JP6264082B2 - Manufacturing method of hot-rolled steel sheet - Google Patents

Description

  The present invention relates to a method for producing a hot-rolled steel sheet. More specifically, the present invention relates to a method for producing a high-strength hot-rolled steel sheet excellent in workability, which is suitable as a material used for automobiles, home appliances, mechanical structures, architectural uses, and the like.

Steel sheets that are used as structural materials for transportation machinery such as automobiles and various industrial machines have various strengths, workability such as elongation and hole expansibility, toughness, and uniformity of their properties. Special characteristics are required.
High strength steel sheets applied to members (subframes) and reinforcements (reinforcing members) that are skeleton members of automobiles are required to have not only ductility but also excellent hole expansibility. In press molding, since workability in various deformation modes is required, reduction of in-plane anisotropy of mechanical properties is also required.

  It is known that it is effective to refine the structure of a steel plate in order to comprehensively improve the mechanical properties of the steel plate. As a structure refinement method, a method of adding Ti or Nb is well known. However, this method has a problem that the in-plane anisotropy of mechanical properties is increased. Patent Document 1 below proposes a method for improving in-plane anisotropy by adding Nb to refine the ferrite grain size and increasing the hot rolling temperature and the rolling reduction to weaken the texture. . However, since Mn is limited to 0.5% or less in this method, there is a problem that it is difficult to obtain a high-strength steel sheet.

  On the other hand, studies for obtaining a high-strength hot-rolled steel sheet rich in workability by using a composite structure having retained austenite and martensite are also widely performed.

  For example, in Patent Document 2 below, a steel sheet having a composite structure composed of ferrite, bainite, retained austenite, and martensite structure, which is extremely low P steel, control of the maximum length of the microstructure and inclusions, A method for improving hole expansibility by hardness control or the like has been proposed. In order to control such microstructures and inclusions, paragraphs 0065 and 0066 of the same document describe that the entry side temperature and the exit side temperature of finish rolling are each set to a predetermined temperature or more.

Patent Document 3 below proposes a high-strength hot-rolled steel sheet having a tensile strength of 780 MPa or more and excellent elongation and hole expansion workability and a method for producing the same. This steel plate has C: 0.05 to 0.15%, Si: 1.50% or less, Mn: 0.5 to 2.5%, P: 0.035% or less, S: 0.01% or less, A bainite containing Al: 0.02 to 0.15%, Ti: 0.05 to 0.2%, the balance having a chemical composition composed of Fe and inevitable impurities, and a metal structure of 60 to 95 area% In addition, solid solution strengthened or precipitation strengthened ferrite or a structure containing ferrite and martensite. In order to obtain such a solid solution strengthened or precipitation strengthened structure, paragraph 0036 of the same document describes that the hot rolling finishing temperature is set to Ar ₃ or higher.

Japanese Unexamined Patent Publication No. 2000-111984 Special table 2004-536965 gazette JP 2006-274318 A

Hirofumi Inoue, Naoji Inabe “Determination of crystal orientation distribution function from incomplete pole figure by iterative series expansion method” Journal of the Japan Institute of Metals, The Japan Institute of Metals, August 1994, Vol. 58, No. 8, p. 892-898

  As described above, conventionally, studies have been conducted to obtain a high-strength hot-rolled steel sheet having high workability by using a composite structure containing retained austenite and martensite.

  However, in recent years, more excellent ductility and hole expansibility have been required for high-strength hot-rolled steel sheets. As described above, since the conventional manufacturing method focuses on the temperature of hot rolling to obtain a desired structure, in order to more stably manufacture a hot-rolled steel sheet having such excellent mechanical properties. Needs more ingenuity.

  An object of this invention is to provide the manufacturing method of the hot-rolled steel plate which has the outstanding ductility and hole expansibility while being high intensity | strength.

  Accordingly, the present inventors have investigated in detail the effect of the hot rolled steel sheet having a fine composite structure mainly composed of ferrite, focusing on the ferrite grain size and texture, focusing on the ferrite grain size.

