WO2016114146A1 - 厚肉高靭性高強度鋼板およびその製造方法 - Google Patents

厚肉高靭性高強度鋼板およびその製造方法 Download PDF

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WO2016114146A1
WO2016114146A1 PCT/JP2016/000197 JP2016000197W WO2016114146A1 WO 2016114146 A1 WO2016114146 A1 WO 2016114146A1 JP 2016000197 W JP2016000197 W JP 2016000197W WO 2016114146 A1 WO2016114146 A1 WO 2016114146A1
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Prior art keywords
toughness
less
steel sheet
thick
point
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PCT/JP2016/000197
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English (en)
French (fr)
Japanese (ja)
Inventor
茂樹 木津谷
克行 一宮
長谷　和邦
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Ｊｆｅスチール株式会社
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Application filed by Ｊｆｅスチール株式会社 filed Critical Ｊｆｅスチール株式会社
Priority to EP16737217.6A priority Critical patent/EP3246426B1/en
Priority to US15/543,364 priority patent/US20170369958A1/en
Priority to SG11201704242TA priority patent/SG11201704242TA/en
Priority to CN201680005979.9A priority patent/CN107208212B/zh
Priority to CA2969200A priority patent/CA2969200C/en
Priority to JP2016532648A priority patent/JP6048626B1/ja
Priority to KR1020177019203A priority patent/KR101994784B1/ko
Publication of WO2016114146A1 publication Critical patent/WO2016114146A1/ja

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    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
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    • B21B1/024—Forging or pressing
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    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
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    • B21B1/026—Rolling
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    • B21B2001/028—Slabs
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
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    • C21D2211/00—Microstructure comprising significant phases
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    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
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Definitions

  • the present invention relates to a thick, high-toughness, high-strength steel sheet used for steel structures such as buildings, bridges, shipbuilding, marine structures, construction machinery, tanks, and penstock, and a method for producing the same.
  • This invention is excellent in the toughness of a steel plate surface, the intensity
  • the steel sheet has a thickness of 100 mm or more and a yield strength of 620 MPa or more.
  • bainite or a mixed structure of bainite and martensite is formed in the thickness center during quenching. It is important to let For this purpose, it is necessary to add a large amount of alloy elements such as Mn, Ni, Cr, and Mo.
  • a martensitic structure is formed on the surface of the steel sheet, which has a higher cooling rate and lower toughness than the thickness center part. Therefore, in a high-strength steel plate having a thickness of 100 mm or more, it is difficult to achieve both surface toughness and strength and toughness inside the steel plate.
  • Non-Patent Document 1 describes a material with a plate thickness of 210 mm
  • Non-Patent Document 2 describes a material with a plate thickness of 180 mm.
  • the above non-patent document describes that the strength and toughness of the central portion of the plate thickness are good. However, there is no description about the toughness (Charpy impact property) of the steel sheet surface. Such thick materials are usually manufactured by a quenching and tempering process, but a martensite structure is formed on the surface of the steel plate, which has a faster cooling rate than the center of the plate thickness, and the toughness of the steel plate surface (Charpy impact properties). In view of the decrease in the thickness, the above-mentioned non-patent document does not describe the point of manufacturing a steel sheet that stably satisfies the toughness of the steel sheet surface.
  • the present invention has been made to solve the above-mentioned problems, and its object is to provide a thick-walled, high-toughness, high-strength steel sheet having both surface toughness and strength and toughness inside the steel sheet, and a method for producing the same. There is.
  • the inventors have made a microstructure for achieving both the toughness of the steel sheet surface and the strength and toughness at the center of the sheet thickness for a thick steel sheet having a yield strength of 620 MPa or more and a sheet thickness of 100 mm or more.
  • % which is the unit of the said ratio means volume%.
  • the steel composition (component composition) is appropriately selected and the cooling rate is low. It is also important that the microstructure can be martensite and / or bainite. For this purpose, it is necessary to appropriately select alloy components, and in particular, the carbon equivalent (Ceq) needs to be 0.65% or more. In addition to appropriate component design, it is also important to create a structure by hot working and heat treatment.
  • the present invention has been made by further studying the above knowledge, and provides the following.
  • Ceq IIW C + Mn / 6 + (Cu + Ni) / 15 + (Cr + Mo + V) /5 ⁇ 0.65 (1) (C L -C) / C L ⁇ 100 ⁇ 30 (2)
  • CL is defined by the following equation.
