Title of invention: Hot-rolled steel sheet
Technical field
[0001]
The present invention relates to a hot-rolled steel sheet. Specifically, the present invention relates to a high-strength hot-rolled steel sheet having excellent formability and low-temperature toughness.
This application claims priority based on Japanese Patent Application No. 2019-222161 filed in Japan on December 9, 2019, and the contents thereof are incorporated herein by reference.
Background technology
[0002]
The strength of steel sheets is increasing in order to ensure the collision safety of automobiles and reduce the environmental load. As the strength of the steel sheet increases, the formability decreases. Therefore, it is required to improve the formability of the high-strength (preferably 980 MPa class) steel sheet. Generally, ductility, hole expandability and bendability are used as indicators of formability, but these characteristics are in a trade-off relationship, and a steel sheet having excellent ductility, hole expandability and bendability is required. ..
[0003]
Further, when press-molding a complicated part shape such as an undercarriage part, it is particularly necessary to have excellent ductility and hole widening property. Further, in order to secure the impact characteristics, it may be necessary to have excellent low temperature toughness in addition to increasing the strength of the steel sheet.
[0004]
In Patent Document 1, a bainite phase having an area ratio of 85% or more is used as a main phase, a martensite phase or a martensite-austenite mixed phase having an area ratio of 15% or less is used as the second phase, and the balance is composed of a ferrite phase. The average particle size of the second phase is 3.0 μm or less, the average aspect ratio of the old austenite grains is 1.3 or more and 5.0 or less, and the area of ​​the recrystallized old austenite grains with respect to the unrecrystallized old austenite grains. It has a structure with a ratio of 15% or less, and the precipitate having a diameter of less than 20 nm deposited in the hot-rolled steel plate is 0.10% or less in mass%, and the tensile strength TS is 980 MPa or more. Strong hot-rolled steel sheets are disclosed.
[0005]
Patent Document 2 includes a bainite phase having an area ratio of more than 90% as a main phase, or further having one or more of a ferrite phase, a martensite phase and a retained austenite phase as a second phase. The average particle size of the bainite phase is 2.5 μm or less, and the interval of Fe-based carbides precipitated in the bainite ferrite grains in the bainite phase is 600 nm or less, and the tension is high. A high-strength hot-rolled steel plate having a strength TS of 980 MPa or more is disclosed.
[0006]
In Patent Document 3, the bainite phase is more than 92% by volume, the average interval of bainite lath is 0.60 μm or less, and the number ratio of Fe-based carbides precipitated in the grains among all Fe-based carbides is 10% or more. A high-strength hot-rolled steel sheet having an excellent mass-produced punching property, which is characterized by having a certain structure, is disclosed.
[0007]
In Patent Document 4, the Mn microsegregation in the range of 1/8 t to 3/8 t of the plate thickness satisfies the formula (1) (0.10 ≧ σ / Mn), and the average carbon content in the structure is 0. A high-strength thin steel sheet having excellent formability, which is characterized by containing 3% or more of retained austenite of 9% or more, is disclosed.
Prior art literature
Patent documents
[0008]
Patent Document 1: International Publication No. 2017/017933
Patent Document 2: International Publication No. 2015/129199
Patent Document 3: Japanese Patent Application Laid-Open No. 2014-205888
Patent Document 4: Japanese Patent Application Laid-Open No. 2007-70660
Outline of the invention
Problems to be solved by the invention
[0009]
Patent Document 1 does not consider bendability. The present inventors have found that in the high-strength hot-rolled steel sheet disclosed in Patent Document 1, it may not be possible to obtain excellent bendability, and it is necessary to further improve the hole-expandability. Furthermore, the present inventors have found that the high-strength hot-rolled steel sheet disclosed in Patent Document 1 may not be able to obtain excellent low-temperature toughness.
[0010]
Patent Document 2 does not consider hole expandability and bendability. The present inventors have found that in the high-strength hot-rolled steel sheet disclosed in Patent Document 2, it may not be possible to obtain excellent hole-spreading property and bendability.
[0011]
In Patent Document 3, in order to ensure mass production punching performance, the total of the martensite phase and the retained austenite phase is less than 1%, so that sufficient strength cannot be obtained. It was
[0012]
In Patent Document 4, air cooling is performed in cooling after hot rolling to secure 3% or more of retained austenite. The steel sheet described in Patent Document 4 is a so-called TRIP steel sheet. The present inventors have found that in the steel sheet described in Patent Document 4, it is necessary to further enhance the strength and the hole expandability.
[0013]
In view of the above circumstances, an object of the present invention is to provide a hot-rolled steel sheet having excellent strength, ductility, bendability, hole-spreading property and low-temperature toughness.
Means to solve problems
[0014]
As a result of studies by the present inventors in order to solve the above problems, the present inventors have obtained the following findings (a) to (h).
[0015]
(A) By making the metal structure a single phase, the difference in hardness between the structures can be reduced and the generation of voids at the structure interface can be suppressed, so that the hole expandability of the hot-rolled steel sheet can be improved.
[0016]
(B) When the metal structure is a bainite single phase, high strength (preferably strength of 980 MPa or more) cannot be obtained, so a desired amount of hard phase (martensite phase or martensite-austenite mixed phase) is used. By including it, it is possible to obtain a desired strength while ensuring the hole expanding property of the hot-rolled steel plate.
[0017]
(C) By reducing the average particle size of the particles having a particle size within the top 10% of all the particles in the hard phase, the hole expandability of the hot-rolled steel sheet can be further improved.
[0018]
(D) By setting the polar density in the (110) <112> orientation to 3.0 or less, the anisotropy can be reduced and the hole expandability of the hot-rolled steel sheet can be further improved.
[0019]
(E) By using bainite as the main phase (90% or more), high ductility (preferably, total elongation is 13.0% or more) can be achieved, and desired ductility can be obtained.
[0020]
(F) In order to improve low temperature toughness, it is necessary to suppress embrittlement due to precipitation strengthening, and in particular, to suppress precipitation of MC carbides (particularly TiC) during cooling after hot rolling, diameter. Increasing the average spacing of MC carbides of 20 nm or less is effective in improving low temperature toughness. By increasing the average cooling rate in cooling after hot rolling, precipitation of MC carbide (particularly TiC) can be suppressed and the average interval of MC carbide with a diameter of 20 nm or less can be increased, and the low temperature of the hot-rolled steel sheet can be increased. The toughness can be improved.
[0021]
(G) By controlling the texture in the surface layer (1/16 position of the plate thickness in the plate thickness direction from the surface to the surface), the bendability of the hot-rolled steel sheet can be further improved.
[0022]
(H) In order to obtain the above-mentioned metal structure, it is particularly effective to control the cooling conditions after hot rolling and the cooling conditions after coiling in a complex and indivisible manner.
[0023]
The gist of the present invention made based on the above findings is as follows.
(1) The hot-rolled steel sheet according to one aspect of the present invention has a chemical composition of mass%.