  As a result, the rolling reduction at the end of hot rolling, the temperature at which hot rolling is completed, and the three-stage cooling after hot rolling combine to reduce the ferrite grain size and control the texture at the center of the plate thickness. It has become possible, and it has been newly found that a hot-rolled steel sheet having excellent ductility and hole expandability while having high strength can be produced. Specifically, the recrystallization austenite grains are finely promoted by appropriately promoting the recrystallization of austenite by setting the rolling reduction and rolling completion temperature of the rolling pass immediately before the final rolling pass and the rolling completion temperature within a predetermined range. Become. Here, after completion of hot rolling, simply cooling to the coiling temperature as in the prior art does not mean that there is no possibility of variation in the structure of the hot-rolled steel sheet depending on the width of the cooling temperature and the cooling time. Therefore, in order to stably obtain a hot-rolled steel sheet having a desired structure with respect to a steel sheet having such fine recrystallized austenite at the time of completion of hot rolling, three stages in which the cooling temperature and the cooling stop time are strictly defined. By performing the cooling, it is possible to form a desired structure, refine the structure, and homogenize the structure.

  In this way, the present inventors have achieved the above-described hot rolling with excellent mechanical properties by simultaneously satisfying the rolling reduction at the end of hot rolling, the hot rolling conditions, and the cooling conditions after hot rolling in an integral manner. The knowledge to manufacture steel sheets was obtained.

The present invention based on the above-mentioned new knowledge is, in mass%, C: 0.005% to 0.3%, Si: 0.02% to 3.0%, Mn: 0.7% to 4.0% Hereinafter, P: 0.20% or less, S: 0.010% or less, sol. A multi-pass hot rolling is applied to a slab containing Al: 0.001% or more and 1.0% or less, N: 0.01% or less, and the balance comprising Fe and impurities to obtain a hot-rolled steel sheet. A method for producing a hot-rolled steel sheet, wherein the rolling reduction of the rolling pass immediately before the final rolling pass in the multi-pass hot rolling is 22% to 60%, and the final rolling pass is reduced in the multi-pass hot rolling. The rate is 10% or more and 50% or less, the rolling completion temperature is Ar ₃ points or more and 830 ° C. or more and 1100 ° C. or less, and after completion of hot rolling, 0.1 seconds or more and 1.0 seconds or less (rolling completion temperature −40 ° C. ) After cooling to the following temperature and allowing it to stay in the temperature range for 0.2 second to 4 seconds, cool to 750 ° C or lower and 600 ° C or higher at a cooling rate of 30 ° C / second or higher. For more than 2 seconds in the above temperature range, A method for producing a hot-rolled steel sheet, characterized by cooling to a lower temperature range , and the multi-pass hot rolling satisfies the following formula (1) .
0.002 / exp (−6080 / (T + 273)) ≦ t ≦ 2.0 (1)
Where the meaning of each symbol is as follows:
t: Time (seconds) between passes from the completion of rolling of the rolling pass immediately before the final rolling pass to the start of rolling of the final rolling pass.
T: Rolling completion temperature (° C.) of the rolling pass immediately before the final rolling pass.

Before Symbol Chemical composition, instead of a part of the Fe, 1 or two or more elements selected from the following group (% are all by weight%) may further contain:
(1) 1 selected from the group consisting of Ti: 0.1% or less, Nb: 0.1% or less, V: 0.5% or less, Mo: 0.5% or less, and B: 0.005% or less Species or two or more species;
(2) Cr: 2.0 mass% or less,
(3) One or more selected from the group consisting of Ca: 0.01% or less, Mg: 0.01% or less, and REM: 0.01% or less.

  According to the present invention, it is possible to stably produce a hot-rolled steel sheet having high strength and excellent ductility and hole expansibility and having both strength and workability. The hot-rolled steel sheet produced by the method of the present invention is useful for the production of automobile subframes and reinforcing members.

  The method for producing a hot-rolled steel sheet according to the present invention will be described in more detail below. In the following description, all percentages relating to the chemical composition of steel are mass%.

<Chemical composition of steel>
C: 0.005% or more and 0.3% or less C has an action of generating a hard second phase and increasing the strength of the steel. When the C content is less than 0.005%, it is difficult to sufficiently obtain the effect by the above action. Therefore, the C content is 0.005% or more. Preferably it is 0.007% or more. On the other hand, if the C content exceeds 0.3%, the ferrite transformation after hot rolling is remarkably delayed, the area ratio of the second phase becomes excessive, and the hole expandability and ductility decrease significantly. Furthermore, the deterioration of weldability becomes remarkable. Therefore, the C content is 0.3% or less. Preferably it is 0.25% or less, More preferably, it is 0.20% or less.