  • C L 0.2 ⁇ ( ⁇ 0.1 ⁇ (0.2 ⁇ Si) ⁇ 0.03 ⁇ (1.1 ⁇ Mn) ⁇ 0.12 ⁇ (0.2 ⁇ Cu) ⁇ 0.11 ⁇ ( 3-Ni) + 0.025 ⁇ (1.2-Cr) + 0.1 ⁇ (0.5-Mo) + 0.2 ⁇ (0.04-V) ⁇ 0.05 ⁇ (0.06-Al)) (3)
  • the element symbol is the content (% by mass) of each alloy component, and 0 is not included.
  • Mg 0.0001 to 0.0050%
  • Ta 0.01 to 0.20%
  • Zr 0.005 to 0.1%
  • Y 0.001 to 0.00.
  • [6] A method for producing a thick, high toughness and high strength steel sheet according to any one of [1] to [5], wherein the steel material is heated to 1200 to 1350 ° C., and the cumulative reduction amount is 25% or more.
  • the hot forging is performed and heated to Ac3 point or higher and 1200 ° C or lower, hot rolled to a cumulative reduction of 40% or higher, allowed to cool, reheated to Ac3 point or higher and 1050 ° C or lower, and Ac3 point.
  • a method for producing a thick, high-toughness, high-strength steel sheet characterized by quenching from the above temperature to a lower temperature of 350 ° C. or lower or an Ar 3 point or lower and tempering at a temperature of 450 ° C. to 700 ° C.
  • a thick, high-toughness, high-strength steel sheet characterized by being rapidly cooled from a temperature of Ar 3 point or higher to 350 ° C or lower or a lower temperature of Ar 3 or lower and tempered at a temperature of 450 ° C. to 700 ° C. Method.
  • [8] A method for producing the thick, high toughness and high strength steel sheet according to any one of [1] to [5],
  • the steel material is heated to 1200 to 1350 ° C. and subjected to partial rolling to make the cumulative reduction amount 40% or more, and heated to the Ac3 point or more and 1200 ° C. or less, and the hot rolling to make the cumulative reduction amount 40% or more.
  • a method for producing a thick-walled, high-toughness, high-strength steel sheet is a method for producing a thick-walled, high-toughness, high-strength steel sheet.
  • the present invention it is possible to obtain a thick high toughness high strength steel sheet having a thickness of 100 mm or more and having a yield strength of 620 MPa or more and excellent toughness. If this thick-walled high-toughness high-strength steel plate is used, a steel structure with high safety can be produced.
  • the composition of the thick-walled, high-toughness, high-strength steel sheet of the present invention is, by mass, C: 0.08 to 0.20%, Si: 0.40% or less (including 0%), Mn: 0.0. 5 to 5.0%, P: 0.010% or less (including 0%), S: 0.0050% or less (including 0%), Cr: 3.0% or less (provided that 0) %), Ni: 0.1 to 5.0%, Al: 0.010 to 0.080%, N: 0.0070% or less (including 0%), O: 0.0025% or less (However, 0% is included).
  • C 0.08 to 0.20%
  • Si 0.40% or less
  • Mn 0.0. 5 to 5.0%
  • P 0.010% or less
  • S 0.0050% or less
  • Cr 3.0% or less
  • Ni 0.1 to 5.0%
  • N: 0.0070% or less including 0%
  • O 0.0025% or less
  • C 0.08 to 0.20%
  • C is an element useful for obtaining the strength required for structural steel at a low cost. In order to obtain the effect, the C content needs to be 0.08% or more. On the other hand, when the C content exceeds 0.20%, the toughness of the base metal and the welded portion is significantly deteriorated when a steel structure is produced by welding using a thick, high toughness and high strength steel plate. Therefore, the upper limit of the C content is set to 0.20%. The preferred C content is 0.08% to 0.14%.
  • Si 0.40% or less Si is added for deoxidation.
  • the steel sheet of the present invention may not contain Si. If the Si content exceeds 0.40%, the toughness of the base metal and the weld heat affected zone is significantly reduced when a steel structure is produced by welding using a thick, high toughness, high strength steel sheet. For this reason, Si content shall be 0.40% or less.
  • a preferred Si content is in the range of 0.05 to 0.3%. More preferably, it is in the range of 0.1 to 0.3%.
