2.2 2.3 3.1 1.8 (7). 5X10'^ 1^10'^ 7 X 1 0 ' ' 0 1X10'° 4 x 1 0 '^ 2X10'° 0 9X10'^ 1 X10'6 . 3 X 1 0 ' ' 5 X 1 0 " 5 X 1 0 " dxio" 2 X 1 0 " 3 x 1 0 " 1 X 1 0 " 1 X 1 0 " 1X10'^ dxio" MECHANICAL PROPERTIES! TENSILE TEST YP (MPa) 675 682 429 387 360 377 302 380 796 821 695 678 692 879 477 761 750 720 480 730 TS (MPa) 799 801 624 488 497 601 455 526 1089 1067 812 816 822 1025 631 846 833 800 533 811 EI (%) 19.6 19.2 29.4 34.0 32.2 30.2 38.0 27.2 10.5 11.0 19.5 18.9 19.0 13.4 28.8 17.7 18.0 18.8 28.1 18.5 ISOTROPY 1/|Ar| 5.4 4.5 4.5 4.5 3.5 4.5 4.5 3.8 3.3 2.9 4.5 4.7 4.7 5.0 5.0 3.6 3.5 2.9 3.5 3.5 HOLE EXPANSIBILITY X (%) 97 110 179 145 96 204 212 45 19 22 102 113 120 70 168 89 90 51 70 70 i FRACTURE SURFACE CRACKING 1 0: NONE X: CRACKED • | o o o o i o I 0 X i O o o o o i O o o 1 O i O o o X TOUGHNESS vTrs (°C) -93 -60 -68 -18 -61 -61 -15 -19 -125 -145 -108 -93 -62 -80 -64 -62 -125 -93 -108 -93 (DMICROSTRUCTURE (2)AVERAGE GRAIN SfeE(//m) (3)CEMENTITE GRAIN SIZE(/i m) (4)AVERAGE POLE DENSITY OF ORIENTATION dkoUP {100K011> TO {223l<110> (5)P0LE DENSITY OFCRYSTAL ORIENTATION {332)<113> (6)TiC SIZE (nm) (7)TiC DENSITY (GRAINS/crri^) ^ CO TABLE 12 STEEL ;N0. 41 42 43 44 45 46 47 48 49 50 51 52 53 54 55 56 57 58 59 60 MICROSTRUCTURE (1) F+Zw Zw F+P F+Zw F+Zw F+Zw F+Zw F+Zw F+Zw F+Zw Zw F+Zw F+Zw F+Zw F+Zw F+Zw F+Zw F+P F+Zw F+Zw (2) 6.0 7.5 8.0 8.0 7.0 6.5 10.5 11.0 12.0 4.5 11.0 11.0 10.0 12.0 11.5 11.0 6.5 12.0 8.0 8.0 (3) 1.7 1.9 2.9 1.5 1.7 1.4 1.9 1.9 1.7 1.5 1.5 1.6 1.6 1.9 1.9 1.9 1.6 3.0 2.0 2.2 (4) 3.3 1.7 1.7 1.8 2.0 2.0 1.7 2.0 4.1 5.1 1.7 5.3 1.7 1.7 1.8 1.8 5.4 1.7 1.8 1.8 (5) 4.2 2.5 2.5 2.6 3.0 2.9 2.5 3.0 4.7 5.5 2.5 5^ 2.5 2.5 2.6 2.6 5J 2.5 2.6 2.6 (6) 3.9 1.8 4.4 1.4 2.0 1.7 1.6 1.4 1.4 1.8 1.8 1.4 3.0 2.7 1.7 1.5 2.8 4.7 5.5 1.2 (7) 1X10'" ^XIO'^ 1 dxiO'^ 3x10'' ^xio'" 1X10'« ixio'^ 2Xip'« 1><10'' 2X10'^ 7^10'^ 4X10'^ 6k10'' IklO"* 7!<16'^ gk10'' j y w 1X10'^ ^ k l O '" tklO'5 MECHANICAL PROPERTIES! TENSILE TEST YP (MPa) 450 846 756 733 470 598 704 698 743 702 760 739 734 774 754 743 708 600 475 610 TS (MPa) 523 1000 916 803 524 765 790 791 807 775 833 815 817 837 831 820 778 692 528 753 EI (%) 27.0 13.2 15.0 20.0 22.8 29.0 20.4 20.8 18.5 20.0 18.2 18.8 19.1 18.1 18.3 19.3 20.5 22.4 28.4 22.4 ISOTROPY 1 /1 Ar 1 3.6 12.5 12.5 9.2 6.0 6.5 12.5 6.3 3.3 3.1 12.5 3.0 12.5 12.5 9.2 9.2 3.0 12.5 9.2 9.2 HOLE EXPANSIBILITY X 71 77 48 91 70 94 92 95 46 35 94 45 88 100 98 80 50 66 102 67 : FRACTURE SURFACE CRACKING i 0: NONE X: CRACKED 1 O ' O O ! O i O ! O 1 o O 1 O o ; o o •• o 1 O i o i O ! O 1 O O o TOUGHNESS vTrs CO -93 -58 -48 -48 -68 -80 -11 -5 6 -120 -5 -10 -24 0 0 -7 -80 0 -48 -48 1^*" - J oo (DMICROSTRUCTURE (2)AVERAGE GRAIN SEE(//m) (3)CEMENTITE GRAIN SIZE(//m) i (4)AVERAGE POLE DENSITY OF ORIENTATION dkoUP {100}<011> TO {223K110> (5)P0LE DENSITY OF CRYSTAL ORIENTATION (332K113> (6)TiC SIZE (nm) (7)TiC DENSITY (GRAINS/crti^) i IMiiHHIiKISHHi op TABLE 13 STEEL NO. 61 62 63 64 65 66 67 68 69 70 71 72 73 74 75. 