C: 0.040 to 0.150%,
Si: 0.50 to 1.50%,
Mn: 1.00 to 2.50%,
P: 0.100% or less,
S: 0.010% or less,
Al: 0.01-0.10%,
N: 0.0100% or less,
Ti: 0.005 to 0.150%,
B: 0.0005 to 0.0050%,
Cr: 0.10 to 1.00%,
Nb: 0 to 0.06%,
V: 0 to 0.50%,
Mo: 0 to 0.50%,
Cu: 0 to 0.50%,
Ni: 0 to 0.50%,
Sb: 0 to 0.020%,
Ca: 0 to 0.010%,
REM: 0-0.010%, and
Mg: 0 to 0.010%
Containing, the balance is iron and impurities,
In the metal structure at the 1/4 position of the plate thickness in the plate thickness direction from the surface
In terms of area ratio, the main phase is a bainite phase of 90.0 to 98.0%, the second phase is a martensite phase of 2.0 to 10.0%, or a martensite-austenite mixed phase.
The average particle size of the second phase is 1.5 μm or less,
Of all the particles in the second phase, the average particle size of the particles whose particle size is within the top 10% is 2.5 μm or less.
(110) <112> The extreme density of the orientation is 3.0 or less,
The polar density in the (110) <1-11> orientation is 3.0 or less in the metal structure at the position 1/16 of the plate thickness in the plate thickness direction from the surface to the surface.
(2) In the hot-rolled steel sheet according to (1) above, the average spacing of MC carbides having a diameter of 20 nm or less is 50 nm or more in the metal structure at a position of 1/4 of the plate thickness in the plate thickness direction from the surface. May be good.
(3) The hot-rolled steel sheet according to (1) or (2) above has a chemical composition of% by mass.
Nb: 0.005 to 0.06%,
V: 0.05 to 0.50%,
Mo: 0.05 to 0.50%,
Cu: 0.01-0.50%,
Ni: 0.01-0.50%,
Sb: 0.0002 to 0.020%,
Ca: 0.0002 to 0.010%,
REM: 0.0002 to 0.010%, and
Mg: 0.0002 to 0.010%
It may contain one or more selected from the group consisting of.
Effect of the invention
[0024]
According to the above aspect according to the present invention, it is possible to provide a hot-rolled steel sheet having excellent strength, ductility, bendability, hole-spreading property and low-temperature toughness.
Embodiment for carrying out the invention
[0025]
The chemical composition and metallographic structure of the hot-rolled steel sheet (hereinafter, may be simply referred to as a steel sheet) according to the present embodiment will be specifically described below. However, the present invention is not limited to the configuration disclosed in the present embodiment, and various modifications can be made without departing from the spirit of the present invention.
[0026]
In addition, the lower limit value and the upper limit value are included in the numerical limitation range described below with "~" in between. Numerical values ​​indicated as "less than" and "greater than" do not include the value in the numerical range. All% of the chemical composition indicate mass%.
[0027]
The hot-rolled steel sheet according to the present embodiment has a chemical composition of% by mass, C: 0.040 to 0.150%, Si: 0.50 to 1.50%, Mn: 1.00 to 2.50%. , P: 0.100% or less, S: 0.010% or less, Al: 0.01 to 0.10%, N: 0.0100% or less, Ti: 0.005 to 0.150%, B: 0 It contains 0005 to 0.0050%, Cr: 0.10 to 1.00%, and the balance: iron and impurities. Hereinafter, each element will be described.
[0028]
C: 0.040 to 0.150%
C is an element that promotes the formation of bainite by improving the strength of hot-rolled steel sheets and improving hardenability. In order to obtain this effect, the C content is 0.040% or more. Preferably, the C content is 0.050% or more and 0.060% or more.
On the other hand, when the C content exceeds 0.150%, it becomes difficult to control the formation of bainite, and a large amount of martensite phase or martensite-austenite mixed phase is formed, and the ductility and hole expandability of the hot-rolled steel sheet Both or one of them decreases. Therefore, the C content is set to 0.150% or less. The C content is preferably 0.140% or less, 0.120% or less, and 0.100% or less.
[0029]
Si: 0.50 to 1.50%
Si is an element that contributes to solid solution strengthening and contributes to improving the strength of hot-rolled steel sheets. Further, Si is an element that suppresses the formation of carbides in steel. By suppressing the formation of carbides during bainite transformation, a fine martensite phase or a martensite-austenite mixed phase is formed at the lath interface of the bainite phase. Since the martensite phase or the martensite-austenite mixed phase present in the bainite phase is fine, it does not deteriorate the hole expandability of the hot-rolled steel sheet. In order to obtain the above effect due to the Si content, the Si content is 0.50% or more. Preferably, the Si content is 0.55% or more, 0.60% or more, and 0.65% or more.
On the other hand, Si is also an element that lowers toughness, and the Si content is 1.50%. If it exceeds, the toughness of the hot-rolled steel sheet decreases. Therefore, the Si content is 1.50% or less. Preferably, the Si content is 1.30% or less, 1.20% or less, and 1.00% or less.
[0030]
Mn: 1.00 to 2.50%
Mn dissolves in the steel and contributes to the increase in the strength of the hot-rolled steel sheet, and promotes the formation of bainite by improving the hardenability, improving the hole-expanding property of the hot-rolled steel sheet. In order to obtain such an effect, the Mn content is set to 1.00% or more. Preferably, the Mn content is 1.30% or more and 1.50% or more.
On the other hand, if the Mn content exceeds 2.50%, it becomes difficult to control the formation of bainite, and the martensite phase or the martensite-austenite mixed phase increases, resulting in both ductility and hole expansion of the hot-rolled steel sheet, or any of them. One goes down. Therefore, the Mn content is set to 2.50% or less. Preferably, the Mn content is 2.00% or less and 1.95% or less.
[0031]
P: 0.100% or less
P is an element that dissolves in steel and contributes to increasing the strength of hot-rolled steel sheets. However, P is also an element that segregates at the grain boundaries, particularly the former austenite grain boundaries, and promotes the grain boundary fracture due to the grain boundary segregation, thereby causing a decrease in ductility, bendability, and hole expanding property of the hot-rolled steel sheet. The P content is preferably as low as possible, but a P content of up to 0.100% is acceptable. Therefore, the P content is set to 0.100% or less. Preferably, the P content is 0.090% or less and 0.080% or less.
The P content is preferably 0%, but if it is reduced to less than 0.0001%, the manufacturing cost increases, so the P content may be 0.0001% or more. Preferably, the P content is 0.001% or more and 0.010% or more.
[0032]
S: 0.010% or less
S is an element that adversely affects weldability and manufacturability during casting and hot rolling. S combines with Mn to form coarse MnS. This MnS deteriorates the bendability and hole widening property of the hot-rolled steel sheet, and promotes the occurrence of delayed fracture. The S content is preferably as low as possible, but the content of S up to 0.010% is acceptable. Therefore, the S content is 0.010% or less. Preferably, the S content is 0.008% or less and 0.007% or less.
The S content is preferably 0%, but if it is reduced to less than 0.0001%, the manufacturing cost increases and it is economically disadvantageous. Therefore, the S content may be 0.0001% or more. Preferably, the S content is 0.001% or more.