  • Mn 0.5 to 5.0% Mn is added from the viewpoint of securing the strength of the base material. If the Mn content is less than 0.5%, the effect is not sufficient. Further, when the Mn content exceeds 5.0%, the center segregation is promoted, the casting defect of the slab becomes large, and when the steel structure is manufactured by welding using a thick-walled high-toughness high-strength steel plate, The characteristics of the will deteriorate. Therefore, the upper limit of the Mn content is 5.0%.
  • the Mn content is preferably in the range of 0.6 to 2%, more preferably 0.6 to 1.6%.
  • the P content exceeds 0.010%, the toughness of the base material and the weld heat-affected zone is reduced when a steel structure is produced by welding using a thick, high-toughness, high-strength steel sheet. It drops significantly.
  • the P content is preferably as small as possible (it may not be included), and is limited to 0.010% or less.
  • the S content exceeds 0.0050%, when a steel structure is manufactured by welding using a thick-walled high-toughness high-strength steel sheet, the toughness of the base material and the weld heat-affected zone is low. Remarkably reduced. For this reason, the S content is preferably as small as possible (it may not be included), and is made 0.0050% or less.
  • Cr 3.0% or less Cr is an element effective for increasing the strength of the base material. However, when the Cr content is excessive, the weldability is lowered. Therefore, the Cr content is 3.0% or less.
  • a preferable Cr content is 0.1% to 2%. More preferably, it is in the range of 0.7% to 1.7%. Further, the Cr content may be 0%.
  • Ni 0.1-5.0%
  • Ni is a beneficial element that improves the strength of the steel and the toughness of the heat affected zone. In order to obtain this effect, the Ni content is set to 0.1% or more. On the other hand, if the Ni content exceeds 5.0%, the economic efficiency is significantly reduced. Therefore, the upper limit of the Ni content is 5.0%.
  • the Ni content is preferably 0.4 to 4%, more preferably 0.8% to 3.8%.
  • Al 0.010 to 0.080% Al is added to sufficiently deoxidize the molten steel. If the Al content is less than 0.010%, the effect is insufficient. On the other hand, when the Al content exceeds 0.080%, when a steel structure is produced by welding using a thick, high toughness, high strength steel sheet, the Al content that is dissolved in the base material increases, The toughness of the material decreases. Therefore, the Al content is set to 0.080% or less.
  • the Al content is preferably in the range of 0.030 to 0.080%, more preferably in the range of 0.030 to 0.070%.
  • N 0.0070% or less
  • N is a base material and weld when a microstructure is formed by forming a nitride with Ti or the like, and a steel structure is manufactured by welding using a thick, high toughness, high strength steel plate. It has the effect of improving the toughness of the heat affected zone. Since the effect of improving toughness can be obtained by a configuration other than N, the steel plate of the present invention may not contain N. However, from the viewpoint of obtaining this effect with N, the N content is preferably 0.0015% or more. On the other hand, when the N content exceeds 0.0070%, when a steel structure is produced by welding using a thick, high toughness, high strength steel plate, the amount of N dissolved in the base material increases.
  • the toughness is remarkably lowered, and coarse carbonitride is formed also in the weld heat affected zone, and the toughness is lowered. Therefore, the N content is set to 0.0070% or less. Preferably, it is 0.006% or less, more preferably 0.005% or less.
  • O 0.0025% or less
  • the thick, high toughness and high strength steel sheet of the present invention can contain at least one of Cu, Mo, V, Nb and Ti for the purpose of further increasing the strength and / or toughness in addition to the above elements. .
  • Cu 0.50% or less If Cu is contained, the strength of steel can be improved without impairing toughness. If the Cu content exceeds 0.50%, the steel sheet surface may be cracked during hot working. Therefore, when Cu is contained, its content is set to 0.50% or less.
  • Mo 1.50% or less Mo contributes to increasing the strength of a base material when a steel structure is produced by welding using a thick, high-toughness, high-strength steel sheet. However, if the Mo content exceeds 1.50%, the hardness increases due to precipitation of alloy carbides, and the toughness decreases. Therefore, when Mo is contained, the upper limit of the Mo content is set to 1.50%. A preferable Mo content is in the range of 0.2% to 0.8%.
  • V 0.400% or less V contributes to the improvement of the strength and toughness of the base metal when a steel structure is produced by welding using a thick, high toughness, high strength steel plate. Further, V is effective for lowering solid solution N by precipitating as VN. However, if the V content exceeds 0.400%, the toughness decreases due to precipitation of hard VC. Therefore, when V is added, the V content is preferably 0.400% or less. More preferably, it is in the range of 0.01 to 0.1%.