76 77 78 79 80 81 82 MICROSTRUCTURE (1) F+P F+Zw Zw F+Zw F+P F+P F F F+P F+Zw Zw F+Zw F+Zw F+Zw Zw F+Zw F+Zw F+Zw F+Zw F+Zw F+Zw F+Zw (2) 10.0 7.0 9.0 8.0 10:0 10.0 8.5 14.0 9.5 6.0 5.5 6.5 7.0 8.5 7.5 8.5 10.0 7.0 15.0 7.5 8.0 8.0 (3) 3.2 1.4 1.3 1.7 3.1 4.6 0.6 - 5.1 1.6 1.9 1.9 1.6 1.4 1.8 1.7 1.6 1.7. 1.8 1.9 0.7 1.7 (4) 1.7 1.7 2.0 2.0 2.0 1.9 2.0 2.0 2.0 4.1 5.5 2.0 1.9 1.9 1.8 1.8 1.9 2.0 4.1 2.0 2.0 1.8 (5) 2.5 2.5 2.9 2.9 2.9 2.8 2.9 2.9 3.0 M 5J 2.9 2.8 2.8 2.6 2.6 2.7 2.9 M 3.0 2.9 2.6 (6) 6.3 1.8 2.5 1.7 - 3.7 1.6 6.0 - 3.0 2.0 2.1 3.0 2.6 2.3 1.8 2.0 2.2 2.3 3.1 1.8 3.4 (7) 1x10'" SxlO'^ 1x10'6 7 X 10'« 0 1x10'° 4x10'« 5x10'° 0 &x10'^ 1x10'« 5xio'« SxlO'« 6xl0'« 6x10'^ ^ x 1 0 '« &X10'« 1x10'« 1 X ro'« 1 xlO'" fexlO'e 1x10'^ MECHANICAL PRGPERTIESi TENSILE TEST YP (MPa) 587 663 670 417 375 348 365 290 368 784 809 683 666 680 867 465 769 739 716 475 723 457 TS (MPa) 674 785 787 607 473 480 582 437 509 1073 1051 798 802 808 1011 615 854 821 796 528 803 508 EI (%) 23.5 20.0 19.5 30.2 35.1 33.3 31.2 39.6 28.1 10.7 11.2 19.8 19.2 19.3 13.6 29.5 17.6 18.3 18.8 28.4 18.7 28.0 ISOTROPY 1/|Ar| 12.5 12.5 6.5 6.5 6.5 7.0 6.5 6.5 6.4 3.2 3.0 6.5 7.5 7.5 9.2 9.2 7.5 6.5 3.3 6.2 . 6.5 9.2 HOLE EXPANSIBILITY X (%) 66 97 110 179 145 96 204 212 45 19 22 102 113 120 70 168 122 88 91 70 142 76 FRACTURE SURFACE CRACKING 0: NONE k: CRACKED 1 • 0 ! O^ o ! O O 1 0 : 0 X 0 ! 0 1 O i O 0 ' 0 ! O 1 O ! O 0 O o 1 X o TOUGHNESS vTrs (°C) -19 -68 -40 -75 -19 -17 -41 21 -10 -93 -108 -80 -68 -45 -58 -80 -21 -59 31 -58 -48 -48 (DMICROSTRUCTURE (2)AVERAGE GRAIN SI'2E(JU m) (3)CEMENTITE GRAIN SIZE(//m) | (4)AVERAGE POLE DENSITY OF ORIENTATION GIROUP |100}<011> TO {223K110> (5)P0LE DENSITY OF CRYSTAll ORIENTATION [332)<113> (6)TiG SIZE (nm) (7)TiC DENSITY (GRAINS/cm^) W^ CO CO n [0208] "Microstructure" represents the optical microscopic structure; "Average Grain Size" represents the average grain size measured using EBSP-OIM (registered trademark); and "Cementite Grain Size" represents the average grain size of cementite precipitating in a grain boundary. [0209] "Average Pole Density of Orientation Group {100} <011 > to {223}<110>" -and-'Pole Densityof Crystal Orientation-{332}" represent the above-described - pole densities. [0210] "Tie Size" represents the average precipitate size of TiC (which may contain Nb and a small content of N) measured using 3D-AP (3-dimensional Atom Probe); and "TiC Density" represents the average number of TiC per unit volume measured using 3D-AP [0211] "Tensile Tesf represents the result of the tensile test using JIS No. 5 test piece in the C direction. "YP" represents yield point; "TS" represents tensile strength; and the "El" represents-eloiigation. [0212] "Isotropy" represents the inverse of | Ar | as the index. "Hole Expansibility" represents the results of the hole expansibility test method according to JFS T 1001- 1996. "Fracture Surface Cracking" represents the results of observing whether or not fracture surface cracking occurred by visual inspection. Cases where fracture surface cracking did not occur are represented by "None"; and cases where fracture surface cracking occurred are represented by "Cracked" "Toughness" represents the -ri - transition temperature (vTrs) obtained in the sub-size V-notch Charpy impact test. [0213] According to the examples according to the present invention, a high-strength steel sheet having a strength of 540 MPa grade or higher was obtained in which, in the texture of the steel sheet having the predetermined chemical composition, the average pole density of the orientation group {100}<011> to {223}<110> was 1.0 to 4.0; the pole density of a crystal orientation {332}<113> was 1.0 to 4.8, in the thickness center — portion which is a thickness range of 5/8 to 3/8 from the surface-of the steel sheet; the average grain size in the thickness center portion was less than or equal to 10 |am; the grain size of cementite precipitating in a grain boundary of the steel sheet was less than or equal to 2 fim; the average grain size of precipitates containing TiC in grains was less than or equal to 3 nm; and the density of the precipitates was greater than or equal to 1x10 grains/cm . As a result, the results for hole expansibility were also superior at 70% or higher. [0214] In the examples of steel sheet for comparison other than the above-described examples, as shown in Tables 1 to 9, the components or the production conditions were out of the ran^e of the present invention. Therefore, as shown in Tables 10 Jo 13, "Microstructure" was out of the range of the present invention and thus, sufficient mechanical properties were not obtained. In "Cementite Grain Size" and "TiC size" of the tables, "-" represents cementite or TiC not being observed. [Industrial Applicability] [0215] As described above, according to the present invention, it is possible to easily provide a steel sheet which can be applied to components (automobile components such as inner plate components, structural components, suspension components, and transmissions; and other components such as shipbuilding materials, construction materials, bridge materials, marine structures, pressure vessels, line pipes, and mechanical components) requiring workability such as hole expansibility or bendability, strict homogeneity in thickness and circularity after processing, and lowtemperature toughness. In addition, according to the present invention, a highstrength steel sheet having superior low-temperature toughness and a strength of 540 —MPa grade or higher can be stably produced at a low cost. Accordingly, the present invention has a high industrial value. [Designation of Document] CLAIMS [Claim 1] A hot-rolled steel sheet comprising, by mass %, C: a content [C] of 0.02% to 0.07%, Si: a content [Si] of 0.001% to 2.5%, Mn: a content [Mn] of 0.01% to 4%, Al: a content [Al] of 0.001% to 2%, --- — Ti: a content [Ti] of 0.015%-to 0:2%— — "- ^ P: a limited content [P] of 0.15%) or less, S: a limited content [S] of 0.03% or less, N: a limited content [N] of 0.01 % or less, and the balance consisting of Fe and unavoidable impurities, wherein the contents [Ti], [N], [S], and [C] satisfy the following expressions (a) and (b); an average pole density of an orientation