[0033]
Al: 0.01-0.10%
Al is an element that acts as a deoxidizing agent and is effective in improving the cleanliness of steel. In order to obtain this effect, the Al content is 0.01% or more. Preferably, the Al content is 0.02% or more.
On the other hand, if Al is excessively contained, the oxide-based inclusions increase, and the hole-expanding property of the hot-rolled steel sheet decreases. Therefore, the Al content is set to 0.10% or less. Preferably, the Al content is 0.08% or less and 0.06% or less.
[0034]
N: 0.0100% or less
N is an element that forms a coarse nitride in steel. This nitride deteriorates the bendability and hole widening property of the hot-rolled steel sheet and also deteriorates the delayed fracture resistance. Therefore, the N content is 0.0100% or less. Preferably, the N content is 0.0080% or less, 0.0060% or less, 0.0050% or less.
Since reducing the N content to less than 0.0001% causes a significant increase in manufacturing cost, the N content may be 0.0001% or more. Preferably, the N content is 0.0005% or more and 0.0010% or more.
[0035]
Ti: 0.005 to 0.150%
Ti is an element that forms a nitride in the austenite phase high temperature region (high temperature region in the austenite phase region and higher temperature region than the austenite phase region (casting stage)). By containing Ti, precipitation of BN is suppressed, and B is in a solid solution state, so that the hardenability required for the formation of bainite can be obtained. As a result, the strength and hole expandability of the hot-rolled steel sheet can be improved. In addition, Ti forms carbides in the steel during hot rolling to suppress recrystallization of old austenite grains. In order to obtain these effects, the Ti content is 0.005% or more. Preferably, the Ti content is 0.020% or more, 0.030% or more, 0.050% or more, and 0.080% or more.
On the other hand, when the Ti content exceeds 0.150%, the old austenite grains are less likely to recrystallize, and the rolled texture develops, so that the hole expansion property of the hot-rolled steel sheet deteriorates. Therefore, the Ti content is set to 0.150% or less. Preferably, the Ti content is 0.120% or less.
[0036]
B: 0.0005 to 0.0050%
B is an element that segregates into the old austenite grain boundaries, suppresses the formation and growth of ferrite, and contributes to the improvement of the strength and hole expandability of hot-rolled steel sheets. In order to obtain these effects, the B content is 0.0005% or more. Preferably, the B content is 0.0007% or more and 0.0010% or more.
On the other hand, even if B is contained in excess of 0.0050%, the above effect is saturated. Therefore, the B content is set to 0.0050% or less. Preferably, the B content is 0.0030% or less and 0.0025% or less.
[0037]
Cr: 0.10 to 1.00%
Cr is an element that forms carbides in steel and contributes to high strength of hot-rolled steel sheets, promotes the formation of bainite by improving hardenability, and promotes the precipitation of Fe-based carbides in bainite grains. .. In order to obtain these effects, the Cr content is set to 0.10% or more. Preferably, the Cr content is 0.30% or more, 0.40% or more, 0.50% or more.
On the other hand, when the Cr content exceeds 1.00%, a martensite phase or a martensite-austenite mixed phase is likely to be formed, and both the hole-spreading property and the ductility of the hot-rolled steel sheet, or one of them, is lowered. Therefore, the Cr content is set to 1.00% or less. Preferably, the Cr content is 0.80% or less and 0.70% or less.
[0038]
The balance of the chemical composition of the hot-rolled steel sheet according to the present embodiment may be Fe and impurities. In the present embodiment, the impurities mean those mixed from ore as a raw material, scrap, manufacturing environment, etc., or those permitted within a range that does not adversely affect the characteristics of the hot-rolled steel sheet according to the present embodiment. do.
[0039]
The hot-rolled steel sheet according to this embodiment may contain the following elements as optional elements instead of a part of Fe. The lower limit of the content when the following optional elements are not contained is 0%. Hereinafter, each arbitrary element will be described in detail.
[0040]
Nb: 0 to 0.06%
Nb is an element that has the effect of forming carbides during hot rolling and suppressing the recrystallization of austenite, and contributes to improving the strength of hot-rolled steel sheets. In order to surely obtain this effect, the Nb content is preferably 0.005% or more. The Nb content is more preferably 0.015% or more.
On the other hand, if the Nb content exceeds 0.06%, the recrystallization temperature of the old austenite grains becomes too high, the texture develops, and the hole expansion property of the hot-rolled steel sheet may deteriorate. Therefore, the Nb content is 0.06% or less. Preferably, the Nb content is 0.04% or less.
[0041]
V: 0 to 0.50%
V is an element that has the effect of forming carbonitride during hot rolling and suppressing the recrystallization of austenite, and contributes to improving the strength of the hot-rolled steel sheet. In order to surely obtain this effect, the V content is preferably 0.05% or more. The V content is more preferably 0.10% or more.
On the other hand, when the V content exceeds 0.50%, the recrystallization temperature of the old austenite grains becomes high, and the recrystallization temperature of the austenite grains after the finish rolling is high, so that the texture develops and the hot rolling occurs. The hole expandability of the steel plate may decrease. Therefore, the V content is set to 0.50% or less. Preferably, the V content is 0.25% or less.
[0042]
Mo: 0 to 0.50%
Mo is an element that promotes the formation of a bainite phase by improving hardenability and contributes to improving the strength and hole expansion of hot-rolled steel sheets. In order to surely obtain this effect, the Mo content is preferably 0.05% or more. The Mo content is more preferably 0.10% or more.
On the other hand, when the Mo content exceeds 0.50%, the martensite phase or the martensite-austenite mixed phase is likely to be formed, and the ductility and / or the expandability of the hot-rolled steel sheet are deteriorated. There is. Therefore, the Mo content is set to 0.50% or less. Preferably, the Mo content is 0.30% or less.
[0043]
Cu: 0 to 0.50%
Cu is an element that dissolves in steel and contributes to increasing the strength of hot-rolled steel sheets. Further, Cu is an element that promotes the formation of a bainite phase by improving the hardenability and contributes to the improvement of the strength and the hole expanding property of the hot-rolled steel sheet. In order to surely obtain these effects, the Cu content is preferably 0.01% or more. The Cu content is more preferably 0.02% or more.
On the other hand, if the Cu content exceeds 0.50%, the surface texture of the hot-rolled steel sheet may deteriorate. Therefore, the Cu content is set to 0.50% or less. Preferably, the Cu content is 0.20% or less.
[0044]
Ni: 0 to 0.50%
Ni is an element that dissolves in steel and contributes to increasing the strength of hot-rolled steel sheets. Further, Ni is an element that promotes the formation of a bainite phase by improving the hardenability and contributes to the improvement of the strength and the hole expanding property of the hot-rolled steel sheet. In order to surely obtain these effects, the Ni content is preferably 0.01% or more. The Ni content is more preferably 0.02% or more.
On the other hand, when the Ni content exceeds 0.50%, a martensite phase or a martensite-austenite mixed phase is likely to be formed, and both the bendability and the hole-expanding property of the hot-rolled steel sheet are lowered. In some cases. Therefore, the Ni content is set to 0.50% or less. Preferably, the Ni content is 0.20% or less.