  • Nb 0.100% or less Nb is effective because it is effective in improving the strength of the base material.
  • the upper limit of the Nb content is set to 0.100%. Preferably, it is 0.025% or less.
  • Ti 0.005 to 0.020% Ti produces TiN during heating, effectively suppresses coarsening of austenite, and when steel structures are produced by welding using thick, high toughness, high strength steel sheets, the toughness of the base metal and the weld heat affected zone To improve.
  • the Ti content exceeds 0.020%, the Ti nitride becomes coarse and the toughness of the base material is lowered. Therefore, when Ti is contained, the Ti content is in the range of 0.005% to 0.020%. Preferably, it is in the range of 0.008% to 0.015%.
  • the thick-walled high-toughness high-strength steel sheet of the present invention can contain at least one of Mg, Ta, Zr, Y, B, Ca, and REM for the purpose of further improving the material. .
  • Mg 0.0001 to 0.0050%
  • Mg is an effective element for forming a stable oxide at a high temperature, effectively suppressing the coarsening of old ⁇ grains in the weld heat affected zone, and improving the toughness of the weld zone.
  • the Mg content is set to 0.0001% or more. However, if the Mg content exceeds 0.0050%, the amount of inclusions increases and the toughness decreases. Therefore, when Mg is contained, its content is preferably 0.0050% or less. More preferably, it is in the range of 0.0001% to 0.015%.
  • Ta 0.01-0.20% Adding an appropriate amount of Ta is effective for improving the strength. Specifically, it is effective to make the Ta content 0.01% or more. However, when the content exceeds 0.20%, the toughness decreases due to the formation of precipitates. Therefore, when Ta is contained, its content is set to 0.01% to 0.20%.
  • Zr 0.005 to 0.1%
  • Zr is an element effective for increasing the strength. In order to obtain this effect, it is effective to make the Zr content 0.005% or more. On the other hand, when the Zr content exceeds 0.1%, coarse precipitates are generated and the toughness is lowered. Therefore, when Zr is contained, the content is made 0.005 to 0.1%.
  • Y 0.001 to 0.01%
  • Y is an element effective for forming a stable oxide at a high temperature, effectively suppressing the coarsening of the old ⁇ grains in the weld heat affected zone, and improving the toughness of the weld zone. In order to obtain this effect, it is effective to make the Y content 0.001% or more. However, if the Y content exceeds 0.01%, the amount of inclusions increases and the toughness decreases. Therefore, when Y is contained, the content is made 0.001 to 0.01%.
  • B 0.0030% or less B has the effect of suppressing the ferrite transformation from the grain boundary by segregating at the austenite grain boundary and increasing the hardenability. However, if the B content exceeds 0.0030%, B precipitates as a carbonitride, lowering the hardenability and lowering the toughness. Therefore, the B content is set to 0.0030% or less. When B is contained, its content is preferably in the range of 0.0003 to 0.0030%. More preferably, it is in the range of 0.0005 to 0.002%.
  • Ca 0.0005 to 0.0050%
  • Ca is an element useful for controlling the morphology of sulfide inclusions. In order to exhibit the effect, it is necessary to make Ca content 0.0005% or more. However, if the Ca content exceeds 0.0050%, the cleanliness is lowered and the toughness is deteriorated. Therefore, when Ca is contained, its content is preferably 0.0050% or less. More preferably, it is in the range of 0.0005% to 0.0025%.
  • REM 0.0005 to 0.0100% REM also has the effect of improving material quality by forming oxides and sulfides in steel like Ca.
  • the REM content needs to be 0.0005% or more.
  • the REM content is saturated.
  • the content shall be 0.0100% or less.
  • the preferred REM content is in the range of 0.0005 to 0.005%.
  • Ceq IIW ⁇ 0.65%
  • Ceq IIW C + Mn / 6 + (Cu + Ni) / 15 + (Cr + Mo + V) /5 ⁇ 0.65 (1)
  • each element symbol in a formula shows content (mass%) of each element. In addition, 0 is not included.
  • a steel plate having good characteristics can be obtained even when it is manufactured from a steel material cast at a cooling rate of 1 ° C./s or less when the slab surface is solidified. .
  • the cooling rate during solidification of the slab surface is 1 ° C./s.