group {100}<011> to {223}<110>, which is represented by an arithmetic mean of pole densities of orientations {100}<011>, {116}<110>, {114}<110>, {112}<110>, and {223}<110> is 1.0 to 4.0 and apole density of a crystal orientation {332}<113> is 1.0 to 4.8, in a thickness center portion which is a thickness range of 5/8 to 3/8 from the surface of the steel sheet; an average grain size in the thickness center portion is less than or equal to 10 \xm and a grain size of a cementite precipitating in a grain boundary in the steel sheet is less than or equal to 2 |j,m; and an average grain size of precipitates containing TiC in grains is less than or equal to 3 nm and a number density per unit area is greater than or equal to 1 x 10'^ - ^ - grains/cm . 0%<([Ti]-[N]x48/14-[S]x48/32) ... (a) 0%<[C]-12/48x([Ti]-[N]x48/14-[S]x48/32)... (b) [Claim 2] The hot-rolled steel sheet according to Claim 1, wherein the average pole density of the orientation group {100}<011> to {223}<110> is less than or equal to 2.0 and the pole density of the crystal orientation {332}<113>islessthanor equal to 3.0. ~ ~ [Claim 3] The hot-rolled steel sheet according to Claim 1, wherein the average grain size is less than or equal to 7 |j,m. [Claim 4] The hot-rolled steel sheet according to any one of Claims 1 to 3, further comprising, by mass%, Nb: a content [Nb] of 0.005% to 0.06%, wherein the contents [Nb], [Ti], [N], [S], and [C] satisfy the following expression (c). 0%<[CJ-12/48x([Ti]+INbJx48/93-[N]x48/14-[SJx48/32) ... (c) [Claims] The hot-rolled steel sheet according to Claim 4, further comprising one or two or more selected from the group consisting of, by mass%, Cu: a content [Cu] of 0.02% to 1.2%, Ni: a content [Ni] of 0.01% to 0.6%, Mo: a content [Mo] of 0.01% to 1%, • V: a content [V] of 0.01% to 0.2%, -FCr: a content [Cr] of 0.01% to 2%, Mg: a content [Mg] of 0.0005% to 0.01%, Ca: a content [Ca] of 0.0005% to 0.01 %, REM: a content [REM] of 0.0005% to 0.1 %, and B: a content [B] of 0.0002% to 0.002%. [Claim 6] The hot-rolled steel sheet according to any one of Claims 1 to 3, further • comprising — — " one or two or more selected from the group consisting of, by mass%, Cu: a content [Cu] of 0.02% to 1.2%, Ni: a content [Ni] of 0.01% to 0.6%, Mo: a content [Mo] of 0.01 % to 1 %, V: a content [V] of 0.01 % to 0.2%, Cr: a content [Cr] of 0.01% to 2%, Mg: a content [Mg] of 0.0005% to 0.01%, Ca: a content [Ca] of 0.0005% to 0.01%, REM: a content [REM] of 0.0005% to 0.1%, and JB: a content IB] of 0.0002% to 0.002%. [Claim?] A method of producing a hot-rolled steel sheet, the mothod comprising: heating a steel ingot or a slab including, by mass%), C: a content [C] of 0.02% to 0.07%, Si: a content [Si] of 0.001% to 2.5%, Mn: a content [Mn] of 0.01% to 4%, Al: a content [Al] of 0.001 % to 2%, -sgTTi: a content [Ti] of 0.015% to 0.2%, P: a limited content [P] of 0.15% or less, S: a limited content [S] of 0.03% or less, N: a limited content [N] of 0.01% or less, and the balance consisting of Fe and unavoidable impurities, in which the contents [Ti], [N], [S], and [C] satisfy the following expressions (a) and (b), at SRTmin°C, which is a temperature determined according to the following expression (d), to i260°e;— " "- ^ ~- performing a first hot rolling in which reduction is performed once or more at a rolling reduction of 40%) or higher in a temperature range of 1000°C to 1200C; starting a second hot rolling in a temperature range of 1000°C or higher within 150 seconds after a finish of the first hot rolling; performing a reduction in the second hot rolling in a temperature range of (T1+30)°C to (T1+200)°C, when a temperature determined by components of the steel sheet according to the following expression (e) is represented by T1°C so as to obtain a total reduction ratio of 50 % or higher, with at least one of a rolling reduction ratio of 30%; jerforminj a third hot rolling in which a total rolling reduction is lower than or equal to 30% in a temperature range of a Ar3 transformation temperature to less than (T1+30)°C; finishing the hot rollings at the Ar3 transformation temperature or higher; performing a primary cooling under conditions of a cooling rate of 50°C/sec or higher, a temperature change of 40°C or more and 140°C or less, and a cooling end temperature of (T1+100)°C or lower such that, when a pass of a rolling reduction of 30% or higher in the temperature range of (T1+30)°C to (T1+200)°C is defined as a large reduction pass, a waiting time t (second) from a finish of a final pass of the large reduction pass to a start of cooling satisfies the following expression (f); performing a secondary cooling at a cooling rate of 15°C/sec or higher within 3 seconds from the finish of the primary cooling; and performing a coiling in a temperature range of 550°C to lower than 700°C. 0%<([Ti]-[N]x48/14-[S]x48/32) ... (a) 0%<[C]-12/48x([Ti]-[N]x48/14-[S]x48/32)... (b) SRTmin=7000/{2.75-log([Ti]x[e])}-273 .:; (d)- - Tl=850+10x([C]+[N])x[Mn]+350x[Nb]+250x[Ti]+40x[B]+10x[Cr]+100x[Mo]+100x [V] ... (e) t<2.5xtl... (f) where tl is represented by the following expression (g). tl=0.001x((Tf-Tl)xPl/100)^-0.109x((Tf-Tl)xPl/100)+3.1 ... (g) where Tf represents a temperature (°C) after a final reduction at a rolling reduction of 30% or higher, and PI represents the rolling reduction (%) during the final reduction at a rolling reduction of 30% or higher. [Claim 8] The inethod .of,prjDducing^JiDlir£)lled-sleel.5Jie£l^C£iudingio £!Ja.im 7, wherein the primary cooling is performed between rolling stands and the secondary cooling is performed after passage through a final rolling stand. [Claim9] The method of producing a hot-rolled steel sheet according to Claim 7 or 8, wherein the waiting time t (second) further satisfies the following expression (h). tl, eu:-a-content[Cu]ofO:02%-to-l;2%, --— :— Ni: a content [Ni] of 0.01 % to 0.6%, Mo: a content [Mo] of 0.01% to 1%, V: a content [V] of 0.01% to 0.2%, Cr: a content [Cr] of 0.01% to 2%, Mg: a content [Mg] of 0.0005% to 0.01%, Ca: a content [Ca] of 0.0005% to 0.01%, REM: a content [REM] of 0.0005% to 0.1%, and B: a content [B] of 0.0002% to 0.002%.