Title of invention: Steel plate
Technical field
[0001]
This disclosure relates to steel plates.
Background technology
[0002]
In recent years, it has been required to improve the fuel efficiency of automobiles from the viewpoint of regulation of greenhouse gas emissions associated with global warming countermeasures, and the application of high-strength steel plates is expanding more and more to reduce the weight of the car body and ensure collision safety. be. Particularly recently, there is an increasing need for ultra-high strength steel plates having a tensile strength of 1470 MPa or more. Further, a high-strength hot-dip zinc-plated steel plate having a hot-dip zinc-plated surface is required for a portion of the vehicle body where rust resistance is required.
[0003]
However, when an ultra-high strength steel plate having a tensile strength exceeding 1470 MPa is applied as a member for an automobile, it is necessary to solve hydrogen brittle cracking of the steel plate as well as its press formability.
[0004]
Hydrogen brittle cracking is a phenomenon in which a steel member under high stress under usage conditions suddenly breaks due to hydrogen that has entered the steel from the environment. This phenomenon is also called delayed destruction because of the form of destruction. In general, it is known that hydrogen brittle cracking of a steel plate is more likely to occur as the tensile strength of the steel plate increases. It is considered that this is because the higher the tensile strength of the steel plate, the greater the stress remaining on the steel plate after forming the part. The sensitivity to this hydrogen fragility cracking (delayed fracture) is called the hydrogen fragility resistance property.
[0005]
Various attempts have been made to improve the hydrogen brittle resistance of steel sheets.
[0006]
For example, in Patent Document 1, "having a predetermined chemical composition, the value of the solid melt B amount solB [mass%] and the old austenite particle size Dγ [μm] in the steel is the formula (1): solB · Dγ ≧. The relationship of 0.0010 is satisfied, and in terms of area ratio, polygonal ferrite is 10% or less, baynite is 30% or less, retained austenite is 6% or less, tempered martensite is 60% or more, and tempered martensite. Effective crystals when the number density of Fe carbides in the steel is 1 × 10 6 / mm 2 or more, the average dislocation density of the entire steel is 1.0 × 10 15 / m 2 or more, and 2.0 × 10 16 / m 2 or less. An ultra-high-strength cold-rolled steel plate having a steel structure having a particle size of 7.0 μm or less, having a tensile strength of 1300 MPa or more and excellent hydrogen brittle resistance.
[0007]
Further, Patent Document 2 states that "they have a predetermined composition, and the total area ratio of the tempered martensite and baynite to the entire structure is 95% or more and 100% or less, and they are stretched and / or dotted in the rolling direction. One or more major axes distributed in a shape: It is composed of inclusion particles of 0.3 μm or more, and when the inclusion particles are composed of two or more, the distance between the inclusion particles is 30 μm or less. , The total length in the rolling direction is more than 120 μm, the inclusion group is 0.8 pieces / mm2 or less, the aspect ratio is 2.5 or less, the major axis is 0.20 μm or more and 2 μm or less, and the main component is Fe. The number of charcoal to be used is 3500 / mm 2 or less, and the amount of charcoal having a diameter of 10 to 50 nm distributed inside the tempered martensite and / or the baynite is 0.7 × 10 7 / mm 2 or more. A cold-rolled steel plate having a structure in which the average particle size of γ grains is 18 μm or less, a plate thickness of 0.5 to 2.6 mm, and a tensile strength of 1320 MPa or more.
[0008]
Further, Patent Document 3 states, "It has a structure having a predetermined component composition and having a structure consisting of martensite: 90% or more and retained austenite: 0.5% or more in terms of area ratio with respect to the total structure, and has a local Mn concentration. However, there is a region where the Mn content of the entire steel plate is 1.1 times or more in terms of area ratio, and the tensile strength is 1470 MPa or more. Strong steel plate. ”Is disclosed.
Prior art literature
Patent documents
[0009]
Patent Document 1: Japanese Unexamined Patent Publication No. 2016-50343
Patent Document 2: International Publication No. 2016/152163
Patent Document 3: Japanese Unexamined Patent Publication No. 2016-153524
Outline of the invention
Problems to be solved by the invention
[0010]
As described above, all of Patent Documents 1 to 3 disclose steel plates having excellent hydrogen brittle resistance.
[0011]
However, in recent years when the required level has become high, it has been required to further improve the hydrogen fragility resistance property of the sheared portion, in particular, to improve the hydrogen fragility resistance property of the sheared portion while having a tensile strength of 1470 MPa or more and a high total elongation. The current situation is that there is.
[0012]
Therefore, an object of the present disclosure is to provide a steel plate having a tensile strength of 1470 MPa or more and a high total elongation, and excellent hydrogen brittle resistance of the sheared portion.
Means to solve the problem
[0013]
Means for solving the problem include the following aspects.
[1]
By mass%
C: 0.18% to 0.35%,
Si: 0.01% to 1.00%,
Mn: 0.10% to 2.40%,
P: 0.050% or less,
S: 0.0050% or less,
Al: 0.001% to 1.00%,
Ti: 0.001% to 0.050%,
B: 0.0005% -0.0050%,
N: 0.0100% or less,
O: 0.0050% or less,
Cr: 0% to 1.00%,
Mo: 0% to 0.50%,
Cu: 0% to 0.50%,
Ni: 0% to 0.50%,
Co: 0% to 0.50%,
W: 0% to 0.50%,
Sn: 0% to 0.50%,
Sb: 0% to 0.50%,
Nb: 0% to 0.050%,
V: 0% to 0.50%,
Ca: 0% to 0.0100%,
Mg: 0% -0.0100%,
Ce: 0% -0.0100%,
Zr: 0% -0.0100%,
La: 0% -0.0100%,
Hf: 0% to 0.0100%,
Bi: 0% to 0.0100%, and
REM: Contains 0% to 0.0100% and
Formula: 0.001 ≦ Ti− (47.88 / 14.01) × N ≦ 0.040 (However, in the formula, the element symbol indicates the mass% of the corresponding element).
The balance has a chemical composition consisting of Fe and impurities,
In the rolling direction cross section of the steel plate, the steel structure in the range of 1/8 thickness to 3/8 thickness centered on 1/4 thickness from the surface of the steel plate has an area ratio of%.
Ferrite: 0-5%,
Martensite: 90.0-99.5%,
Percentage of burnt-back martensites in all martensites: 80.0-100.0%
Residual austenite: 0.5-6.0%
Contains,
The number density of inclusions satisfying the maximum diameter ≧ 3 μm in the measurement region in the range of 1/8 thickness to 7/8 thickness × 25 mm from the surface of the steel plate in the rolling direction cross section of the steel plate is 40 pieces / mm 2 or less,
When the measurement area was divided into 100 sections divided into two in the thickness direction and 50 in the width direction, and the number density of the inclusions satisfying the maximum diameter ≥ 3 μm of each section was calculated, the number density was the top 10%. The number density in the section is 80 pieces / mm 2 or less, and
Satisfying the following formula (A),
A steel plate with a tensile strength of 1470 MPa or more.
Vγ'/ Vγ ≧ 0.1 ... (A)
Vγ: area ratio of initial retained austenite, Vγ': area ratio of retained austenite after deep cooling at -196 ° C.
[2]
The steel plate according to [1], wherein the number density of inclusions satisfying the maximum diameter ≥ 3 μm is 30 pieces / mm 2 or less.
[3]
The steel plate according to [1] or [2], wherein the number density in the section where the number density is the top 10% is 60 pieces / mm 2 or less.
[4]
The steel plate according to any one of [1] to [3] that satisfies the following formula (A2).
Vγ'/ Vγ ≧ 0.2 ... (A2)
Vγ: area ratio of initial retained austenite, Vγ': area ratio of retained austenite after deep cooling at -196 ° C.
Effect of the invention
[0014]
According to the present disclosure, it is possible to provide a steel plate having a tensile strength of 1470 MPa or more and a high total elongation, and having excellent hydrogen brittle resistance of the sheared portion.
A brief description of the drawing
[0015]
[Fig. 1] Fig. 1 is a schematic diagram for explaining a measurement position of an area ratio of each structure of a steel structure.
[Fig. 2] Fig. 2 is a schematic diagram for explaining the measurement position of the number density of inclusions.
FIG. 3 is a schematic configuration diagram showing a part of a vertical bending type continuous casting facility having a vertical portion.
Embodiment for carrying out the invention
[0016]
Hereinafter, this disclosure will be described.
In the present specification, the numerical range represented by using "-" means a range including the numerical values ​​before and after "-" as the lower limit value and the upper limit value.