Si: 0.02% or more and 3.0% or less Si promotes ferrite transformation and suppresses cementite precipitation, thus promoting C concentration to untransformed austenite in the cooling process after hot rolling. It is an element that makes it possible to increase the hardness of the second phase in the steel structure after cooling and to efficiently increase the strength of the steel. When the Si content is less than 0.02%, it is difficult to obtain the effect by the above action. Therefore, the Si content is 0.02% or more. Preferably it is 0.04% or more. On the other hand, if the Si content exceeds 3.0%, the surface properties may be significantly deteriorated due to surface oxidation in the hot rolling process. Therefore, the Si content is 3.0% or less. Preferably it is 2.5% or less, More preferably, it is 2.0% or less, Most preferably, it is 1.5% or less.

Mn: 0.7% or more and 4.0% or less Mn has the effect of enhancing the hardenability, so that it is possible to increase the hardness of the second phase in the steel structure after cooling and efficiently increase the strength of the steel. It is an important element. Moreover, it has the effect | action which raises the intensity | strength of steel by solid solution strengthening. When the Mn content is less than 0.7%, it is difficult to obtain the effect by the above-described action. Therefore, the Mn content is 0.7% or more. Preferably it is 0.9% or more. On the other hand, if the Mn content exceeds 4.0%, the ferrite transformation in the cooling process after hot rolling is excessively delayed, and the area ratio of the second phase may be excessive. Therefore, the Mn content is 4.0% or less. Preferably, it is 3.5% or less, more preferably 3.0% or less.

P: 0.20% or less P is an element contained as an impurity and has an effect of reducing the workability of the steel sheet. Therefore, the P content is 0.20% or less. Preferably, it is 0.06% or less, more preferably 0.03% or less, and particularly preferably 0.015% or less.

S: 0.010% or less S is an element contained as an impurity, and has the effect of reducing the workability of the steel sheet. For this reason, S content shall be 0.010% or less. Preferably, it is 0.005% or less, more preferably 0.003% or less, and particularly preferably 0.001% or less.

sol. Al: 0.001% or more and 1.0% or less Al has an action of making steel healthy by deoxidation. sol. If the Al content is less than 0.001%, it is difficult to obtain the effect by the above action. Therefore, sol. The Al content is 0.001% or more. Preferably it is 0.01% or more, More preferably, it is 0.02% or more. On the other hand, sol. Even if the Al content is more than 1.0%, the effect by the above action is saturated, and the cost is unnecessarily increased. Therefore, sol. The Al content is 1.0% or less, preferably 0.8% or less, and more preferably 0.6% or less.

N: 0.01% or less N is an element contained as an impurity and has the effect of reducing the workability of the steel sheet. For this reason, N content shall be 0.01% or less. Preferably it is 0.006% or less.

  The following elements are optional elements that can be included in the hot-rolled steel sheet of the present invention as needed.

One or two selected from the group consisting of Ti: 0.1% or less, Nb: 0.1% or less, V: 0.5% or less, Mo: 0.5% or less, and B: 0.005% or less More than seeds Ti, Nb, V, Mo, and B have the effect of increasing the strength of the steel by precipitation in the steel as carbides or nitrides. At the same time, it also has the effect of suppressing the coarsening of ferrite to refine the steel structure. Further, Ti and Nb have the effect of suppressing the coarsening of austenite to further refine the steel structure. Therefore, you may contain 1 type, or 2 or more types of these elements. However, if it is excessively contained, the workability deteriorates due to coarse carbides or nitrides. Further, Ti and Nb cause an excessive increase in the recrystallization temperature, making it difficult to obtain the target texture. Therefore, the contents of Ti and Nb are each set to 0.1% or less. Each is preferably 0.06% or less, more preferably 0.03% or less, particularly preferably 0.02% or less, and most preferably 0.01% or less. Further, the contents of V and Mo are 0.5% or less, respectively. Each is preferably 0.3% or less, more preferably 0.1% or less, particularly preferably 0.05% or less, and most preferably 0.01% or less. Further, the B content is 0.005% or less. Preferably it is 0.003% or less, More preferably, it is 0.001% or less, Most preferably, it is 0.0005% or less. In order to more reliably obtain the effect of the above action, Ti: 0.001% or more, Nb: 0.001% or more, V: 0.01% or more, Mo: 0.001% or more, and B: 0 It is preferable to satisfy any of 0.0001% or more.

Cr: 2.0% or less Cr has an action of promoting the formation of the second phase containing martensite by enhancing the hardenability. Therefore, Cr may be contained. However, if excessively contained, ferrite transformation in the cooling process after hot rolling is excessively delayed, and the area ratio of the second phase may become excessive. Therefore, the Cr content is 2.0% or less. Preferably it is 1.5% or less, More preferably, it is 1.0% or less, Most preferably, it is 0.5% or less. In addition, in order to acquire the effect by the said action | operation more reliably, it is preferable to make Cr content 0.02% or more.