[0045]
Sb: 0 to 0.020%
Sb has the effect of suppressing nitriding of the slab surface at the slab heating stage. By containing Sb, precipitation of BN on the surface layer of the slab is suppressed. In order to surely obtain this effect, the Sb content is preferably 0.0002% or more. The Sb content is more preferably 0.001% or more.
On the other hand, even if Sb is contained in excess of 0.020%, the above effect is saturated, so the Sb content should be 0.020% or less.
[0046]
Ca: 0 to 0.010%
Ca is an element that controls the shape of sulfide-based inclusions and improves the ductility and hole expandability of hot-rolled steel sheets. In order to surely obtain this effect, the Ca content is preferably 0.0002% or more. The Ca content is more preferably 0.001% or more.
On the other hand, if the Ca content exceeds 0.010%, surface defects of the hot-rolled steel sheet may occur and the productivity may decrease. Therefore, the Ca content is 0.010% or less. Preferably, the Ca content is 0.008% or less.
[0047]
REM: 0 to 0.010%
Like Ca, REM is an element that controls the shape of sulfide-based inclusions and improves the ductility and hole-expandability of hot-rolled steel sheets. In order to surely obtain this effect, the REM content is preferably 0.0002% or more. The REM content is more preferably 0.001% or more.
On the other hand, if the REM content exceeds 0.010%, the cleanliness of the steel deteriorates, and both the hole-spreading property and the bendability of the hot-rolled steel sheet, or one of them, deteriorates. Therefore, the REM content is 0.010% or less. Preferably, the REM content is 0.008% or less.
[0048]
Here, REM refers to a total of 17 elements composed of Sc, Y and lanthanoids, and the content of the above REM refers to the total content of these elements. In the case of lanthanoids, industrially Added in the form of Schmetal.
[0049]
Mg: 0 to 0.010%
Mg is an element that can control the morphology of sulfide by containing it in a small amount. In order to surely obtain this effect, the Mg content is preferably 0.0002% or more. The Mg content is more preferably 0.0005% or more.
On the other hand, if the Mg content exceeds 0.010%, the formation of coarse inclusions causes a decrease in cold formability. Therefore, the Mg content is set to 0.010% or less. Preferably, the Mg content is 0.008% or less.
[0050]
The chemical composition of the hot-rolled steel sheet may be measured by a general analysis method. For example, ICP-AES (Inductively Coupled Plasma-Atomic Emission Spectrum) may be used for measurement. In addition, C and S may be measured by using the combustion-infrared absorption method, and N may be measured by using the inert gas melting-thermal conductivity method.
[0051]
Next, the metal structure of the hot-rolled steel sheet according to this embodiment will be described.
The hot-rolled steel plate according to the present embodiment has a baynite phase having a main phase of 90.0 to 98.0% in terms of area ratio in a metal structure at a position of 1/4 of the plate thickness in the plate thickness direction from the surface. The two phases are a martensite phase of 2.0 to 10.0% or a martensite-austenite mixed phase, the average particle size of the second phase is 1.5 μm or less, and all the particles of the second phase. Among them, the average particle size of the particles whose particle size is within the top 10% is 2.5 μm or less, the extreme density in the (110) <112> orientation is 3.0 or less, and the surface to the surface is said to be. In the metal structure at 1/16 of the plate thickness in the plate thickness direction, the polar density in the (110) <1-11> orientation is 3.0 or less.
[0052]
In this embodiment, the types of the main phase and the second phase at the position 1/4 of the plate thickness in the plate thickness direction from the surface, the average particle size of the second phase, and the extreme density in the (110) <112> direction are determined. This is specified because the metallographic structure at this position represents the typical metallic structure of the steel sheet. Further, the position defining the metal structure is preferably the center position in the plate width direction.
Below, each regulation will be explained.
[0053]
Bainite phase (main phase): 90.0-98.0%
The hot-rolled steel sheet according to this embodiment has a bainite phase as the main phase. The area ratio of the bainite phase, which is the main phase, is 90.0% or more. In the present embodiment, the main phase means that the area ratio is 90.0% or more.
The bainite phase means a lath-shaped bainitic ferrite and a structure having Fe-based carbides between and / or inside the bainitic ferrite. Unlike polygonal ferrite, bainitic ferrite has a lath-like shape and has a relatively high dislocation density inside, so it can be easily distinguished from other structures using SEM or TEM.
[0054]
In order to achieve high strength (preferably tensile strength of 980 MPa or more) and enhance hole expandability, it is necessary to use the bainite phase as the main phase. When the area ratio of the bainite phase is less than 90.0%, the decrease in hole widening property due to the difference in hardness from the second phase becomes remarkable. Therefore, the area ratio of the bainite phase is 90.0% or more. Preferably, it is 92.0% or more and 93.0% or more.
On the other hand, if the area ratio of the bainite phase exceeds 98.0%, the strength may not be high (preferably the tensile strength is 980 MPa or more), so the area ratio of the bainite phase is 98.0% or less. Preferably, it is 96.0% or less and 95.0% or less.
[0055]
Martensite phase or martensite-austenite mixed phase (Phase 2): 2.0-10.0%
The hot-rolled steel sheet according to this embodiment has a martensite phase or a martensite-austenite mixed phase as the second phase. The martensite phase is a collection of lath-shaped crystal grains, and means a structure in which iron carbides have two or more elongation directions inside the crystal grains. The mixed phase of martensite-austenite is also called striped martensite (MA: Martensite-Austenite constituent) and means a structure consisting of both martensite and retained austenite.
[0056]
The higher the area ratio of the second phase, the better the tensile strength of the hot-rolled steel sheet. If the area ratio of the second phase is less than 2.0%, the desired tensile strength cannot be obtained. Therefore, the area ratio of the second phase is set to 2.0% or more. Preferably, it is 3.0% or more, 4.0% or more, and 5.0% or more.
On the other hand, if the area ratio of the second phase exceeds 10.0%, the desired hole expandability and ductility cannot be obtained. Therefore, the area ratio of the second phase is set to 10.0% or less. Preferably, it is 9.0% or less, 8.0% or less, and 7.0% or less.
[0057]
The hot-rolled steel sheet according to the present embodiment may contain 5% or less ferrite in addition to the bainite phase and the second phase. However, since it is not always necessary to include ferrite, the area ratio of ferrite may be 0%.
[0058]
The method of measuring the area ratio of the metal structure will be described below.
First, from the hot-rolled steel sheet, it is a plate thickness cross section perpendicular to the rolling direction, and is a 1/4 position of the plate thickness in the plate thickness direction from the surface (1/8 position in the plate thickness direction from the surface to 3 in the plate thickness direction from the surface). The test piece is collected so that the region at the / 8 position, that is, the region starting from the 1/8 position in the plate thickness direction from the surface and ending at the 3/8 position in the plate thickness direction from the surface) can be observed. The cross section of the test piece is mirror-polished, corroded with a repera corrosive solution, and then the structure is observed using an optical microscope.