In the numerical range described in stages, the upper limit value described in one numerical range may be replaced with the upper limit value of the numerical range described in another stage, and the lower limit value may be described in another stage. It may be replaced with the lower limit of the numerical range of.
In the numerical range, the upper limit value or the lower limit value described in a certain numerical range may be replaced with the value shown in the embodiment.
The term "process" is included in this term not only for independent processes but also for cases where the intended purpose of the process is achieved even if it cannot be clearly distinguished from other processes.
The "combination of preferred embodiments" is a more preferred embodiment.
[0017]
The "cross section in the rolling direction of the steel plate" indicates a cut surface whose normal is the plate width direction of the steel plate.
The notation "Y / X thickness" indicates that the plate thickness is Y / X. Specifically, "1/8 thickness" indicates that it is 1/8 of the plate thickness.
[0018]
(Steel plate)
The steel plate of the present disclosure has a predetermined chemical composition and has the following steel structure.
(1) The steel structure in the range of 1/8 to 3/8 thickness centered on 1/4 thickness from the surface of the steel plate has an area ratio of%, ferrite: 0 to 5%, and martensite: 90.0 to. It contains 99.5%, the ratio of tempered martensite to the total martensite: 80.0 to 100.0%, and retained austenite: 0.5 to 6.0%.
(2) The number density of inclusions satisfying the maximum diameter ≧ 3 μm in the measurement region in the range of 1/8 thickness to 7/8 thickness × 25 mm from the surface of the steel plate in the rolling direction cross section of the steel plate. 40 pieces / mm 2 or less.
(3) When the measurement area of ​​the number density of inclusions is divided into 100 sections divided into two in the thickness direction and 50 in the width direction, and the number density of inclusions satisfying the maximum diameter ≧ 3 μm of each section is calculated. , The number density is 80 pieces / mm 2 or less in the section where the number density is the top 10%.
(4) Satisfies equation (A).
Vγ'/ Vγ ≧ 0.1 ... (A)
Vγ: initial retained austenite, Vγ': -196 ° C retained austenite after deep cooling
(5) The tensile strength is 1470 MPa or more.
[0019]
Due to the above configuration, the steel plate of the present disclosure is a steel plate having a tensile strength of 1470 MPa or more and a high total elongation, and excellent in hydrogen brittle resistance of the sheared portion. The steel plate of the present disclosure was found by the following findings.
[0020]
The inventor examined the hydrogen brittle resistance characteristics of the sheared part. As a result, the following findings were obtained.
With high-strength steel plates, minute initial cracks may occur just below the end face of the sheared part. In the sheared portion, the initial crack just below the end face becomes the starting point of the hydrogen brittle crack. Furthermore, this initial crack tends to occur at a site where a large number of coarse inclusions are accumulated. That is, it is known that reducing the number density of inclusions improves the hydrogen brittle property, but in addition, the degree of accumulation of inclusions (that is, the number in the compartment where the number density of inclusions is in the top 10%). By reducing the density), the hydrogen brittle resistance characteristics of the sheared portion can be further improved.
In addition, retained austenite also causes hydrogen brittle cracking in the sheared part. This is because retained austenite undergoes processing-induced transformation into martensite by shearing. Since such martensite contains a high concentration of solidified carbon, it is extremely brittle and is considered to have an adverse effect on hydrogen brittle cracking. On the other hand, retained austenite is also a necessary structure for increasing the ductility of the steel plate.
Therefore, the inventor considered stabilizing retained austenite. As a result, it was found that the stability of retained austenite can be improved by devising the cooling pattern in the continuous annealing process, and as a result, the hydrogen brittle resistance property of the sheared portion can be improved.
[0021]
That is, the inventor has a tensile strength of 1470 MPa or more and a high total elongation in the case of the above steel structure. However, it was found that the hydrogen brittle resistance of the sheared part can be improved.
[0022]
From the above findings, it was found that the steel plate of the present disclosure is a steel plate having a tensile strength of 1470 MPa or more and a high total elongation, and excellent in hydrogen brittle resistance of the sheared portion.
[0023]
Hereinafter, the steel plate of the present disclosure will be described in more detail.
[0024]
(Chemical composition)
The chemical composition of the steel plate of the present disclosure will be described.
In addition, Cr, Mo, Cu, Ni, Co, W, Sn, Sb, Nb, V, Ca, Mg, Ce, Zr, La, Hf, Bi and REM are optional elements and are not contained in the steel. You may.
[C: 0.18% to 0.35%]
C is an essential element for achieving the desired tensile strength. On the other hand, excessive C content deteriorates hydrogen brittle resistance and weldability. Therefore, the amount of C is set to 0.18% to 0.35%.
The lower limit of the amount of C is preferably 0.19% or more, more preferably 0.20% or more.
The upper limit of the amount of C is preferably 0.33% or less, more preferably 0.25% or less.
[0025]
[Si: 0.01% to 1.00%]
Si is an element effective for increasing the strength of steel sheets because it suppresses the formation and growth of iron carbide in martensite in addition to being a solid solution strengthening element. On the other hand, excessive Si content deteriorates the chemical conversion processability and hydrogen brittle resistance of the steel plate. Therefore, the amount of Si is set to 0.01% to 1.00%.
The lower limit of the amount of Si is preferably 0.10% or more, more preferably 0.30% or more.
The upper limit of the amount of Si is preferably 0.90% or less, more preferably 0.80% or less.
[0026]
[Mn: 0.10% to 2.40%]
Mn is a strong austenite stabilizing element and is an essential element for improving the hardenability of steel sheets. On the other hand, excessive Mn content deteriorates the toughness and hydrogen brittle resistance of the spot welded portion. Therefore, the amount of Mn is set to 0.10% to 2.40%.
The lower limit of the amount of Mn is preferably 0.70% or more, more preferably 1.00% or more, and further preferably 1.30% or more.
The upper limit of the amount of Mn is preferably 2.10% or less, more preferably 1.80% or less.
[0027]
[P: 0.050% or less]
P is a solid solution strengthening element and is an effective element for increasing the strength of steel plates. On the other hand, excessive P content deteriorates weldability and toughness. Therefore, the amount of P is set to 0.050% or less.
The upper limit of the amount of P is preferably 0.02% or less, more preferably 0.015%.
However, from the viewpoint of suppressing an increase in the cost of removing P, the lower limit of the amount of P is, for example, more than 0% (preferably 0.001%).
[0028]
[S: 0.0050% or less]
S is an element contained as an impurity and forms MnS in steel to deteriorate toughness, perforation property, and hydrogen brittle resistance. Therefore, the amount of S is set to 0.0050% or less.
The upper limit of the amount of S is preferably 0.0040% or less, more preferably 0.0030% or less.
However, from the viewpoint of suppressing an increase in the cost of removing S, the lower limit of the amount of S is, for example, more than 0% (preferably 0.0001%).
[0029]
[Al: 0.001% to 1.00%]
Al is an element for deoxidizing steel. On the other hand, the excessive content of Al not only saturates the deoxidizing effect and raises the cost, but also raises the transformation temperature of the steel and increases the load during hot rolling. Therefore, the amount of Al is set to 0.001% to 1.00%.
The lower limit of the amount of Al is preferably 0.005% or more, more preferably 0.010% or more.
The upper limit of the amount of Al is preferably 0.50% or less, more preferably 0.20% or less.
[0030]
[Ti: 0.001% to 0.050%]
Ti suppresses the formation of BN, which is a factor for reducing hardenability, by fixing N as TiN in steel. In addition, the austenite particle size during heating is made finer to improve toughness and hydrogen brittleness resistance. On the other hand, if the excess Ti is contained, a large amount of coarse TiS is generated, and the toughness and hydrogen brittleness resistance of the steel plate are lowered. Therefore, the amount of Ti is set to 0.001% to 0.050%.
The lower limit of the Ti amount is preferably 0.005% or more, more preferably 0.010% or more.
The upper limit of the Ti amount is preferably 0.040% or less, more preferably 0.030% or less.
[0031]
[B: 0.0005% -0.0050%]
B segregates into the austenite grain boundaries when the steel plate is heated, and stabilizes the austenite grain boundaries to improve the hardenability of the steel. In addition, the toughness and hydrogen brittle resistance of the steel plate are improved by increasing the bonding force of the austenite grain boundaries. On the other hand, excessive content of B results in impairing the hardenability of the steel by forming a boro compound. Therefore, the amount of B is set to 0.0005% to 0.0050%.
The lower limit of the amount of B is preferably 0.0007% or more, more preferably 0.0010% or more.
The upper limit of the amount of B is preferably 0.0035% or less, more preferably 0.0025% or less.
[0032]
[N: 0.0100% or less]
N is an element contained as an impurity and forms a coarse nitride in the steel to deteriorate the hole expanding property and the hydrogen brittle resistance property. Therefore, the amount of N is set to 0.0100% or less.