One or more selected from the group consisting of Ca: 0.01% or less, Mg: 0.01% or less, and REM: 0.01% or less Ca, Mg, and REM are formed in the process of solidification of molten steel It has the function of maintaining the soundness of the slab by miniaturizing oxides and nitrides. Therefore, you may contain 1 type, or 2 or more types of these elements. However, even if contained excessively, the effect by the above action is saturated, and since these elements are expensive, the cost is unnecessarily increased. Therefore, the content of these elements is 0.01% or less. The total content of these elements is preferably 0.005% or less. In addition, in order to acquire the effect by the said action more reliably, it is preferable to contain any element 0.0002% or more.

  Here, REM refers to a total of 17 elements of Sc, Y and lanthanoid, and the content of REM refers to the total content of these elements. In the case of a lanthanoid, it is industrially added in the form of misch metal.

<Manufacturing method>
A hot rolled steel sheet is manufactured by subjecting the slab having the above chemical composition to multi-pass hot rolling. The slab to be subjected to hot rolling may be obtained by continuous casting or casting / bundling rolling, but may be obtained by adding hot working or cold working to them. Moreover, the reheated slab may be used for hot rolling, or a slab in a high temperature state after continuous casting or after partial rolling may be used as it is. If the hot rolling completion temperature mentioned later can be ensured, there will be no restriction | limiting in particular. The temperature of the slab used for hot rolling is generally 900 to 1350 ° C. Multi-pass hot rolling can be performed using a lever mill or a tandem mill. From the viewpoint of industrial productivity, it is preferable to use a tandem mill for at least the last several stages.

In the method for producing a hot-rolled steel sheet according to the present invention, the rolling reduction of the rolling pass immediately before the final rolling pass in multi-pass hot rolling is 22% to 60%, and the rolling reduction of the final rolling pass is 10% to 50%. %, And the rolling completion temperature is Ar ₃ or more and 830 ° C. or more and 1100 ° C. or less, and is cooled to a temperature of 0.1 second or more and 1.0 second or less (rolling completion temperature −40 ° C.) after hot rolling is completed. Then, after being kept in the temperature range for 0.2 second or more and 4 seconds or less, it is cooled to a temperature range of 750 ° C. or less and 600 ° C. or more at a cooling rate of 30 ° C./second or more, and the temperature range is 2 seconds. It is made the hot-rolled steel sheet by making it hold | maintain for the above time and cooling to the temperature range of 600 degrees C or less.

  By adopting the above production method, a hot rolled steel sheet having a steel structure suitable for ductility and hole expansibility and a texture at the center of the plate thickness can be produced, as will be described in detail later.

(The rolling reduction of the rolling pass immediately before the final rolling pass is 22% to 60%, and the rolling reduction of the final rolling pass is 10% to 50%)
By increasing the rolling reduction ratio of the rolling pass immediately before the final rolling pass as described above, recrystallized austenite grains are mainly refined, and further, the rolling reduction rate of the final rolling pass is increased as described above. In this way, γ is recrystallized and refined, and in combination with the cooling conditions after hot rolling described later, a hot-rolled steel sheet having a fine steel structure and texture suitable for ductility and hole expansibility is manufactured. can do. Therefore, the rolling reduction of the rolling pass immediately before the final rolling pass is set to 22% or more. Preferably it is 25% or more. More preferably, it is 30% or more. The rolling reduction of the final rolling pass is 10% or more, preferably 15% or more, more preferably 20% or more, and particularly preferably 23% or more.

  On the other hand, from the viewpoint of ensuring good flatness for the steel sheet and suppressing undesired texture development, the rolling reduction of the rolling pass immediately before the final rolling pass is 60% or less. Preferably it is 50% or less. Further, the rolling reduction of the final rolling pass is 50% or less, preferably 45% or less.