[0059]
The second phase appears as a white part by the repera corrosive liquid, and the other structure (bainite phase) is stained, so that it can be easily distinguished. The area ratio of the white part is calculated by binarizing the white part (bright part) and the other areas. For example, by binarizing the white portion and the other region using image analysis software such as Image-J, the area ratio of the white portion and the area ratio of the other region can be obtained. The observation field of view shall be three or more, and the area of ​​each field of view shall be 300 μm × 400 μm or more.
[0060]
The area ratio of the second phase is obtained by calculating the average value of the area ratio of the white part measured in a plurality of visual fields. The area ratio of the bainite phase is obtained by calculating the average value of the area ratio of the region other than the white portion measured in the plurality of visual fields.
[0061]
If a ferrite phase is present in the metallographic structure, the ferrite phase is dyed white in the same manner as the bainite phase. However, the bainite phase and the ferrite phase can be easily distinguished by observing their morphology. When a ferrite phase is present, the area ratio of the bainite phase is obtained by subtracting the area ratio of the white portion determined to be the ferrite phase from the area ratio of the region other than the white portion. The bainite phase is observed as lath-shaped crystal grains, and the ferrite phase is observed as massive crystal grains containing no lath inside.
[0062]
Average particle size of the second phase: 1.5 μm or less
When the average particle size of the second phase becomes large, voids are likely to occur, and the hole expanding property of the hot-rolled steel sheet decreases. In order to suppress the generation of voids and improve the hole expanding property, it is preferable that the average particle size of the second phase is small. If the average particle size of the second phase is more than 1.5 μm, the desired hole-expanding property cannot be obtained. Therefore, the average particle size of the second phase is set to 1.5 μm or less. It is preferably 1.4 μm or less, and more preferably 1.3 μm or less.
Since it is technically difficult to make the average particle size of the second phase less than 0.1 μm, the average particle size of the second phase may be 0.1 μm or more.
[0063]
Of all the particles in the second phase, the average particle size of the particles whose particle size is within the top 10%: 2.5 μm or less
When the average particle size of the particles having a particle size within the top 10% of all the particles in the second phase is large, the starting point of void generation increases, so that the hole expansion property of the hot-rolled steel sheet decreases. Therefore, among all the particles in the second phase, the smaller the average particle size of the particles whose particle size is within the top 10% is preferable. In order to obtain the desired hole-spreading property, the average particle size of the particles having a particle size within the upper 10% among all the particles of the second phase is 2.5 μm or less. It is preferably 2.3 μm or less, more preferably 2.2 μm or less, and even more preferably 2.0 μm or less.
[0064]
The lower limit of the average particle size of the particles whose particle size is within the upper 10% is not particularly limited, but may be 1.5 μm or more and 1.7 μm or more.
[0065]
The method for measuring the average particle size of the second phase and the method for measuring the average particle size of the particles having a particle size within the top 10% of all the particles of the second phase will be described below.
First, from the hot-rolled steel sheet, it is a plate thickness cross section perpendicular to the rolling direction, and is a 1/4 position of the plate thickness in the plate thickness direction from the surface (1/8 position in the plate thickness direction from the surface to 3 in the plate thickness direction from the surface). The test piece is collected so that the region at the / 8 position, that is, the region starting from the 1/8 position in the plate thickness direction from the surface and ending at the 3/8 position in the plate thickness direction from the surface) can be observed. The cross section of the test piece is mirror-polished, corroded with a repera corrosive solution, and then the structure is observed using an optical microscope. Using image analysis software (Image-J), a binarized image of the white part and the other areas is created. After that, particle analysis is performed based on the binarized image, and the area of ​​each particle is calculated. The average particle size of the second phase is obtained by calculating the average value of the average particle size obtained in each field of view with three or more observation fields.
[0066]
Next, for each field of view, the average particle size of the particles having a particle size within the top 10% of all the particles of the second phase is calculated, and the average value of the whole field is calculated. The average particle size of the particles having a particle size within the top 10% of all the particles of the two phases is obtained.
[0067]
The average particle size of the particles whose particle size is within the top 10% is, for example, 100 particles of the second phase observed in one field of view, and the particles having the smallest particle size are 1. When numbered 2, 3 ... 99, 100, it means the average value of the particle size of the 91st to 100th particles.
[0068]
The second phase, which has an area of ​​less than 0.5 μm 2, does not affect the hole-spreading property of the hot-rolled steel plate. Of these, the measurement of the average particle size of the particles whose particle size is within the top 10%) is excluded from the measurement target.
[0069]
(110) <112> Directional extreme density: 3.0 or less
The extreme density of the (110) <112> orientation in the metal structure at the position of 1/4 of the plate thickness in the plate thickness direction from the surface is an index for evaluating the development condition of the rolled texture. The more the (110) <112> orientation polar density develops, that is, the larger the (110) <112> orientation polar density, the greater the anisotropy of the structure and the lower the hole expandability of the hot-rolled steel sheet. If the polar density in the (110) <112> orientation exceeds 3.0, the hole-expanding property deteriorates, so the polar density in the (110) <112> orientation is set to 3.0 or less. It is preferably 2.8 or less, 2.5 or less, and 2.3 or less.
[0070]
The smaller the extreme density in the (110) <112> orientation, the more random the structure is and the better the hole expanding property of the hot-rolled steel sheet. Therefore, the smaller the extreme density in the (110) <112> orientation is, the more preferable. (110) The extreme density of the <112> orientation is 1.0 when it does not have an texture, so the lower limit may be 1.0.
[0071]
The method of measuring the extreme density in the (110) <112> orientation will be described below.
(110) The extreme density of the <112> orientation was measured by the EBSD (Electron Backscattering Diffraction) method using a device combining a scanning electron microscope and an EBSD analyzer and OIM Analysis (registered trademark) manufactured by AMETEK. The orientation data can be obtained from a crystal orientation distribution function (ODF: Origination Diffraction Function) that displays a three-dimensional aggregate structure calculated by using a spherical harmonic function. The measurement range is 1/4 position of the plate thickness in the plate thickness direction from the surface (1/8 position in the plate thickness direction from the surface to 3/8 position in the plate thickness direction from the surface, that is, 1 in the plate thickness direction from the surface. Starting from the / 8 position, 3/8 in the plate thickness direction from the surface A region whose end point is the position), and a region of 400 μm in the rolling direction. It is preferable to set the measurement pitch so that the measurement pitch is 0.5 μm / step or less.
[0072]
Extreme density of (110) <1-11> orientation in the metal structure at 1/16 of the plate thickness in the plate thickness direction from the surface to the surface: 3.0 or less
(110) <1 in the metal structure at the 1/16 position of the plate thickness in the plate thickness direction from the surface to the surface (the region starting from the surface and ending at the position of 1/16 of the plate thickness in the plate thickness direction from the surface). The extreme density of -11> orientation is an index for evaluating the development of the shear texture in the surface layer region of the hot-rolled steel sheet. When the polar density in the (110) <1-11> orientation develops at this position, that is, when the polar density in the (110) <1-11> orientation increases, the anisotropy of the structure increases and the hot-rolled steel sheet bends. The sex is reduced. If the polar density in the (110) <1-11> orientation exceeds 3.0, the bendability of the hot-rolled steel sheet decreases, so the polar density in the (110) <1-11> orientation shall be 3.0 or less. .. It is preferably 2.8 or less, 2.5 or less, and 2.2 or less.