  • the primary crystal at the time of solidification must be the ⁇ phase, and the ratio of the ⁇ phase at the start of the ⁇ phase generation ((C L -C) / C L ⁇ 100) must be 30% or more.
  • C L 0.2 ⁇ ( ⁇ 0.1 ⁇ (0.2 ⁇ Si) ⁇ 0.03 ⁇ (1.1 ⁇ Mn) ⁇ 0.12 ⁇ (0.2 ⁇ Cu) ⁇ 0.11 ⁇ ( 3-Ni) + 0.025 ⁇ (1.2-Cr) + 0.1 ⁇ (0.5-Mo) + 0.2 ⁇ (0.04-V) ⁇ 0.05 ⁇ (0.06-Al)) (3)
  • the element symbol is the content (% by mass) of each alloy component, and 0 is not included.
  • the coefficient was determined based on the result of calculating the influence of the alloy element on the C solid solubility limit (C L ) of the ⁇ phase using the thermodynamic calculation software “Thermo-Calc”. For example, the coefficient “-0.1” of “Si” indicates that when 1% Si is contained, the solid solubility limit of C in the ⁇ phase decreases by 0.1%, and the necessary ⁇ phase ratio is ensured. This indicates that the C content of the base material needs to be reduced.
  • the present invention 0.12% of C as a component on which to base the calculation of C L in 0.2% of Si, and Mn 1.1%, 0.2% and Cu, 1.2% of Cr,
  • the coefficient is calculated by calculating the change from the amount of solute C when the content of each alloy element is changed with Ni 3%, Mo 0.5%, V 0.04% and Al 0.06%. It was.
  • the percentage of C added to the solid solubility limit of C in the ⁇ phase calculated in this way: (C L -C) / C L ⁇ 100 is set to 30% or more, so that at the start of ⁇ phase generation.
  • the ratio of the ⁇ phase can be 30% or more.
  • the diaphragm in the thickness direction at the center of the thickness measured by the method described in the examples is 40% or more.
  • the temperature “° C.” means the temperature at the center of the plate thickness excluding the quenching temperature when quenching without cooling after rolling.
  • the quenching temperature when quenching without cooling after rolling is the steel sheet surface temperature. This is because the steel plate temperature distribution in the plate thickness direction increases during rolling, and it is necessary to consider the temperature drop on the steel plate surface.
  • the temperature at the center of the plate thickness is obtained by simulation calculation or the like from the plate thickness, surface temperature, cooling conditions, and the like. For example, the plate thickness center temperature is obtained by calculating the temperature distribution in the plate thickness direction using the difference method.
  • the partial thickness rolling may be performed to reduce the thickness of the material.
  • Conditions for hot forging of steel material A slab or steel slab having the above composition is heated to 1200 to 1350 ° C. If the reheating temperature is less than 1200 ° C, it will cause an increase in the load to secure the cumulative reduction amount of the predetermined hot working, and it will not be possible to secure a sufficient reduction amount, but it must be heated again during the processing if necessary. In some cases, the production efficiency must be reduced. For this reason, reheating temperature shall be 1200 degreeC or more. Further, when the alloy element addition amount is high as in the case of a steel having a carbon equivalent of 0.65% or more, the casting defects such as center porosity and zaku in the steel material are remarkably coarsened.
  • a slab or steel slab having the above composition is heated to 1200 to 1350 ° C. If the reheating temperature is less than 1200 ° C, it will cause an increase in the load to secure the cumulative reduction amount of the predetermined hot working, and it will not be possible to secure a sufficient reduction amount, but it must be heated again during the processing if necessary. In some cases, the production efficiency must be reduced. For this reason, reheating temperature shall be 1200 degreeC or more. In order to make the casting defect harmless by crimping and to obtain the effect of the present invention, the cumulative rolling amount may be 30% or more, but the cumulative rolling amount is from the viewpoint of excellent drawing (RA). Is preferably 40% or more. On the other hand, if the reheating temperature exceeds 1350 ° C., excessive energy is consumed, surface flaws are likely to occur due to the scale during heating, and the maintenance load after hot forging increases, so the upper limit is made 1350 ° C.
  • the steel material after forging is heated to an Ac3 transformation point or higher and 1200 ° C or lower in order to homogenize the steel into a single austenite structure.
  • the temperature is preferably 1000 ° C. or more and 1200 ° C. or less.
  • Ac3 transformation point a value calculated by the following formula (4) is used.