(Rolling completion temperature is Ar ₃ or higher and 830 ° C. or higher and 1100 ° C. or lower)
The rolling completion temperature is Ar ₃ or more and 830 ° C. or more and 1100 ° C. or less. As a result, ferrite transformation during rolling is prevented, and recrystallization of austenite is moderately promoted between rolling passes, and recrystallized austenite grains are mainly refined. After hot rolling, it will be described later. Combined with the cooling conditions after hot rolling, a hot rolled steel sheet having a fine steel structure and texture suitable for ductility and hole expansibility is obtained. When the rolling completion temperature is less than 830 ° C., the deformation resistance during rolling becomes remarkably high and rolling becomes difficult. In addition, austenite before cooling after hot rolling becomes extremely flat, and a hot rolled steel sheet as a final product takes on a form of structure stretched in the rolling direction, resulting in increased plastic anisotropy and reduced formability. Therefore, the rolling completion temperature is 830 ° C. or higher. Preferably it is 850 degreeC or more, More preferably, it is 880 degreeC or more. On the other hand, when the rolling completion temperature exceeds 1100 ° C., the release of strain introduced by rolling proceeds, and a hot-rolled steel sheet having both ductility and hole expandability cannot be obtained. Therefore, the rolling completion temperature is 1100 ° C. or lower. Preferably it is 1060 degrees C or less, More preferably, it is 1020 degrees C or less, Most preferably, it is 980 degrees C or less. In addition, these temperatures are the surface temperature of steel materials, and can be measured with a radiation thermometer or the like.

As manufacturing conditions, it is preferable that the following formula (1) is further satisfied.
0.002 / exp (−6080 / (T + 273)) ≦ t ≦ 2.0 (1)
Where the meaning of each symbol is as follows:
t: Time (seconds) between passes from the completion of rolling of the rolling pass immediately before the final rolling pass to the start of rolling of the final rolling pass.

T: Rolling completion temperature (° C.) of the rolling pass immediately before the final rolling pass.
By satisfying the above formula (1), austenite recrystallization is promoted and austenite grain growth is achieved between the passes from the completion of rolling of the rolling pass immediately before the final rolling pass to the start of rolling of the final rolling pass. Therefore, the recrystallized austenite grains are further refined during rolling, which makes it easier to obtain a fine steel structure and texture suitable for ductility and hole expansibility.

(Cooling to a temperature range of 0.1 to 1.0 seconds after completion of hot rolling (rolling completion temperature −40 ° C.) or less)
After completion of hot rolling, in order to refine the structure of the hot rolled steel sheet as the final product and simultaneously suppress the development of the texture, within 0.1 second to 1.0 second after the completion of rolling (rolling completion temperature) Cool to -40 ° C or below. (Rolling completion temperature −40 ° C.) The shorter the time for cooling to the temperature range below, the easier it is to obtain a fine structure, but the texture develops excessively, the desired structure cannot be obtained, The directionality may decrease. (Rolling completion temperature −40 ° C.) When the time for cooling to the temperature range of 0.1 second or more is 0.1 seconds or more, recrystallization of austenite is moderately promoted, and the austenite grain interfacial area which is α transformation nucleation site increases. Organization is obtained. This also makes it easier to obtain a desired texture. Preferably it is 0.13 second or more, More preferably, it is 0.15 second or more.

  On the other hand, if the time for cooling to a temperature range of (rolling completion temperature −40 ° C.) or less exceeds 1.0 seconds, austenite grains grow significantly and the structure of the hot-rolled steel sheet as a final product also becomes coarse. Therefore, the time for cooling to a temperature range of (rolling completion temperature −40 ° C.) or less is 1.0 second or less. Preferably, it is 0.8 seconds or less, more preferably 0.5 seconds or less, and most preferably 0.3 seconds or less. The cooling at this time is preferably 200 ° C./s or more, and more preferably 300 ° C./second or more.

(Residence of 0.2 to 4 seconds in the temperature range)
Immediately after the cooling is stopped, it is a mixed grain structure of finely recrystallized austenite and relatively coarse processed austenite, and the transformed structure in this state tends to be inhomogeneous. The structure of the final product is homogenized by allowing it to stay in the temperature range for a short time. For this purpose, a residence time of 0.2 seconds or longer is required. The residence time is preferably 0.3 seconds or more, and more preferably 0.5 seconds or more. On the other hand, if the residence time exceeds 4 seconds, the recrystallized austenite becomes coarse due to grain growth, and the structure of the final product also becomes coarse. Therefore, the residence time in the temperature range is set to 4 seconds or less. Preferably it is 3 seconds or less, More preferably, it is 2.5 seconds or less.

(Cooling to a temperature range of 750 ° C. or less and 600 ° C. or more at a cooling rate of 30 ° C./second or more, and staying in the temperature range for 2 seconds or more)
After that, water cooling is performed again, while suppressing the grain growth suppression of recrystallized austenite and the recovery of processing strain of the remaining processed austenite, cooling to a temperature range where transformation from austenite to ferrite becomes active, and in that temperature range Once held, the above processing strain is used as a driving force to transform from austenite to ferrite. Thereby, the density of the nucleation site of ferrite transformation increases dramatically, and a fine steel structure is obtained.