[0073]
The smaller the extreme density in the (110) <1-11> orientation, the more random the structure is and the better the bendability of the hot-rolled steel sheet. Therefore, the smaller the extreme density in the (110) <1-11> orientation is, the more preferable. (110) The extreme density of the <1-11> orientation is 1.0 when it does not have an texture, so the lower limit may be 1.0.
[0074]
The method of measuring the extreme density in the (110) <1-11> orientation will be described below.
(110) The extreme density of the <1-11> orientation is determined by the EBSD (Electron Backscattering Diffraction) method using a device combining a scanning electron microscope and an EBSD analyzer and OIM Analysis (registered trademark) manufactured by AMETEK. The measured orientation data can be obtained from a crystal orientation distribution function (ODF: Origination Diffraction Function) that displays a three-dimensional texture calculated by calculating using a spherical harmonic function. The measurement range is the region from the surface to the plate thickness direction at 1/16 of the plate thickness (the region starting from the surface and the end point from the surface to the plate thickness direction at 1/16 of the plate thickness) and rolling. In the direction, a region of 400 μm or more is evaluated. It is preferable to set the measurement pitch so that the measurement pitch is 0.5 μm / step or less.
[0075]
Average spacing of MC carbides with a diameter of 20 nm or less in the metal structure at 1/4 of the plate thickness in the plate thickness direction from the surface: 50 nm or more
The hot-rolled steel sheet according to the present embodiment has a region of 1/4 position of the plate thickness in the plate thickness direction from the surface (1/8 position in the plate thickness direction from the surface to 3/8 position in the plate thickness direction from the surface, that is, the surface. In the metallographic structure (a region starting from the 1/8 position in the plate thickness direction and ending at the 3/8 position in the plate thickness direction from the surface), the average spacing of MC carbides having a diameter of 20 nm or less is 50 nm or more. May be good.
[0076]
In the present embodiment, the MC carbide means a metal carbide such as TiC and VC.
[0077]
The average spacing of MC carbides with a diameter of 20 nm or less can be adjusted, in particular by more strictly controlling the cooling rate after the completion of hot rolling. Specifically, by setting the average cooling rate in cooling after hot rolling to 90 ° C./s or more, MC having a diameter of 20 nm or less in the metal structure at a position 1/4 of the plate thickness in the plate thickness direction from the surface. The average spacing of carbides can be 50 nm or more.
By setting the average interval of MC carbides with a diameter of 20 nm or less to 50 nm or more, the low temperature toughness of the hot-rolled steel sheet can be further improved.
[0078]
The method for measuring the average interval of MC carbides having a diameter of 20 nm or less will be described below.
First, from the hot-rolled steel plate, the plate thickness cross section is parallel to the rolling direction of the hot-rolled steel plate, and the plate thickness is 1/4 of the plate thickness in the plate thickness direction from the surface (1/8 position in the plate thickness direction from the surface to the plate from the surface). The test piece is collected so that the metallographic structure in the region at the 3/8 position in the thickness direction can be observed. The cross section is electrolytically etched, and 10 fields of view are photographed with a transmission electron microscope (TEM) at a magnification of 20000 times. For the precipitates having a diameter of 20 nm or less in the photographed photograph, the closest contact distance is obtained by image analysis and the average value of these is calculated to obtain the average interval of MC carbides having a diameter of 20 nm or less.
[0079]
MC carbides with a precipitate diameter of less than 5 nm do not affect the improvement of low temperature toughness and are difficult to observe, so they are excluded from the above-mentioned observation targets. Further, the MC carbide to be observed refers to metal carbides such as TiC and VC.
[0080] [0080]
Next, a preferable manufacturing method of the hot-rolled steel sheet according to the present embodiment will be described.
A preferred method for manufacturing a hot-rolled steel sheet according to this embodiment includes the following steps.
A heating step that heats a slab having a predetermined chemical composition to 1100 ° C or higher and lower than 1350 ° C.
A hot rolling process in which hot rolling is performed so that the hot rolling start temperature is 1050 to 1200 ° C and the finish rolling completion temperature is more than 950 ° C and 1050 ° C or lower.
A cooling step in which cooling is started within 1.0 second after the completion of the hot rolling and is cooled to a cooling stop temperature of 400 to 500 ° C. at an average cooling rate of 30 to 150 ° C./s.
A winding process in which winding is performed in a temperature range of 400 to 500 ° C after cooling to the cooling shutdown temperature.
After the winding, a coil cooling step of cooling to a temperature range of 50 ° C or lower at an average cooling rate of more than 25 ° C / h and 100 ° C / h or less.
Below, each process will be explained in detail.
[0081]
Heating process
In the heating step, the slab having the above-mentioned chemical composition is heated to 1100 ° C or higher and lower than 1350 ° C. Since the coarse precipitates present in the slab stage cause cracks during rolling and deterioration of material properties, it is preferable to heat the steel material before hot rolling to dissolve the coarse carbides in a solid solution. Therefore, the heating temperature is preferably 1100 ° C. or higher. More preferably, it is 1150 ° C. or higher. On the other hand, even if the heating temperature becomes too high, the yield decreases due to the large amount of scale generated, so the heating temperature is preferably 1350 ° C. or lower. More preferably, it is 1300 ° C. or lower.
[0082]
The slab to be heated is preferably produced by continuous casting from the viewpoint of manufacturing cost, but may be produced by another casting method (for example, ingot forming method).
[0083]
Hot rolling process
The temperature of the steel sheet in hot rolling affects the precipitation of carbides and nitrides of Ti and Nb in austenite. If the hot rolling start temperature is less than 1050 ° C., precipitation starts before the start of hot rolling and the precipitate becomes coarse, so that the precipitate cannot be controlled to a desired form and a homogeneous slab can be obtained. May not be possible. Therefore, the hot rolling start temperature is preferably 1050 ° C. or higher. More preferably, it is 1070 ° C. or higher.
On the other hand, when the hot rolling start temperature exceeds 1200 ° C., it becomes difficult to start the precipitation during hot rolling, and the precipitate may not be controlled to a desired form. Therefore, the hot rolling start temperature is preferably 1200 ° C. or lower. More preferably, it is 1170 ° C. or lower.
[0084]
Finish rolling completion temperature is a factor that affects the texture of old austenite grains. When the finish rolling completion temperature is 950 ° C. or lower, the texture of the old austenite grains may develop and the anisotropy of the steel material characteristics may increase. Therefore, the finish rolling completion temperature is preferably over 950 ° C. More preferably, it is 960 ° C. or higher.
On the other hand, if the finish rolling completion temperature is too high, the coarsening of the old austenite grains becomes remarkable, and the second phase becomes coarse, so that the desired hole expanding property may not be obtained. Therefore, the finish rolling completion temperature is preferably 1050 ° C. or lower. More preferably, it is 1020 ° C. or lower.