The upper limit of the amount of N is preferably 0.0060% or less.
However, from the viewpoint of suppressing an increase in the cost of removing N, the lower limit of the amount of N is, for example, more than 0% (preferably 0.0005%).
[0033]
[O: 0.0050% or less]
O is an element contained as an impurity and forms a coarse oxide in the steel to deteriorate the hole-expanding property and the hydrogen brittle resistance. Therefore, the amount of O is set to 0.0050% or less.
The upper limit of the amount of O is preferably 0.0030% or less.
However, from the viewpoint of suppressing an increase in the cost of removing O, the lower limit of the amount of O is, for example, more than 0% (preferably 0.0001%).
[0034]
In addition to the above elements, the composition of the steel plate according to the present embodiment may contain one or more selected from the element groups described below for the purpose of improving the characteristics. In the steel plate according to this embodiment, these are arbitrary elements. In the steel plate according to the present embodiment, the content of these optional elements may be less than the lower limit (including 0%) shown below for each of these optional elements.
[0035]
[Cr: 0% to 1.00%]
Cr is an element effective for increasing the strength of steel plates. Therefore, Cr may be contained in the steel if necessary. On the other hand, excessive Cr content saturates the effect and leads to an increase in cost. Therefore, the amount of Cr is set to 0% to 1.00%.
The lower limit of the amount of Cr is preferably 0.001% or more.
The upper limit of the amount of Cr is preferably 0.50% or less.
[0036]
[Mo: 0% to 0.50%]
Mo is an element effective for improving the hardenability of a steel plate, and also has an effect of improving toughness and hydrogen brittle resistance by reducing the austenite particle size during heating of the steel plate. Therefore, Mo may be contained in the steel, if necessary. On the other hand, excessive Mo content saturates the effect and leads to an increase in cost. Therefore, the amount of Mo is set to 0% to 0.50%.
The lower limit of the amount of Mo is preferably 0.001% or more, more preferably 0.050% or more.
The upper limit of the amount of Mo is preferably 0.30% or less, more preferably 0.20% or less.
[0037]
[Cu: 0% to 0.50%]
Cu is an element effective for increasing the strength of steel plates. Therefore, Cu may be contained in the steel if necessary. On the other hand, excessive inclusion of Cu saturates the effect and causes an increase in cost. Therefore, the amount of Cu is set to 0% to 0.50%.
The lower limit of the amount of Cu is preferably 0.001% or more.
The upper limit of the amount of Cu is preferably 0.30% or less.
[0038]
[Ni: 0% to 0.50%]
Ni is an element that is effective in increasing the strength of steel sheets. Therefore, Ni may be contained in the steel if necessary. On the other hand, excessive Ni content saturates the effect and leads to an increase in cost. Therefore, the amount of Ni is set to 0% to 0.50%.
The lower limit of the amount of Ni is preferably 0.001% or more.
The upper limit of the amount of Ni is preferably 0.30% or less.
[0039]
[Co: 0% to 0.50%]
Co is an element effective for increasing the strength of steel sheets. Therefore, Co may be contained in the steel if necessary. On the other hand, excessive Co content saturates the effect and leads to an increase in cost. Therefore, the amount of Co is set to 0% to 0.50%.
The lower limit of the amount of Co is preferably 0.001% or more.
The upper limit of the amount of Co is preferably 0.30% or less.
[0040]
[W: 0% to 0.50%]
W is an element effective for increasing the strength of steel plates. Therefore, W may be contained in the steel if necessary. On the other hand, excessive W content saturates the effect and leads to an increase in cost. Therefore, the amount of W is set to 0% to 0.50%.
The lower limit of the W amount is preferably 0.001% or more.
The upper limit of the W amount is preferably 0.30% or less.
[0041]
[Sn: 0% to 0.50%]
Sn is an element effective for improving the corrosion resistance of steel plates. Therefore, Sn may be contained in the steel if necessary. On the other hand, excessive Sn content saturates the effect and leads to an increase in cost. Therefore, the Sn amount is set to 0% to 0.50%.
The lower limit of the Sn amount is preferably 0.001% or more.
The upper limit of the Sn amount is preferably 0.30% or less.
[0042]
[Sb: 0% to 0.50%]
Sb is an element effective for improving the corrosion resistance of steel plates. Therefore, Sb may be contained in the steel if necessary. On the other hand, excessive Sb content saturates the effect and leads to an increase in cost. Therefore, the amount of Sb is set to 0% to 0.50%.
The lower limit of the amount of Sb is preferably 0.001% or more.
The upper limit of the amount of Sb is preferably 0.30% or less.
[0043]
[Nb: 0% to 0.050%]
Nb is a charcoal-forming element and is an effective element for increasing the strength of steel sheets. Therefore, Nb may be contained in the steel if necessary. On the other hand, excessive Nb content saturates the effect and leads to an increase in cost. Therefore, the amount of Nb is set to 0% to 0.050%.
The lower limit of the amount of Nb is preferably 0.001% or more.
The upper limit of the amount of Nb is preferably 0.035% or less.
[0044]
[V: 0% to 0.50%]
V is a charcoal-forming element and is an effective element for increasing the strength of steel plates. Therefore, V may be contained in the steel if necessary. On the other hand, excessive V content saturates the effect and leads to an increase in cost. Therefore, the amount of V is set to 0% to 0.50%.
The lower limit of the amount of V is preferably 0.001% or more.
The upper limit of the amount of V is preferably 0.300% or less.
[0045]
[Ca: 0% to 0.0100%]
Ca is an element that contributes to the fine dispersion of inclusions in steel, and is an element that contributes to the improvement of hydrogen brittle resistance and toughness of steel sheets. Therefore, Ca may be contained in the steel if necessary. On the other hand, excessive Ca content causes deterioration of ductility. Therefore, the amount of Ca is set to 0% to 0.0100%.
The lower limit of the Ca amount is preferably 0.0001% or more.
The upper limit of the Ca amount is preferably 0.0050% or less.
[0046]
[Mg: 0% to 0.0100%]
Mg is an element that contributes to the fine dispersion of inclusions in steel, and is an element that contributes to the improvement of hydrogen brittle resistance and toughness of steel sheets. Therefore, Mg may be contained in the steel if necessary. On the other hand, excessive inclusion of Mg causes deterioration of ductility. Therefore, the amount of Mg is set to 0% to 0.0100%.
The lower limit of the amount of Mg is preferably 0.0001% or more.
The upper limit of the amount of Mg is preferably 0.0050% or less.
[0047]
[Ce: 0% to 0.0100%]
Ce is an element that contributes to the fine dispersion of inclusions in steel, and is an element that contributes to the improvement of hydrogen brittle resistance and toughness of steel sheets. Therefore, Ce may be contained in the steel if necessary. On the other hand, excessive content of Ce causes deterioration of ductility... Therefore, the Ce amount is set to 0% to 0.0100%.
The lower limit of the Ce amount is preferably 0.0001% or more.
The upper limit of the Ce amount is preferably 0.0050% or less.
[0048]
[Zr: 0% to 0.0100%]
Zr is an element that contributes to the fine dispersion of inclusions in steel, and is an element that contributes to the improvement of hydrogen brittle resistance and toughness of steel sheets. Therefore, Zr may be contained in the steel if necessary. On the other hand, excessive Zr content causes deterioration of ductility. Therefore, the amount of Zr is set to 0% to 0.0100%.
The lower limit of the amount of Zr is preferably 0.0001% or more.
The upper limit of the amount of Zr is preferably 0.0050% or less.
[0049]
[La: 0% -0.0100%]
La is an element that contributes to the fine dispersion of inclusions in steel, and is an element that contributes to the improvement of hydrogen brittle resistance and toughness of steel sheets. Therefore, La may be contained in the steel if necessary. On the other hand, excessive inclusion of La causes deterioration of ductility. Therefore, the amount of La is set to 0% to 0.0100%.
The lower limit of the La amount is preferably 0.0001% or more.
The upper limit of the amount of La is preferably 0.0050% or less.
[0050]
[Hf: 0% to 0.0100%]
Hf is an element that contributes to the fine dispersion of inclusions in steel, and is an element that contributes to the improvement of hydrogen brittle resistance and toughness of steel sheets. Therefore, Hf may be contained in the steel if necessary. On the other hand, excessive Hf content causes deterioration of ductility. Therefore, the amount of Hf is set to 0% to 0.0100%.
The lower limit of the Hf amount is preferably 0.0001% or more.
The upper limit of the amount of Hf is preferably 0.0050% or less.