  For this reason, it cools to a temperature range of 750 ° C. or lower and 600 ° C. or higher at a cooling rate of 30 ° C./second or higher, and holds it for 2 seconds or longer in the temperature range. By cooling at 30 ° C./second or more, it is possible to suppress grain growth suppression of recrystallized austenite and recovery of processed austenite. Preferably, it is 45 ° C./second or more, more preferably 60 ° C./second or more.

  The transformation from austenite to ferrite becomes active when it reaches a temperature range of 750 ° C. or lower and 600 ° C. or higher. Therefore, by holding for 2 seconds or longer in the above temperature range, transformation from austenite to ferrite with the processing strain as the driving force. As a result, the density of nucleation of ferrite transformation increases dramatically, and it becomes easy to obtain a fine steel structure. The upper limit of the holding time in the temperature range does not need to be specified, but is preferably within 20 seconds from the viewpoint of productivity.

  After maintaining in the above temperature range, the untransformed austenite is cooled to a temperature range of 600 ° C. or lower in order to obtain a hard second phase such as pearlite, bainite, and martensite. In this case, the average cooling rate is preferably 30 ° C./second or more.

After cooling to a temperature range of 600 ° C. or lower, winding is generally performed.
Thus, the hot-rolled steel sheet manufactured by the method according to the present invention may be plated to be a plated steel sheet. The plating may be either electroplating or hot dip plating, and the type of plating is not particularly limited, but is generally zinc-based plating including zinc plating and zinc alloy plating. Examples of the plated steel sheet include an electrogalvanized steel sheet, an electrogalvanized nickel-plated steel sheet, a hot-dip galvanized steel sheet, an alloyed hot-dip galvanized steel sheet, and a hot-dip zinc-aluminum alloy plated steel sheet. The plating adhesion amount may be a general amount.

<Steel structure>
The hot-rolled steel sheet obtained by the production method according to the present invention is composed of 40% by area or more of ferrite and the second phase at a depth of 1/4 of the sheet thickness from the steel sheet surface, and the following formula (2) and It is preferable to have a steel structure that satisfies (3).

D ≦ 7.0 (2)
1.0 ≦ D ≦ 8 / (100 × C × Mn) ^0.22 (3)
Where the meaning of each symbol is as follows:
D: Average particle diameter (μm) of the ferrite,
C: C content (% by mass) in the chemical composition
Mn: Mn content (% by mass) in the chemical composition.

  In addition to polygonal ferrite, the ferrite includes bainitic ferrite, acicular ferrite, granular bainitic ferrite, and pseudopolygonal ferrite, and does not include ferrite forming a pearlite structure or a bainite structure.

  Further, the second phase means a phase and structure other than the above-mentioned ferrite constituting the main phase, and even those composed of one kind selected from the group consisting of cementite, bainite, martensite, retained austenite, etc. A mixed tissue containing two or more kinds may be used.

  Here, the steel structure at a depth position that is ¼ of the plate thickness from the steel sheet surface is defined because the steel structure at the position represents the steel structure of the steel sheet.

-Ferrite area ratio: 40% or more The ferrite phase is necessary to obtain good ductility. Therefore, the area ratio of the ferrite phase is preferably 40% or more. More preferably, it is 45% or more, and particularly preferably 50% or more. On the other hand, in the case of a ferrite single phase structure, the work hardening rate may decrease. Therefore, the area ratio of the ferrite phase is preferably 97% or less. More preferably, it is 95% or less.

-Satisfying the above formulas (2) and (3) In the present invention, the refinement of ferrite grains is important. Thereby, generation | occurrence | production, progress, and connection of a crack are suppressed and local deformability is improved. Furthermore, by finely dispersing the second phase, the deformation during processing is made uniform, the work hardening rate is improved, and the ductility and hole expandability are improved. On the other hand, excessive miniaturization may reduce the work hardening rate and reduce ductility. For this reason, it is preferable to satisfy said formula (2) and (3). More preferably, the following formula (3-1) is satisfied:
1.0 <= D <= 7 / (100 * C * Mn) ^0.22 (3-1).

<Group organization>
The steel structure of the hot-rolled steel sheet obtained by the production method according to the present invention satisfies the following formulas (4) and (5) at the center position of the thickness, and {211} <011> to {100} <011> It is preferable to have a texture in which the maximum value of the ratio of the diffracted X-ray intensity of the orientation group to the diffracted X-ray intensity of the random sample is 8.0 or less.