[0085]
Before hot rolling, the slab may be roughly rolled to form a rough bar and then hot rolled.
[0086]
Also, before finish rolling, the scale formed on the surface of the steel sheet is usually removed (descaling). In the present embodiment, descaling may be performed by a conventional method, for example, so that the collision pressure of the injected water is less than 3.0 MPa. If high-pressure descaling in which the collision pressure of the jetted water is 3.0 MPa or more is performed, the texture of the surface layer may not be preferably controlled.
[0087]
Further, in finish rolling, in order to preferably control the texture, the total rolling reduction of the rolling reduction in the final pass and the rolling reduction one pass before the final pass is preferably less than 30%.
[0088]
Cooling process
In the present embodiment, in order to obtain a desired metallographic structure, it is possible to control the cooling conditions after hot rolling in the cooling step and the cooling conditions after winding into a coil in the coil cooling step in a complex and indivisible manner. It is effective.
[0089]
In the above-mentioned hot rolling, since the rolling is performed at a relatively high temperature, the coarsening of the old austenite grains tends to proceed. Therefore, it is necessary to start cooling in a short time after the completion of finish rolling to suppress the coarsening of the old austenite grains. If the time from the completion of finish rolling to the start of cooling is long, the old austenite particles become coarse, and the size of the particle size is within the top 10% of the desired average particle size of the second phase and the total particles of the second phase. It may not be possible to obtain the average particle size of the particles. The earlier the cooling start time is, the better, and in the present embodiment, it is preferable to start cooling within 1.0 second after the completion of hot rolling. It is more preferably within 0.5 seconds, and more preferably 0 seconds.
[0090]
The cooling start time here means the elapsed time from the completion of finish rolling to the start of cooling (cooling having an average cooling rate of 30 to 150 ° C./s) described later.
[0091]
It is preferable that the cooling after hot rolling is performed at an average cooling rate of 30 to 150 ° C./s to a cooling shutdown temperature of 400 to 500 ° C. If the average cooling rate is too slow, ferrite may precipitate, making it impossible to obtain the desired amount of bainite phase, and it may not be possible to obtain the desired tensile strength and / or hole expandability. Further, when the average cooling rate is slow, the carbide forming elements Ti, V, Nb and the like may be bonded to carbon to form a large amount of precipitates, and the low temperature toughness of the hot-rolled steel sheet may decrease. Therefore, the average cooling rate of cooling after the completion of hot rolling is preferably 30 ° C./s or more.
[0092]
In order to further suppress the amount of MC carbide, it is necessary to increase the average cooling rate. In the present embodiment, in order to make the average spacing of MC carbides having a diameter of 20 nm or less 50 nm or more in the metal structure at a position 1/4 of the plate thickness in the plate thickness direction from the surface, the average cooling rate in cooling after hot rolling May be 90 ° C./s or higher.
[0093]
On the other hand, if the average cooling rate after the completion of hot rolling is too fast, the surface temperature becomes too low and martensite is likely to be generated on the surface of the steel sheet, so that the desired ductility and / or bendability can be obtained. It may not be possible. Therefore, the average cooling rate of cooling after the completion of hot rolling is preferably 150 ° C./s or less. More preferably, it is 120 ° C./s or less, and more preferably 100 ° C./s or less.
[0094]
The average cooling rate in the present embodiment is a value obtained by dividing the temperature difference between the start point and the end point in the set range by the elapsed time from the start point to the end point.
If the cooling stop temperature is outside the temperature range of 400 to 500 ° C., the winding step described later cannot be performed in the desired temperature range. Further, in order to obtain a desired metal structure, it is desirable not to perform air cooling in order to suppress ferrite transformation during cooling in cooling after hot rolling.
[0095]
Winding process
After stopping the cooling after hot rolling, the take-up temperature is 400 to 500 ° C. in order to suppress the ferrite transformation and promote the bainite transformation, and to control the distribution, morphology, and fraction of the second phase. It is preferable to perform winding so as to be in the temperature range of. When the winding temperature is less than 400 ° C., martensitic transformation is likely to occur, so that the area ratio of the martensite phase increases and the desired ductility is obtained.It may not be possible. Therefore, the winding temperature is preferably 400 ° C. or higher. More preferably, it is 420 ° C. or higher.
[0096]
On the other hand, when the winding temperature exceeds 500 ° C., carbide-forming elements such as Ti, Nb and V combine with carbon to form fine MC carbides, which may deteriorate the low-temperature toughness of the hot-rolled steel sheet. Therefore, the winding temperature is preferably 500 ° C. or lower. More preferably, it is 480 ° C. or lower.
[0097]
Coil cooling process
The cooling rate after winding into a coil affects the microstructural fraction of the second phase. In the coil cooling step, carbon enrichment to untransformed austenite is performed. Untransformed austenite is the tissue before transformation to the second phase (martensite phase or martensite-austenite mixed phase). When the product is wound into a coil and then cooled at an average cooling rate of 25 ° C./h or less, untransformed austenite may be decomposed and a desired amount of the second phase may not be obtained. In addition, carbon enrichment to untransformed austenite progresses excessively, the hardness of the second phase becomes excessive, and the difference in hardness between the structures of the main phase and the second phase becomes large, so that the holes in the hot-rolled steel sheet are formed. Spreadability may decrease. Therefore, the average cooling rate is preferably more than 25 ° C./h. More preferably, it is 30 ° C./or.
[0098]
On the other hand, if the average cooling rate is too fast, there may be a difference in the cooling rate between the inside and outside of the coil, and uniform cooling may not be possible. Therefore, the average cooling rate is preferably 100 ° C./h or less. It is more preferably 80 ° C./h or less, and even more preferably 60 ° C./h or less.
[0099]
It is preferable that the cooling after winding into a coil is performed up to a temperature range of 50 ° C. or lower at the above-mentioned average cooling rate.
Example
[0100]
Next, an embodiment of the present invention will be described. The conditions in the examples are one condition example adopted for confirming the feasibility and effect of the present invention. The present invention is not limited to this one-condition example. The present invention may adopt various conditions as long as the gist of the present invention is not deviated and the object of the present invention is achieved.
[0101]
Steel Nos. in Tables 1 and 2. Steels having the chemical compositions shown in 1-42 were melted and continuously cast to produce slabs having a thickness of 240 to 300 mm. Using the obtained slab, a hot-rolled steel sheet was obtained under the production conditions shown in Tables 3 and 4. The "average cooling rate between FT and CT" in Tables 3 and 4 indicates the average cooling rate from the start of cooling after hot rolling to the winding (stopping of cooling). Further, before finish rolling, descaling was performed by a conventional method (collision pressure of injected water is less than 3.0 MPa). No. Only for 41, descaling was performed so that the collision pressure of the injected water was 3.5 MPa.