[0051]
[Bi: 0% -0.0100%]
Bi is an element that reduces microsegregation of substituted alloy elements such as Mn and Si in steel, and contributes to the improvement of hydrogen brittle resistance and toughness of steel sheets. Therefore, Bi may be contained in the steel if necessary. On the other hand, excessive Bi content causes deterioration of ductility. Therefore, the Bi amount is set to 0% to 0.0100%.
The lower limit of the Bi amount is preferably 0.0001% or more.
The upper limit of the Bi amount is preferably 0.0050% or less.
[0052]
[REM: 0% to 0.0100%]
REM is an element that contributes to the fine dispersion of inclusions in steel, and is an element that contributes to the improvement of hydrogen brittle resistance and toughness of steel sheets. Therefore, REM may be contained in steel if necessary. On the other hand, excessive REM content causes deterioration of ductility. Therefore, the REM amount is set to 0% to 0.0100%.
The lower limit of the REM amount is preferably 0.0001% or more.
The upper limit of the REM amount is preferably 0.0050% or less.
[0053]
Note that REM is an abbreviation for Rare Earth Metal, and in the present disclosure, it indicates elements belonging to the Sc, Y and lanthanoid series excluding Ce and La.
The REM amount indicates the total amount of elements belonging to the Sc, Y and lanthanoid series excluding Ce and La. The elements belonging to the lanthanoid series are industrially contained in the form of misch metal.
[0054]
[0.001 ≤ Ti- (47.88 / 14.01) x N ≤ 0.040 (however, in the formula, the element symbol indicates the mass% of the corresponding element)]
The above formula is the value obtained by subtracting the amount of Ti consumed as TiN from the amount of Ti in steel. If the value in the above equation is too small, solid-dissolved N that is not fixed as TiN remains, so boron nitride (BN) precipitates and the hardenability of the steel deteriorates. On the other hand, if the above equation is too large, Ti becomes excessive with respect to the amount of N, and Ti-based inclusions such as sulfides increase.
Therefore, the relationship between the Ti amount and the N amount satisfies 0.001 ≦ Ti− (47.88 / 14.01) × N ≦ 0.040.
The relationship between the amount of Ti and the amount of N preferably satisfies 0.003 ≦ Ti− (47.88 / 14.01) × N ≦ 0.025.
[0055]
[Remaining]
The rest is Fe and impurities. The impurities refer to those mixed from ore, scrap, manufacturing environment, etc. as a raw material when the steel plate is industrially manufactured. Further, examples of the impurities include H, Zn, Pb, Cd, As and the like. These elements are limited to, for example, 0.01% or less.
[0056]
(Steel structure)
Next, the steel structure of the steel plate of the present disclosure will be described.
[0057]
[Ferrite: 0 to 5%, Martensite: 90.0 to 99.5%, Ratio of tempered martensite to total martensite: 80.0 to 100.0%, Retained austenite: 0.5 to 6. 0%]
The steel structure in the range of 1/8 to 3/8 thickness (see FIG. 1) centered on 1/4 thickness from the surface of the steel plate has an area ratio of%, ferrite: 0 to 5%, and martensite: 90. It contains 0 to 99.5%, the ratio of rebaked martensite to the total martensite: 80.0 to 100.0%, and retained austenite: 0.5 to 6.0%.
[0058]
If ferrite exceeds 5%, it becomes difficult to obtain a tensile strength of 1470 MPa or more. Further, in the martensite-based structure, the presence of ferrite, which is a soft structure, increases the non-uniformity of the structure and promotes hydrogen brittle cracking. Therefore, the area ratio of ferrite is set to 0 to 5%.
The upper limit of the area ratio of ferrite is preferably 4% or less, preferably 2% or less, and ideally 0%.
[0059]
It is possible to obtain a tensile strength of 1470 MPa or more by using martensite (maltensite as it is baked + martensite that has been tempered) as the main component. On the other hand, among the martensites, if there are many martensites as they are baked and few martensites are back-baked, the hydrogen brittle resistance characteristics deteriorate.
Therefore, the area ratio of martensite is 90.0 to 99.5%, and the ratio of rebaked martensite to all martensite is 80.0 to 100.0%.
The lower limit of the area ratio of martensite is preferably 93.0% or more, more preferably 95.0% or more.
The lower limit of the ratio of tempered martensite to all martensite is preferably 85.0% or more, more preferably 90.0% or more.
[0060]
When retained austenite is contained in the steel structure, the work hardening rate is increased due to the TRIP (TRansformation-Induced Plasticity) effect, so that the ductility is improved (that is, the total elongation is increased). On the other hand, if there is a large amount of retained austenite, the hydrogen brittle resistance property deteriorates.
Therefore, the area ratio of retained austenite is 0.5 to 6.0%.
The lower limit of the area ratio of retained austenite is preferably 1.0% or more, more preferably 1.5% or more.
The upper limit of the area ratio of retained austenite is preferably 5.5% or less, more preferably 5.0% or less.
[0061]
The steel structure may contain a residual structure in addition to ferrite, martensite, and retained austenite. Examples of the remaining structure include baynite. The area ratio of the remaining structure is exemplified by 0 to 10%.
[0062]
[Measuring method of area ratio of each tissue]
The area ratio of each structure other than retained austenite is evaluated by the SEM-EBSD method (electron beam backscattering diffraction method) and SEM secondary electron image observation. First, a sample is taken with a plate thickness cross section parallel to the rolling direction of the steel plate as an observation surface, and the observation surface is mechanically polished to a mirror surface, and then electrolytic polishing is performed. Next, in one or more observation fields in the range of 1/8 to 3/8 thickness centered on 1/4 thickness from the surface on the observation surface, crystals were crystallized by the SEM-EBSD method for a total area of ​​3000 μm 2 or more. Perform structural and orientation analysis. "OIM Analysys 7.0" manufactured by TSL is used for the analysis of the data obtained by the EBSD method. The distance between scores (step) is 0.03 to 0.20 μm. A crystal grain boundary map is obtained with the boundary where the crystal orientation difference is 15 degrees or more as the grain boundary. Next, the same sample is subjected to nightal etching. Then, a secondary electron image is taken using FE-SEM for the same field as the field for which crystal orientation analysis is performed by EBSD. At this time, it is advisable to mark in advance with a Vickers indentation or the like. Finally, the crystal grain boundary map and the secondary electron image are superimposed. The structure of each crystal grain surrounded by grain boundaries with an orientation difference of 15 degrees or more is classified based on the following criteria.
[0063]
In the secondary electron image, crystal grains having neither a substructure nor iron-based carbides and having a crystal structure of BCC are judged to be ferrite.
In the secondary electron image, crystal grains in which a substructure is observed and iron-based carbon dioxide is precipitated in a single variant, or crystal grains in which iron-based carbon dioxide is not observed, are judged to be baynite.
In the secondary electron image, crystal grains in which cementite is precipitated in a lamellar shape are judged to be pearlite. However, in principle, pearlite is not included in this disclosure.
Judge the rest as martensite and retained austenite. The area ratio of martensite can be obtained by subtracting the area ratio of retained austenite, which will be described later, from the area ratio of the remaining portion.
Among the remaining parts, the crystal grains in which the substructure is recognized in the secondary electron image and two or more iron-based carbon dioxide precipitated in multiple variants are recognized are judged to be tempered martensite.
[0064]
The area ratio of retained austenite can be calculated by measurement using X-rays. That is, the portion from the plate surface of the steel plate to the depth 1/4 position in the plate thickness direction is removed by mechanical polishing and chemical polishing. Then, the diffraction of the bcc phase (200), (211) and the fcc phase (200), (220), (311) obtained by using MoKα 1 ray as the characteristic X-ray with respect to the polished sample. The tissue fraction of retained austenite is calculated from the integrated intensity ratio of the peak, and this is used as the area ratio of retained austenite.
[0065]
[Number density of inclusions satisfying maximum diameter ≥ 3 μm]
When a large number of coarse inclusions are present, the inclusions become the starting point of cracking in the sheared portion, and hydrogen brittle cracking occurs. Therefore, it is preferable that the number density of coarse inclusions is small.
Therefore, inclusions satisfying the maximum diameter ≧ 3 μm in the measurement region (see FIG. 2) in the range of 1/8 thickness to 7/8 thickness × 25 mm from the surface of the steel plate in the rolling direction cross section of the steel plate. The number density of is 40 pieces / mm 2 or less. Here, the measurement area is "a range of 1/8 thickness to 7/8 thickness in the plate thickness direction from the surface of the steel plate in the rolling direction cross section of the steel plate" x "a range of a width of 25 mm in the rolling direction of the steel plate". The area to be used is shown (see FIG. 2).