I {111} ≧ 1.2 (4)
I {111} -I {100} -I {211} ≧ −3.2 (5)
Where the meaning of each symbol is as follows:
I {111}: the value of the ratio of {111} diffracted X-ray intensity to the diffracted X-ray intensity of a random sample,
I {100}: the value of the ratio of {100} diffracted X-ray intensity to the diffracted X-ray intensity of a random sample,
I {211}: The value of the ratio of {211} diffracted X-ray intensity to diffracted X-ray intensity of a random sample.

The maximum value of the ratio of the diffraction X-ray intensity of the {211} <011> to {100} <011> orientation group to the diffraction X-ray intensity of the random sample: 8.0 or less {211} < When the texture of 011> to {100} <011> orientation develops, the hole expandability is particularly lowered. For this reason, hole expansibility can be improved by reducing these azimuth | directions. Therefore, it is preferable to set the maximum value of the X-ray random intensity ratio in these directions to 8.0 or less. More preferably, it is 7.5 or less, Most preferably, it is 7.0 or less. The lower the better.

  Here, {hkl} represents a crystal plane parallel to the rolling surface, and <uvw> represents a crystal direction parallel to the rolling direction. That is, {hkl} <uvw> indicates a crystal in which {hkl} is oriented in the normal direction of the plate surface and <uvw> is oriented in the rolling direction.

  The diffraction X-ray intensities of the {211} <011> to {100} <011> orientation groups are obtained by obtaining (110), (200), (211) incomplete pole figures by X-ray diffraction, and then the above-mentioned non-patent ODF analysis is performed by the iterative series expansion method described in Document 1, and the diffraction X-ray intensity is φ1 = 0 °, φ2 = 45 °, and φ = 0-35 ° in the Bunge method. Among them, the highest value of the intensity ratio with respect to the random sample may be 8.0 or less. The incomplete pole figure is a pole figure obtained by the reflection method. A random sample is a sample having an irregular distribution without having a crystal orientation.

-Satisfy the above formulas (4) and (5) When {111} in the plate surface direction develops, the hole expandability improves, and when {100} and {211} develop, the hole expandability decreases. For this reason, hole expansibility can be improved by promoting the development of {111} and suppressing the development of {100} and {211}. Therefore, it is preferable that the above expressions (4) and (5) are satisfied. Regarding the above formula (4), it is more preferable to satisfy the following formula (4-1), and it is particularly preferable to satisfy the following formula (4-2). I {111} is preferably as high as possible. As for the above formula (5), it is more preferable to satisfy the following formula (5-1), particularly preferably to satisfy the following formula (5-2), and to satisfy the following formula (5-3). Most preferred. It should be noted that the value of “I {111} −I {100} −I {211}” is preferably as high as possible.

I {111} ≧ 1.4 (4-1)
I {111} ≧ 1.6 (4-2)
I {111} -I {100} -I {211} ≧ −3.0 (5-1)
I {111} -I {100} -I {211} ≧ −2.8 (5-2)
I {111} -I {100} -I {211} ≧ −2.6 (5-3)
In addition, in the conventional controlled cooling controlled rolling method or the method of adding Ti, Nb or the like to refine the structure, {100} and {211} are developed, while {111} is inhibited from developing. It had been.

  By adopting the production method according to the present invention, {111} is developed along with the refinement of the structure, and at the same time, the development of {100} and {211} is suppressed, so that hot rolling having excellent ductility and hole expandability is achieved. A steel plate can be obtained.

<Mechanical properties>
The hot-rolled steel sheet obtained by the production method according to the present invention has excellent ductility and hole expansibility by controlling the steel structure and the texture. However, when the tensile strength of the steel sheet is small, effects such as weight reduction and rigidity improvement are small. Therefore, it is preferable that the tensile strength (TS) of a steel plate is 370 MPa or more. TS is more preferably 490 MPa or more, particularly preferably 540 MPa.

  About the ductility and hole expansibility of the manufactured hot-rolled steel sheet, TS × EL (EL: total elongation) and TS × HER (HER: Japan Iron and Steel Federation Standard JFS-T1001), which are indicators of the balance between them and strength, respectively. -It is appropriate to evaluate by the hole expansion rate specified in 1996). For the ductility, the value of TS × EL is preferably 14000 MPa ·% or more, more preferably 15000 MPa ·% or more, and particularly preferably 16000 MPa ·% or more. As for the hole expansibility, the value of TS × HER is preferably 44000 MPa ·% or more, more preferably 47000 MPa ·% or more, and particularly preferably 50000 MPa ·% or more.