[0102]
[table 1]

[0103]
[Table 2]

[0104]
[Table 3]

[0105]
[Table 4]

[0106]
With respect to the obtained hot-rolled steel sheet, by the above-mentioned method, among the microstructure fraction at the 1/4 position of the plate thickness in the plate thickness direction from the surface, the average particle size of the second phase, and the total particles of the second phase, the particles Average particle size of particles whose diameter is within the top 10%, extreme density in (110) <112> orientation, average spacing of precipitates with a diameter of 20 nm or less, and plate thickness from surface to surface in the plate thickness direction. The extreme density of the (110) <1-11> orientation in the metal structure at 1/16 of the above was determined. In addition, the test No. For 18, 33, 35 and 36, the second phase was connected and the particle size could not be measured as particles.
[0107]
The obtained results are shown in Tables 5 and 6. In the case where the total area ratio of bainite and the second phase did not reach 100%, the rest of the metal structure was ferrite. In addition, the test No. In No. 24, no precipitate having a diameter of 20 nm or less was observed.
[0108]
[Table 5]

[0109]
[Table 6]

[0110]
For the obtained hot-rolled steel sheet, the tensile strength TS, total elongation El, hole expansion ratio λ, limit bending radius R, and ductile brittle transition temperature vTrs were determined by the methods described below.
[0111]
Tensile strength TS and total elongation El
Tensile strength TS and total elongation El were obtained by conducting a tensile test using a JIS No. 5 test piece in accordance with JIS Z 2241: 2011. The crosshead speed was set to 10 mm / min. When the tensile strength TS was 980 MPa or more, it was determined to be acceptable as having excellent strength, and when it was less than 980 MPa, it was determined to be rejected as being inferior in strength. When the total elongation El was 13.0% or more, it was judged to be acceptable as having excellent ductility, and when it was less than 13.0%, it was judged to be rejected as being inferior in ductility.
[0112]
Hole expansion rate λ
The hole widening property is obtained by punching a circular hole with a diameter of 10 mm under the condition that the clearance is 12.5% ​​using a 60 ° conical punch, and performing a hole widening test so that the burr is on the die side. It was evaluated by the spread ratio λ. For each test number, five hole expansion tests were carried out, and the average value thereof was calculated to obtain a hole expansion rate λ. When the hole expanding rate was 60% or more, it was judged to be acceptable as having excellent hole expanding property, and when it was less than 60%, it was determined to be rejected as being poor in hole expanding property.
[0113]
Limit bending radius R
The bendability was evaluated by the limit bending radius R obtained by performing the V bending test. The limit bending radius R is V-bent using the No. 1 test piece in accordance with JIS Z2248: 2014 so that the direction perpendicular to the rolling direction is the longitudinal direction (the bending ridge line coincides with the rolling direction). Obtained by conducting a test.
[0114]
The angle between the die and the punch was set to 60 °, and the V-bending test was performed by changing the tip radius of the punch in units of 0.1 mm to obtain the maximum value of the tip radius of the punch that could be bent without cracking. I asked. The maximum value of the tip radius of the punch that could be bent without cracking was defined as the limit bending radius R. When the value (R / t) obtained by dividing the limit bending radius R by the plate thickness t of the test piece is 1.0 or less, it is judged to be acceptable as having excellent bendability, and is described as "Good" in Tables 7 and 8. did. On the other hand, if the value (R / t) obtained by dividing the limit bending radius R by the plate thickness t of the test piece is more than 1.0, it is judged to be inferior in bendability and rejected, and "Bad" is shown in Tables 7 and 8. ".
[0115]
Ductile brittle transition temperature vTrs
The ductile brittle transition temperature vTrs was subjected to a Charpy impact test using a V-notch test piece having a subsize of 2.5 mm specified in JIS Z 2242: 2018. The temperature at which the brittle fracture surface ratio was 50% was determined, and this was defined as the ductile brittle transition temperature vTrs. When the ductile brittle transition temperature vTrs is -40 ° C or lower (including -40 ° C, negative value from -40 ° C), it is judged to be acceptable as having excellent low temperature toughness, and it is judged to be acceptable over -40 ° C (not including -40 ° C). , A value positive from -40 ° C) was judged to be inferior in low temperature toughness and rejected. Further, when the ductile brittle transition temperature vTrs was −70 ° C. or lower, it was judged that the low temperature toughness was superior.
[0116]
The above test results are shown in Tables 7 and 8.
[0117]
[Table 7]

[0118]
[Table 8]

[0119]
From Tables 5 to 8, it can be seen that the examples of the present invention have excellent strength, ductility, bendability, drilling property and low temperature toughness. Further, it can be seen that the example of the present invention in which the average spacing of precipitates having a diameter of 20 nm or less is 50 nm or more has better low temperature toughness.
On the other hand, it can be seen that the comparative example is inferior in one or more of the properties of strength, ductility, bendability and hole widening property.
Industrial applicability
[0120]
According to the above aspect according to the present invention, it is possible to provide a hot-rolled steel sheet having excellent strength, ductility, bendability, hole-spreading property and low-temperature toughness, and a method for producing the same.
The scope of the claims
[Claim 1]
The chemical composition is mass%,
C: 0.040 to 0.150%,
Si: 0.50 to 1.50%,
Mn: 1.00 to 2.50%,
P: 0.100% or less,
S: 0.010% or less,
Al: 0.01-0.10%,
N: 0.0100% or less,
Ti: 0.005 to 0.150%,
B: 0.0005 to 0.0050%,
Cr: 0.10 to 1.00%,
Nb: 0 to 0.06%,
V: 0 to 0.50%,
Mo: 0 to 0.50%,
Cu: 0 to 0.50%,
Ni: 0 to 0.50%,
Sb: 0 to 0.020%,
Ca: 0 to 0.010%,
REM: 0-0.010%, and
Mg: 0 to 0.010%
Containing, the balance is iron and impurities,
In the metal structure at the 1/4 position of the plate thickness in the plate thickness direction from the surface
In terms of area ratio, the main phase is a bainite phase of 90.0 to 98.0%, the second phase is a martensite phase of 2.0 to 10.0%, or a martensite-austenite mixed phase.
The average particle size of the second phase is 1.5 μm or less,
Of all the particles in the second phase, the average particle size of the particles whose particle size is within the top 10% is 2.5 μm or less.
(110) <112> The extreme density of the orientation is 3.0 or less,
In the metal structure at the position 1/16 of the plate thickness in the plate thickness direction from the surface to the surface, the extreme density in the (110) <1-11> direction is 3.0 or less.
A hot-rolled steel sheet characterized by this.
[Claim 2]
The hot-rolled steel sheet according to claim 1, wherein the average spacing of MC carbides having a diameter of 20 nm or less is 50 nm or more in the metal structure at a position 1/4 of the plate thickness in the plate thickness direction from the surface.
[Claim 3]
The chemical composition is by mass%
Nb: 0.005 to 0.06%,
V: 0.05 to 0.50%,
Mo: 0.05 to 0.50%,
Cu: 0.01-0.50%,
Ni: 0.01-0.50%,
Sb: 0.0002 to 0.020%,
Ca: 0.0002 to 0.010%,
REM: 0.0002 to 0.010%, and
Mg: 0.0002 to 0.010%
The hot-rolled steel sheet according to claim 1 or 2, wherein the hot-rolled steel sheet contains one kind or two or more kinds selected from the group consisting of.