  • Ac3 937.2-476.5C + 56Si-19.7Mn-16.3Cu-26.6Ni-4.9Cr + 38.1Mo + 124.8V + 136.3Ti + 198.4Al + 3315B (4)
  • Each element symbol in the formula (4) indicates the content (% by mass) of each alloy element.
  • Hot rolling conditions The steel material is processed to a desired thickness by hot rolling.
  • the steel material is processed to a desired thickness by hot rolling.
  • the effect of grain size reduction and refinement of the old ⁇ grain size by heat treatment is fully demonstrated.
  • Construction is necessary. Specifically, by setting the cumulative reduction amount in rolling to 40% or more, it is possible to achieve grain sizing at the rolling stage even in the central portion of the plate thickness where recrystallization due to processing hardly occurs.
  • Heat treatment conditions In order to obtain the strength and toughness at the center of the plate thickness, in the present invention, it is allowed to cool after hot rolling (for example, air cooling) or 350 ° C. from a temperature of Ar 3 point or higher without being allowed to cool after hot rolling. Cool to the following temperature. When it is allowed to cool, it is reheated from Ac 3 point to 1050 ° C. and rapidly cooled from the temperature of Ac 3 point or higher to 350 ° C. or lower. The reheating temperature is set to 1050 ° C.
  • the quenching temperature is set to Ar3 point or higher because quenching is performed from the austenite single phase region.
  • the quenching stop temperature is set to a lower temperature of 350 ° C. or lower or Ar 3 point or lower in order to reliably obtain a transformed structure in the entire steel sheet. That is, the stop temperature needs to be Ar3 point or less and 350 ° C or less.
  • Ar3 transformation point a value calculated by the following formula (5) is used.
  • Ar3 910-310C-80Mn-20Cu-15Cr-55Ni-80Mo (5)
  • Each element symbol in the formula (5) indicates the content (mass%) of each alloy element.
  • the quenching method is generally water cooling industrially, but the cooling rate is preferably as fast as possible. For this reason, the cooling method may be other than water cooling, for example, there is a method such as gas cooling.
  • Tempering conditions The reason for tempering at 450 to 700 ° C. after rapid cooling is as follows. Below 450 ° C., the residual stress removal effect is small. On the other hand, when the temperature exceeds 700 ° C., various carbides precipitate, and when a steel structure is manufactured by welding using a thick, high toughness, high strength steel sheet, the structure of the base material becomes coarse, and the strength and toughness are reduced. Decrease significantly.
  • quenching may be repeated, but at the time of final quenching, it is necessary to heat from Ac 3 point to 1050 ° C., then rapidly cool to 350 ° C. or less, and then temper at 450 to 700 ° C. .
  • [delta] phase fraction for each of the base metal components using the value of the C content value and the base material of C L obtained by formula (3) is a value calculated by equation (2).
  • the cooling rate at the time of solidification when manufacturing the steel material is a value calculated by heat transfer calculation based on data obtained by measuring the temperature of the mold surface with a radiation thermometer.
  • Tensile test A round bar tensile test piece ( ⁇ 12.5 mm, GL50 mm) was sampled in the direction perpendicular to the rolling direction from the center of the thickness of each steel plate, and the yield strength (YS) and tensile strength (TS) were measured.
  • Plate Thickness Direction Tensile Test A plate thickness direction round bar tensile test piece ( ⁇ 10 mm) was collected from a region including the center portion of the thickness of each steel plate, and the drawing (RA) was measured. The drawing is the percentage of the difference between the minimum cross-sectional area and the original cross-sectional area after fracture of the test piece with respect to the original cross-sectional area.
  • test results are shown in Table 2. From these results, the steel sheets (sample Nos. 1 to 21 and 41) of the inventive examples in which the component composition of the steel complies with the present invention are all YS is 620 MPa or more, TS is 720 MPa or more, and the surface of the base material at ⁇ 40 ° C. It can also be seen that the toughness (vE-40) at the center of the plate thickness is 70 J or more, and the strength and toughness of the base material is excellent. No. 5 and 6; Comparison with 41 confirmed that the aperture (RA) was also good when the lump condition met a specific condition.
  • the comparative steel plates (sample Nos. 22 to 32) that deviate from the component composition of the present invention have a YS of the base material of less than 620 MPa, a TS of less than 720 MPa, and a toughness (vE-40) of less than 70 J. It corresponds to any one or more of, and the characteristic is inferior.

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