  After melting and casting steel having the chemical composition shown in Table 1, a 30 mm thick slab was formed by hot forging. The obtained slab was heated to 1250 ° C. and subjected to hot rolling under the conditions shown in Table 2 using a small test tandem mill, and finished to a thickness of 2 mm.

  In Table 2, passes 1 and 2 of the final hot rolling two-pass rolling condition mean the last pass and the last pass, respectively. The time between final rolling passes is the time between passes from the completion of rolling of the rolling pass immediately before the final rolling pass to the start of rolling of the final rolling pass.

  About the obtained hot-rolled steel sheet, the cross section of the steel sheet thickness is observed using a scanning electron microscope, the structure of the second phase is investigated, and the average of ferrite at the 1/4 depth position of the thickness from the steel sheet surface The particle diameter D was determined by the intercept method, and the area ratio was measured by the point calculation method.

  Further, the X-ray diffraction test was performed to measure the diffraction X-ray intensity ratio of the (200), (110), and (211) random samples at the center of the plate thickness, and the (200), (110), and (211) non- A complete pole figure was obtained and ODF analysis was performed as described above to determine the diffracted X-ray intensity in each direction.

  In order to evaluate the mechanical properties of the hot-rolled steel sheet, a tensile test was performed with a JIS No. 5 tensile test piece to obtain a tensile strength TS and a total elongation EL. Moreover, the hole expansion test was done based on Japan Iron and Steel Federation standard JFS-T1001-1996, and HER (hole expansion rate) was measured. Regarding the total elongation EL and the hole expansion ratio HER, values of TS × El and TS × HER indicating a balance with the strength were obtained.

  Table 3 shows the survey results of steel structure, texture and mechanical properties. In the second phase type column, M means martensite, B means bainite, P means pearlite, and θ means grain boundary cementite.

  As shown in Table 3, in the inventive example according to the present invention, a high-strength hot-rolled steel sheet having excellent TS-EL balance and TS-HER balance and excellent ductility and hole expansibility is obtained.

  On the other hand, the comparative example whose chemical composition or manufacturing conditions are outside the scope of the present invention is inferior in TS-EL balance and / or TS-HER balance.

Claims (4)

In mass%, C: 0.005% to 0.3%, Si: 0.02% to 3.0%, Mn: 0.7% to 4.0%, P: 0.20% or less , S: 0.010% or less, sol. A multi-pass hot rolling is applied to a slab containing Al: 0.001% or more and 1.0% or less, N: 0.01% or less, and the balance comprising Fe and impurities to obtain a hot-rolled steel sheet. A method for producing a hot-rolled steel sheet,
In the multipass hot rolling, the rolling reduction of the rolling pass immediately before the final rolling pass is 22% or more and 60% or less, the rolling reduction of the final rolling pass is 10% or more and 50% or less, the rolling completion temperature is Ar ₃ or more, and It is set to 830 ° C. or more and 1100 ° C. or less, and is cooled to a temperature of 0.1 to 1.0 second (rolling completion temperature −40 ° C.) or less after completion of hot rolling, and is 0.2 seconds or more and 4 in this temperature range After being held for a time of less than 2 seconds, it is cooled to a temperature range of 750 ° C. or less and 600 ° C. or more at a cooling rate of 30 ° C./second or more, and kept in this temperature range for 2 seconds or more, and a temperature range of 600 ° C. or less And the multi-pass hot rolling satisfies the following expression (1) .
0.002 / exp (−6080 / (T + 273)) ≦ t ≦ 2.0 (1)
Where the meaning of each symbol is as follows:
t: Time (seconds) between passes from the completion of rolling of the rolling pass immediately before the final rolling pass to the start of rolling of the final rolling pass.
T: Rolling completion temperature (° C.) of the rolling pass immediately before the final rolling pass. The chemical composition is, in place of a part of the Fe, in mass%, Ti: 0.1% or less, Nb: 0.1% or less, V: 0.5% or less, Mo: 0.5% or less, and B: containing one or more compounds selected from the group consisting of 0.005% or less, the manufacturing method of the hot-rolled steel sheet according to claim 1. The method for producing a hot-rolled steel sheet according to claim 1 or 2 , wherein the chemical composition contains Cr: 2.0 mass% or less instead of a part of the Fe. The chemical composition is one type selected from the group consisting of Ca: 0.01% or less, Mg: 0.01% or less, and REM: 0.01% or less in mass%, instead of a part of the Fe. Or the manufacturing method of the hot-rolled steel plate in any one of Claims 1-3 containing 2 or more types.