The number density of inclusions satisfying the maximum diameter ≧ 3 μm is preferably 30 pieces / mm 2 or less, and more preferably 20 pieces / mm 2 or less.
Since it is difficult to completely suppress the formation of inclusions, the lower limit of the number density of inclusions satisfying the maximum diameter ≧ 3 μm is, for example, 1 piece / mm 2 or more, or 2 pieces / mm 2 or more. Is.
[0066]
Here, the inclusions are, for example, TiS, TiN, TiO, Ti (C, S), MnS, CaS, Al 2O 3, SiO 2, CaO, etc., or a complex thereof.
The "maximum diameter" is defined as the diameter in the case of a spherical shape, the length of the long axis in the case of an elliptical shape, the length of the long side in the case of a plate-shaped or rectangular shape, and the length in the case of a rod-shaped shape.
Even if inclusions having a maximum diameter of less than 3 μm are accumulated, they are not considered in the present disclosure because they are unlikely to develop into minute initial cracks at the end face of the sheared portion.
[0067]
[Number density in the section where the number density is the top 10%]
If coarse inclusions are unevenly distributed, coarse inclusions are likely to be present in the sheared portion. Such inclusions serve as the starting point of cracking, and hydrogen brittle cracking occurs. Therefore, it is good to reduce the probability that coarse inclusions are present in the sheared portion by suppressing uneven distribution of coarse inclusions and reducing the degree of accumulation of inclusions.
Therefore, the measurement region of the number density of inclusions (that is, the measurement region in the rolling direction cross section of the steel plate, which is in the range of 1/8 thickness to 7/8 thickness × 25 mm from the surface of the steel plate) is in the thickness direction. Divided into two, width When the number density of inclusions satisfying the maximum diameter ≥ 3 μm of each section is calculated by dividing into 100 sections divided into 50 in the direction (that is, the rolling direction) (see FIG. 2), the number density is the top 10%. The number density in the above is 80 pieces / mm 2 or less.
The number density in the section where the number density is the top 10% is preferably 60 pieces / mm 2 or less, and more preferably 40 pieces / mm 2 or less.
Since it is difficult to set the number density of inclusions to 0, the lower limit of the number density in the section where the number density is the upper 10% is, for example, 1 piece / mm 2 or more, or 2 pieces / mm 2 or more. Is.
[0068]
[Method of measuring the number density of inclusions]
The method for measuring the number density of inclusions is as follows.
A sample is taken with the plate thickness section parallel to the rolling direction of the steel plate as the observation surface, and the observation surface is machine-polished to make a mirror surface. For the region including the range of 25 mm, a backscattered electron image is taken using an SEM equipped with an EDX (energy dispersion type X-ray analyzer), and the composition of individual inclusions is measured. Get information about maximum diameter, position, and composition for each inclusion in the field of view. As inclusions, those having a composition that is almost unthinkable, for example, those in which any of Na, K, and Cl is detected in an amount of 5% by mass or more, Si is detected in an amount of 15% by mass or more, and O is detected in an amount of 60% by mass or more. Is judged to be contamination caused by tap water, abrasives, etc., and is excluded from the measurement results. From this data, the number density can be obtained by dividing the number of inclusions having a maximum diameter of 3 μm or more included in the range of 1/8 thickness to 7/8 thickness × 25 mm by the area. Further, the number density of each section can be obtained by measuring the number of inclusions having a maximum diameter of 3 μm or more and dividing by the section area for each section divided into 100 as described above.
[0069]
[Equation (A)]
When retained austenite is transformed into martensite (martensite as it is hardened) by the energy generated by shearing, the transformed martensite becomes the starting point in the sheared portion, and hydrogen brittle cracking occurs. Therefore, it is preferable that stable retained austenite is present.
Therefore, the following formula (A) is satisfied as an index that the retained austenite is unlikely to be transformed into martensite (maltensite as it is baked) by shearing. It is preferable to satisfy the following formula (A2), and more preferably it is to satisfy the following formula (A3).
However, although the upper limit of "Vγ'/ Vγ" is ideally 1, it is difficult to actually set it to 1, so for example, it is set to 0.95 or less or 0.9 or less.
Vγ'/ Vγ ≧ 0.1 ... (A)
Vγ'/ Vγ ≧ 0.2 ... (A2)
Vγ'/ Vγ ≧ 0.3 ... (A3)
Vγ: area ratio of initial retained austenite, Vγ': area ratio of retained austenite after deep cooling at -196 ° C.
[0070]
[Method for measuring the area ratio of retained austenite at the initial stage and after deep cooling at -196 ° C]
The method for measuring the area ratio of retained austenite at the initial stage and after deep cooling at -196 ° C is as follows. First, a sample is cut out from the target steel plate and then deep-cooled to liquid nitrogen at -196 ° C. The soaking time may be about 1 minute, for example, until the boiling of the liquid nitrogen is sufficiently settled. Subsequent sample preparation method and measurement method are the same as the above-mentioned "method for measuring the area ratio of retained austenite".
[0071]
(Mechanical characteristics, etc.)
Next, the mechanical properties of the steel plate of the present disclosure will be described.
[0072]
[Tensile strength (TS)]
The tensile strength (TS) of the steel plate of the present disclosure is 1470 MPa or more. In order to satisfy the weight reduction and collision safety required for steel sheets for automobiles in recent years, the tensile strength of the steel sheet shall be 1470 MPa or more.
[0073]
[Full growth (El)]
The total elongation (El) of the steel plate of the present disclosure is preferably 6% or more, more preferably 7% or more.
[0074]
Here, the tensile strength and total elongation of the steel plate are measured in the air at room temperature (25 ° C.) by the tensile test specified in JIS Z 2241 (2011).
[0075]
[Hole expansion rate (λ)]
The hole expansion ratio (λ) of the steel plate of the present disclosure is preferably 20% or more, more preferably 30% or more.
The hole expansion rate (λ) is measured by the "JFS T 1001 hole expansion test method" of the Japan Steel Federation standard.
[0076]
[Minimum bending radius (R)]
The minimum bending radius (R) of the steel plate of the present disclosure is preferably 5 mm or less, more preferably 4 mm or less.
The minimum bending radius (R) of the steel plate is measured in the air at room temperature (25 ° C.) by the bending test: V-block method of the bending test specified in JIS Z 2248 (2014).
[0077]
[Plating layer]
The steel plate of the present disclosure may have a plating layer on both sides or one side. As the plating layer, a molten zinc-based plating layer or the like is typically exemplified.
[0078]
(Manufacturing method of steel plate)
Next, an example of the steel plate manufacturing method of the present disclosure will be described.
The steel plate manufacturing method of the present disclosure may be a manufacturing method in which each of the following steps (1) to (4) is sequentially performed.
[0079]
[(1) Casting process]
In the casting process, a molten steel having the chemical composition of the steel plate of the present disclosure is cast in a vertical bending type continuous casting facility having a vertical portion to obtain a steel slab.
Specifically, in the casting process, for example, a vertical bending type continuous casting facility having a vertical portion is used to flow molten steel into a mold, a primary cooling zone in the mold, and a secondary portion in the vertical portion from the outlet side of the mold to the bending start portion. A steel slab is obtained by casting while cooling with a tertiary cooling zone after the cooling zone and the bent portion (see FIG. 3).
Note that FIG. 3 is a schematic configuration diagram showing a part of a vertical bending type continuous casting facility having a vertical portion. In FIG. 3, 10 is a continuous casting facility, and 11 is a vertical portion from the ejection side of the mold to the bending start portion. Part, 12 is a bent part, 20 is a mold (for example, a water-cooled mold), 30 is a dipping nozzle for supplying molten steel to the mold, 31 is a molten steel discharge port of the dipping nozzle, 40 is a support roll, and 50 is a steel slab. ..
[0080] [0080]
The casting process is performed from the viewpoint of suppressing the formation and uneven distribution of coarse inclusions and setting the "number density of inclusions" and the "number density of inclusions in the section where the number density is the top 10%" within the above ranges. , The casting process satisfies the following conditions.
[0081]
-(1-1) In the secondary cooling zone where the steel slab is cooled in the vertical part from the ejection side of the mold to the bending start part, until the surface temperature of the central part in the width direction of the steel slab reaches 1000 ° C. or less. Cooling at a cooling rate of 5 ° C / sec or higher (also referred to as "vertical cooling rate")-
When the cooling rate is increased in the secondary cooling zone in the vertical portion from the ejection side of the mold to the bending start portion, the alloy components (Ti, Mn, S, etc.) that form inclusions are less likely to be concentrated in the steel. The formation of inclusions and the growth of precipitates are suppressed. Thereby, the "number density of inclusions" and the "integration degree of inclusions (that is, the number density in the section where the number density of inclusions is in the top 10%)" can be set in the above range.
Therefore, the cooling rate of the vertical part should be 0.5 ° C / sec or more.
The lower limit of the vertical portion cooling rate is preferably 1.0 ° C./sec or higher.
However, the upper limit of the cooling rate of the vertical part is, for example, 10 ° C./sec or less.
[0082]
-(1-2) The elapsed time from the ejection side of the mold to the bending start part (also referred to as "vertical part elapsed time") is 50 to 500 seconds-
If the elapsed time from the ejection side of the mold to the bending start portion of the steel slab is lengthened, the time required for the inclusions to float and separate on the surface of the molten metal increases, so that the total number of inclusions can be reduced. Thereby, it is possible to reduce the degree of accumulation of inclusions (that is, the number density in the section where the number density of inclusions is in the upper 10%) as well as the number density of inclusions. On the other hand, if the elapsed time is excessively long, the productivity will be hindered and the equipment cost will increase.
Therefore, the elapsed time for the vertical part is 50 to 500 seconds.
The lower limit of the elapsed time of the vertical portion is preferably 75 seconds or more.
The upper limit of the elapsed time of the vertical portion is preferably 300 seconds or less.
[0083]
Here, in the casting process, the secondary cooling zone is cooled by, for example, a mist spray.
[0084]
[(2) Hot rolling process]
In the hot rolling process, the steel slab is hot rolled to obtain a hot rolled plate.
Specifically, in the hot rolling process, for example, a steel slab is roughly rolled and finish-rolled to obtain a hot-rolled plate.
[0085]
Then, the generation of coarse inclusions is suppressed, and the "number density of inclusions" and the "integration degree of inclusions (that is, the number density in the section where the number density of inclusions is the top 10%)" are within the above ranges. From the viewpoint, the hot rolling step of the steel slab is a hot rolling step of the steel slab that satisfies the following conditions.
[0086]
-(2-1) Slab heating temperature is 1200 ° C or higher (preferably 1220-1300 ° C)-
By sufficiently heating the steel slab, alloy carbides such as TiC and some inclusions can be sufficiently dissolved. Thereby, the "number density of inclusions" and the "integration degree of inclusions (that is, the number density in the section where the number density of inclusions is in the top 10%)" can be set in the above range.
Therefore, the slab heating temperature should be 1200 ° C or higher.
The lower limit of the slab heating temperature is preferably 1220 ° C. or higher.
However, the upper limit of the slab heating temperature is, for example, 1300 ° C. or less from the viewpoint of controlling fuel cost and durability of the heating furnace.
The slab heating temperature is the temperature at the time of slab extraction.
[0087]
-(2-2) The rolling ratio at the temperature T TiS B1 or less represented by the formula (B) is 95% or less-
In the present disclosure, in the casting process, after suppressing the formation of inclusions and the growth of precipitates, attention is paid to the precipitation temperature of TiS among the inclusions, and the accumulation of coarse inclusions due to hydrogen brittle cracking is performed. Suppress. The reason is that when excessive hot rolling is performed after the TiS is deposited, the TiS is excessively elongated in the rolling direction, so that the maximum diameter of the finally formed inclusions becomes large. Since such inclusions having a large maximum diameter adversely affect the hydrogen brittle property, the rolling ratio below the precipitation temperature of TiS is limited.
"Rolling rate" at temperature T TiS B1 or less means the total rolling rate at temperature T TiS B1 or less. The total rolling ratio means the degree of change in the plate thickness due to rolling, and is the plate thickness reduction rate at the end of hot rolling when the plate thickness at the temperature T TiS B1 is 100%.
In the hot rolling step, if hot rolling with a high total rolling ratio is performed after TiS is deposited, the maximum diameter increases because the TiS is stretched. That is, when hot rolling is carried out by reducing the total rolling ratio after the TiS is deposited, the stretching of the TiS is suppressed and the coarsening of the inclusions as a whole is suppressed. Thereby, the "number density of inclusions" and the "integration degree of inclusions (that is, the number density in the section where the number density of inclusions is in the top 10%)" can be set in the above range.
Therefore, the rolling ratio at the temperature T TiS B1 or less represented by the formula (B1) is 95% or less.
The upper limit of the rolling ratio at the temperature T TiSB 1 or less is preferably 90% or less, and more preferably 85% or less.
The lower limit of the rolling ratio at the temperature T TiSB 1 or less is, for example, 0% or more.
[0088]
[Number 1]

[0089]
The temperature T TiS B1 represented by the formula (B1) is the temperature at which TiS precipitates. Then, in the formula (B1), the element symbol indicates the mass% of the corresponding element. The unit of the temperature T TiS B1 represented by the formula (B1) is Kelvin (K).
As the solubility product of TiS, the empirical formula shown in the following formula (B) has been reported (see W.J. LIU, ISIJ International, Vol. 30, No. 11, pp. 985-990). However, the following formula (B) is an empirical formula obtained by an equilibrium experiment using an ultra-low carbon steel plate. Since the steel plate of the present disclosure has a high amount of alloying elements such as carbon and hot rolling is a phenomenon of a relatively short time, it is assumed that the equilibrium state has not been reached. Therefore, the precipitation temperature of TiS is set. It may be lower than the following formula (B). Therefore, the inventor further investigated, and the temperature at which TiS is deposited is actually the temperature T TiS B1 represented by the above formula (B1).I found that it fits.
[0090]
[Number 2]

[0091]
In formula (B), the element symbol indicates the mass% of the corresponding element. The unit of the temperature T TiS represented by the formula (B) is also Kelvin (K).
It should be noted that the above rolling control exhibits a better effect when the casting conditions of the slab satisfy the scope of the present disclosure. Although the detailed mechanism is unknown, if the casting conditions do not meet the predetermined range of the present disclosure, the segregation degree of Ti and S in the slab may be increased. As a result, since the concentration of Ti and S is high in the segregated portion, there is a possibility that TiS is deposited from a temperature higher than that of T TiS.
[0092]
Here, in the hot rolling process, for example, finish rolling is carried out at a finish rolling temperature of 800 to 1100 ° C. Then, the hot-rolled plate after hot rolling is wound at, for example, a winding temperature of 400 to 700 ° C.
[0093]
The slab heating temperature, finish rolling temperature, and winding temperature are the surface temperatures of the central portion of the steel slab or plate in the width direction.
[0094]
[(3) Pickling and cold rolling steps]
The hot-rolled plate may be pickled and then cold-rolled to obtain a cold-rolled plate, and then the continuous annealing step described later may be performed. The conditions for pickling and cold rolling may be general conditions. The cold rolling process is an arbitrary process.
[0095]
[(4) Continuous annealing process]
In the continuous annealing process, continuous annealing is performed on a hot-rolled plate or a cold-rolled plate.
Specifically, in the continuous annealing step, the hot-rolled plate or the cold-rolled plate is heated, held at the maximum heating temperature for a predetermined time (heating step), and then subjected to primary cooling, secondary cooling, and low-temperature holding. Obtain an annealed plate.
[0096]
Then, from the viewpoint of obtaining the desired steel structure, stabilizing the retained austenite, and satisfying the formula (A), the continuous annealing step satisfying the following conditions is performed.
[0097]
-(4-1) The maximum heating temperature is Ac 3 to 950 ° C, and the holding time at the maximum heating temperature is less than 240 seconds-
In the heating step, in order to obtain the desired steel structure, the hot-rolled plate or cold-rolled plate is sufficiently heated to be austenite. However, if the holding time at the maximum heating temperature is long, the crystal grain size becomes coarse, the fuel cost increases, and the equipment is damaged.
Therefore, the maximum heating temperature is Ac 3 to 950 ° C., and the holding time at the maximum heating temperature is less than 240 seconds.
The lower limit of the maximum heating temperature is preferably Ac 3 + 10 ° C. or higher. The upper limit of the maximum heating temperature is preferably 920 ° C. or lower.
The upper limit of the holding time at the maximum heating temperature is preferably 200 seconds or less. However, from the viewpoint of sufficient austenite formation, the lower limit of the holding time at the maximum heating temperature is, for example, 50 seconds or more.
The "holding" at a predetermined temperature in the heating step does not necessarily have to hold the steel plate at a constant temperature, and may vary within a range that satisfies the above conditions.
[0098]
Ac 3 (° C) can be calculated by the following formula.
Ac 3 = 912-230.5C + 31.6Si-20.4Mn-39.8Cu-18.1Ni-14.8Cr + 16.8Mo + 100Al
However, each element symbol in the formula indicates the mass% of the corresponding element. When the content is 0, 0 is substituted into the formula for calculation.
[0099]
Here, the heating step may be carried out in an atmosphere having a dew point of −50 to + 10 ° C. and a hydrogen concentration of 1 to 5% by volume, for example.
[0100]
-(4-2) The average cooling rate between 400 and 700 ° C in the primary cooling step of cooling from the maximum heating temperature to 400 ° C or less is 30 ° C / sec or more-
In the primary cooling step, when a hot-rolled plate or a cold-rolled plate (referred to as a heat-treated plate) heat-treated from the maximum heating temperature to 400 ° C. or lower is cooled and the heat-treated plate is rapidly cooled between 400 and 700 ° C. It is possible to suppress the formation of steel structures other than martensite.
Therefore, the average cooling rate between 400 and 700 ° C is 30 ° C / sec or more.
The lower limit of the average cooling rate is preferably 40 ° C./sec.
However, it is difficult to set the cooling rate to 200 ° C / sec or higher due to the capacity of the cooling equipment.
[0101]
The upper limit of the primary cooling stop temperature is preferably 380 ° C. or lower.
However, it is desirable that the lower limit of the primary cooling stop temperature is Ms-60 ° C or higher in which a certain amount of untransformed austenite remains in order to distribute C to austenite.
[0102]
-(4-3) The average cooling rate between the primary cooling stop and the secondary cooling stop in the secondary cooling step of cooling to the range of 100 ° C to Ms-120 ° C after the primary cooling stop is 1 to 20 ° C / Seconds-
In the secondary cooling step, after the primary cooling is stopped, the heat treatment plate is cooled to a range of 100 ° C to Ms-120 ° C, and the cooling rate of the heat treatment plate is reduced between the primary cooling stop and the secondary cooling stop. C, Mn and the like can be concentrated in untransformed austenite, and more stable retained austenite can be present. That is, after the primary cooling is stopped, the average cooling rate is set to 1 to 20 ° C / sec, and the ultimate cooling temperature is set to 100 ° C to Ms-120 ° C. You will be satisfied. If the cooling rate of the heat treatment plate is less than 1 ° C./sec, the martensite area ratio becomes low. If the cooling rate of the heat treatment plate exceeds 20 ° C./sec, stable retained austenite cannot be present, which is not preferable.
Therefore, the average cooling rate between the primary cooling stop and the secondary cooling stop is 1 to 20 ° C / sec.
The lower limit of the average cooling rate is preferably 5 ° C./sec or higher.
The upper limit of the average cooling rate is preferably 18 ° C./sec or less.
[0103]
Ms (° C) can be calculated by the following formula.
Ms = 561-474C-33Mn-17Cr-21Mo-7.5Si + 10Co
However, each element symbol in the formula indicates the mass% of the corresponding element. When the content is 0, 0 is substituted into the formula for calculation.
[0104]
Further, each temperature in the continuous annealing process is the surface temperature of the central portion in the width direction of the hot rolled plate or the cold rolled plate. Then, the average cooling rate is calculated based on the surface temperature of the central portion in the width direction of the cold rolled plate.
[0105]
-(4-4) Holding time of 150 seconds or more in the low temperature holding step of holding in the range of 200 to 320 ° C after secondary cooling-
After cooling to the ultimate cooling temperature, hold the heat treatment plate in the range of 200 to 320 ° C. In the low temperature holding step, by holding the heat treatment plate in the range of 200 to 320 ° C. after the start of martensite formation, C, Mn and the like are concentrated in untransformed austenite, and the retained austenite is stabilized. That is, the equation (A) is satisfied. In addition, the martensite is rebaked as it is baked, and the ratio of the rebaked martensite to the total martensite increases. That is, the ratio of burnt-back martensites to all martensites satisfies the above range.
Therefore, the holding time should be 150 seconds or more.
The lower limit of the holding time is preferably 200 seconds or more.
However, from the viewpoint of productivity, the upper limit of the holding time is, for example, 1000 seconds or less.
Note that "holding" in the low temperature holding step means keeping the predetermined temperature within the range of ± 20 ° C, preferably ± 10 ° C within the range not exceeding the upper and lower limits of the holding temperature. Therefore, the heating operation and the cooling operation that fluctuate above 40 ° C. within the temperature range specified in the low temperature holding step by gradually cooling or gradually heating are included in the low temperature holding step in the present disclosure. Not included.
Here, if the holding temperature of the low temperature holding step exceeds 320 ° C., the tempering of martensite proceeds excessively, so that the strength decreases. On the other hand, if the holding temperature in the low temperature holding step is less than 200 ° C., carbon distribution from martensite to austenite is less likely to occur, so that retained austenite is less likely to be stabilized. Therefore, the holding temperature in the low temperature holding step is set to 200 to 320 ° C.
If the low temperature holding step is not carried out, the retained austenite will not be stabilized and the formula (A) will not be satisfied.
[0106]
[Other processes]
A post-process such as a plating step of forming a plating layer on one side or both sides of the steel plate may be carried out on the steel plate obtained by the steel plate manufacturing method of the present disclosure. Post-processes such as the plating process can be performed by a conventional method.
Example
[0107]
Hereinafter, examples of the steel plate of the present disclosure will be described.
A 240 mm thick steel slab was cast from molten steel having the chemical composition shown in Table 1 under the conditions shown in Table 2 by a vertical bending type continuous casting facility having a vertical portion.
Next, the steel slab was hot-rolled under the conditions shown in Table 2, and a hot-rolled plate having a thickness of 3.0 mm was obtained and wound.
Next, after pickling the hot-rolled plate, it was cold-rolled under the conditions shown in Table 2 to obtain a cold-rolled plate. When the cold rolling ratio is 0%, it means that the cold rolling was not performed.
Next, the cold rolled plate was continuously annealed under the conditions shown in Table 2 to obtain the target steel plate. However, in Table 2, the value in the column of "T TiSB 1" is shown in degrees Celsius (° C.). That is, in order to use the notation in degrees Celsius (° C.), the value obtained by subtracting 273.15 from the value (unit: K) calculated by the formula (B1) is described.
In Table 3, the example described as "CR" in the "surface" column indicates an example in which a steel plate is obtained without plating after cold spreading, and is described as "EG". Shows an example in which a plated steel plate is obtained by performing electrozinc plating after cold spreading.
[0108]
The following characteristics were measured for the obtained steel plate according to the method described above.
-The cross section of the steel plate in the rolling direction, in the range of 1/8 to 3/8 thickness centered on 1/4 thickness from the surface of the steel plate. Site ratio (denoted as "burnback ratio" in the table), retained austenite (denoted as "residual γ" in the table), baynite)
-The number density of inclusions satisfying the maximum diameter ≥ 3 μm in the measurement region in the range of 1/8 thickness to 7/8 thickness × 25 mm from the surface of the steel plate in the rolling direction cross section of the steel plate (in the table). , Notated as "average" of the number density of inclusions.)
-The number of inclusions When the measurement area of ​​the density is divided into 100 sections divided into two in the thickness direction and 50 in the width direction, and the number density of inclusions satisfying the maximum diameter ≥ 3 μm of each section is calculated, the number of inclusions. Number density in the section where the density is the top 10% (in the table, it is expressed as "top 10% section" of the number density of inclusions)
-Vγ'/ Vγ (area ratio of retained austenite after deep cooling at -196 ° C / area ratio of initial retained austenite) (Note that Vγ'/ Vγ could not be calculated because Vγ'was small. Is written as "-".)
・ Tensile strength of steel plate (denoted as "TS" in the table)
・ Full elongation of steel plate (indicated as "El" in the table)
・ Hole expansion rate of steel plate (denoted as "λ" in the table)
・ Minimum bending radius of steel plate (indicated as "R" in the table)
[0109]
(evaluation)
The obtained steel plate was evaluated for hydrogen brittle resistance under the following conditions.
A 40 mm square test piece was collected from a steel plate, and a punched hole was created near the center of the test piece using a punch with a diameter of 20 mm and a die with a diameter of 20.5 mm. Then, the test piece was immersed in a hydrochloric acid aqueous solution having a hydrochloric acid concentration of 0.01N, 0.1N, or 1N for 48 hours. The amount of liquid was 500 mL per test piece. The hydrochloric acid aqueous solution was replaced with a new aqueous solution after 8 hours and 24 hours had passed. After 48 hours had passed, the test piece was thoroughly washed and dried, and then the end face of the punched hole was observed all around using a microscope to confirm the presence or absence of cracks. The number of n was set to 3, and those in which cracks were found were judged to be NG (failed). For example, if all three bodies were not cracked at 0.01N, it was accepted (OK), and if even one body was found to be cracked at 0.01N, it was rejected (NG).
Then, the case where the hydrogen brittle crack did not occur was described as "OK", and the case where the hydrogen brittle crack did occur was described as "NG".
[0110]
[table 1]

[0111]
[Table 2-1]

[0112]
[Table 2-2]

[0113]
[Table 3-1]

[0114]
[Table 3-2]

[0115]
From the above results, the steel plate of the experimental example of the present disclosure example has a tensile strength of 1470 MPa or more and a high total elongation.It can be seen that the steel plate has excellent hydrogen brittle resistance in the sheared portion.
On the other hand, Experimental Example 6 (Comparative Example) is an example in which the average cooling rate until the surface temperature of the central portion in the width direction of the steel slab first reaches 1000 ° C. or lower in the casting process is low. In Experimental Example 6 (Comparative Example), the number density in the section where the number density of inclusions was in the top 10% became large, and the hydrogen brittle resistance property deteriorated.
Experimental example 7 (comparative example) is an example in which the elapsed time from the ejection side of the mold to the bending start portion of the steel slab in the casting process is short. In Experimental Example 7 (Comparative Example), along with the number density of inclusions, the number density in the section where the number density of inclusions is in the upper 10% increases, and the hydrogen brittle resistance property deteriorates.
Experimental example 8 (comparative example) is an example in which the rolling ratio is high at the temperature T TiSB 1 or less represented by the formula (B1) in the hot rolling process. In Experimental Example 8 (Comparative Example), along with the number density of inclusions, the number density in the section where the number density of inclusions is in the upper 10% increases, and the hydrogen brittle resistance property deteriorates.
Experimental example 9 (comparative example) is an example in which the slab heating temperature is low in the hot rolling process. In Experimental Example 9 (Comparative Example), along with the number density of inclusions, the number density in the section where the number density of inclusions is in the upper 10% increases, and the hydrogen brittle resistance property deteriorates.
Experimental example 10 (comparative example) is an example in which the secondary cooling stop temperature is low in the secondary cooling step. In Experimental Example 10 (Comparative Example), the area ratio of retained austenite was low, and the total elongation (El) deteriorated.
Experimental example 11 (comparative example) is an example in which the average cooling rate between the primary cooling stop and the secondary cooling stop is high in the secondary cooling step. In Experimental Example 11 (Comparative Example), the formula (A) was not satisfied, and the hydrogen brittle resistance property deteriorated.
Experimental example 13 (comparative example) is an example in which the primary cooling temperature is high in the primary cooling step. In Experimental Example 13 (Comparative Example), the baynite area ratio was high, the martensite area ratio was low, and the tensile strength (TS) and hydrogen brittle resistance were deteriorated.
Experimental example 14 (comparative example) is an example in which the holding temperature is high in the low temperature holding step. In Experimental Example 14 (Comparative Example), the area ratio of retained austenite was low, and the tensile strength (TS), total elongation (El), and hydrogen brittle resistance were deteriorated.
Experimental example 15 (comparative example) is an example in which the maximum heating temperature in the continuous annealing step is low. In Experimental Example 15 (Comparative Example), the ferrite area ratio was high, the martensite area ratio was low, and the tensile strength (TS) and hydrogen brittle resistance were deteriorated.
Experimental example 16 (comparative example) is an example in which the average cooling rate is low in the primary cooling step. In Experimental Example 16 (Comparative Example), the baynite area ratio was high, the martensite area ratio was low, and the tensile strength (TS) and hydrogen brittle resistance were deteriorated.
Experimental example 17 (comparative example) is an example in which the holding time is short in the low temperature holding step. In Experimental Example 17 (Comparative Example), the formula (A) was not satisfied, and the hydrogen brittle resistance property deteriorated.
Experimental example 20 (comparative example) is an example in which the holding temperature is low in the low temperature holding step. Experimental Example 20 (in Comparative Example) did not satisfy the formula (A), and the hydrogen brittle resistance property deteriorated.
Experimental example 26 (comparative example) is an example in which the cooling stop temperature is low and the average cooling rate is high in the secondary cooling step. In Experimental Example 26 (Comparative Example), the residual austenite area ratio was low and the total elongation (El) deteriorated.
Experimental example 29 (comparative example) is an example in which the average cooling rate is low in the secondary cooling step. In Experimental Example 29 (Comparative Example), the baynite area ratio was high, the martensite area ratio was low, and the tensile strength (TS) and hydrogen brittle resistance were deteriorated.
Experimental examples 37 to 44 (comparative examples) are examples in which the chemical composition of the steel plate does not satisfy the chemical composition of the present disclosure. In Experimental Examples 37 to 44 (Comparative Examples), the tensile strength (TS) deteriorated or the hydrogen brittle resistance property deteriorated.
Experimental example 45 (comparative example) is an example in which slow cooling was carried out at 3 ° C./s from 260 ° C. to 150 ° C. instead of keeping at a low temperature in the continuous annealing step. In Experimental Example 45 (Comparative Example), the formula (A) was not satisfied, and the hydrogen brittle resistance property deteriorated.
[0116]
The explanation of the code is as follows.
10 Continuous casting equipment
11 Vertical part from the outlet side of the mold to the bending start part
12 Bending part
20 mold
30 Immersion nozzle for supplying molten steel to the mold
31 Discharge port of molten steel of immersion nozzle
40 Support roll
50 steel slab
[0117]
The entire disclosure of Japanese Patent Application No. 2019-160683 is incorporated herein by reference in its entirety.
All documents, patent applications, and technical standards described herein are as specifically and individually stated that the individual documents, patent applications, and technical standards are incorporated by reference. Incorporated by reference herein.
The scope of the claims
[Claim 1]
By mass%
C: 0.18% to 0.35%,
Si: 0.01% to 1.00%,
Mn: 0.10% to 2.40%,
P: 0.050% or less,
S: 0.0050% or less,
Al: 0.001% to 1.00%,
Ti: 0.001% to 0.050%,
B: 0.0005% -0.0050%,
N: 0.0100% or less,
O: 0.0050% or less,
Cr: 0% to 1.00%,
Mo: 0% to 0.50%,
Cu: 0% to 0.50%,
Ni: 0% to 0.50%,
Co: 0% to 0.50%,
W: 0% to 0.50%,
Sn: 0% to 0.50%,
Sb: 0% to 0.50%,
Nb: 0% to 0.050%,
V: 0% to 0.50%,
Ca: 0% to 0.0100%,
Mg: 0% -0.0100%,
Ce: 0% -0.0100%,
Zr: 0% -0.0100%,
La: 0% -0.0100%,
Hf: 0% to 0.0100%,
Bi: 0% to 0.0100%, and
REM: Contains 0% to 0.0100% and
Formula: 0.001 ≦ Ti− (47.88 / 14.01) × N ≦ 0.040 (However, in the formula, the element symbol indicates the mass% of the corresponding element).
The balance has a chemical composition consisting of Fe and impurities,
In the rolling direction cross section of the steel plate, the steel structure in the range of 1/8 thickness to 3/8 thickness centered on 1/4 thickness from the surface of the steel plate has an area ratio of%.
Ferrite: 0-5%,
Martensite: 90.0-99.5%,
Percentage of burnt-back martensites in all martensites: 80.0-100.0%
Residual austenite: 0.5-6.0%
Contains,
The number density of inclusions satisfying the maximum diameter ≧ 3 μm in the measurement region in the range of 1/8 thickness to 7/8 thickness × 25 mm from the surface of the steel plate in the rolling direction cross section of the steel plate is 40 pieces / mm 2 or less,
When the measurement area was divided into 100 sections divided into two in the thickness direction and 50 in the width direction, and the number density of the inclusions satisfying the maximum diameter ≥ 3 μm of each section was calculated, the number density was the top 10%. The number density in the section is 80 pieces / mm 2 or less, and
Satisfying the following formula (A),
A steel plate with a tensile strength of 1470 MPa or more.
Vγ'/ Vγ ≧ 0.1 ... (A)
Vγ: area ratio of initial retained austenite, Vγ': area ratio of retained austenite after deep cooling at -196 ° C.
[Claim 2]
The steel plate according to claim 1, wherein in the measurement region, the number density of inclusions satisfying the maximum diameter ≥ 3 μm is 30 pieces / mm 2 or less.
[Claim 3]
The steel plate according to claim 1 or claim 2, wherein the number density in the section where the number density is the top 10% is 60 pieces / mm 2 or less.
[Claim 4]
The steel plate according to any one of claims 1 to 3 that satisfies the following formula (A2).
Vγ'/ Vγ ≧ 0.2 ... (A2)
Vγ: area ratio of initial retained austenite, Vγ': area ratio of retained austenite after deep cooling at -196 ° C.