High-strength high-toughness hot-rolled steel sheet and manufacturing method therefor

Abstract

A preferable aspect of the present invention provides a high-strength high-toughness hot-rolled steel sheet and a manufacturing method therefor, wherein the hot-rolled steel sheet contains, by weight, 0.07-0.13% C, 0.20-0.50% Si, 0.5-0.9% Mn, 0.03% or less P, 0.02% or less S, 0.005-0.03% Nb, 0.3-0.6% Cr, 0.005-0.03% Ti, 0.1-0.35% Cu, 0.05-0.3% Ni, 0.01-0.15% Mo, 0.007% or less N, 0.001-0.006% Ca, 0.01-0.05% Al, and the balance Fe and other unavoidable impurities, the alloy elements satisfying the following relational formulas [Relational formula 1] 1.6≤(Mo/96)/(P/31)≤6, [Relational formula 2] 1.6≤(Ca/S)≤3, and [Relational formula 3] 3.5≤(3*C/12+Mn/55)*100≤5; wherein a microstructure comprises, by area fraction, 85% or more of polygonal ferrite and 15% or less of pearlite, the crystal grain size of the polygonal ferrite being 10 μm or less; and wherein a variation in yield strength in a width direction is 35 MPa or lower.

Claims

1. A high-strength high-toughness hot-rolled steel sheet comprising, by weight percentage (wt %): 0.07 to 0.13% of carbon (C), 0.20 to 0.50% of silicon (Si), 0.5 to 0.9% of manganese (Mn), 0.03% or less of phosphorus (P), 0.02% or less of sulfur (S), 0.005 to 0.03% of niobium (Nb), 0.3 to 0.6% of chromium (Cr), 0.005 to 0.03% of titanium (Ti), 0.1 to 0.35% of copper (Cu), 0.05 to 0.3% of nickel (Ni), 0.01 to 0.15% of molybdenum (Mo), 0.007% or less of nitrogen (N), 0.001 to 0.006% of calcium (Ca), 0.01 to 0.05% of aluminum (Al), and a balance of iron (Fe) and other unavoidable impurities, the alloy elements satisfying Relational Expressions 1 to 3,
1.6≤(Mo/96)/(P/31)≤6,  Relational Expression 1:
1.6≤(Ca/S)≤3, and  Relational Expression 2:
3.5≤(3*C/12+Mn/55)*100≤5,  Relational Expression 3: wherein a microstructure consists of, by area fraction, 85% or more of polygonal ferrite and 15% or less of pearlite and a grain size of the polygonal ferrite is 10 μm or less (excluding 0%), wherein a deviation in yield strength in a width direction is 35 MPa or less, wherein the hot-rolled steel sheet has precipitates in which the number of precipitates of 20 nm or less per mm.sup.2 is 7×10.sup.8 or more, wherein the hot-rolled steel sheet has an impact toughness value measured through a Charpy impact test at temperature of −60° C. of 95 J or more, and separation length on a fracture surface of the impact specimen of 0.01/mm or less, and wherein the hot-rolled steel sheet has a yield strength at room temperature of 520 MPa or more, and a tensile strength at room temperature of 640 MPa or more, wherein yield strength and tensile strength were measured according to ASTM A370.

Description

BEST MODE FOR INVENTION

(1) The present disclosure provides a high-strength high-toughness hot-rolled steel sheet having excellent low-temperature toughness while having a small deviation in strength in a width direction of the steel sheet by optimizing a composition, composition ranges, composition relational expressions, and manufacturing conditions and a method for manufacturing the same.

(2) Hereinafter, a high-strength and high-toughness hot-rolled steel sheet according to an aspect of the present disclosure will be described in detail.

(3) A high-strength high-toughness hot-rolled steel sheet according to an aspect of the present disclosure includes, by weight percentage (wt %): 0.07 to 0.13% of carbon (C), 0.20 to 0.50° of silicon (Si), 0.5 to 0.9% of manganese (Mn), 0.03% or less of phosphorus (P), 0.02% or less of sulfur (S), 0.005 to 0.03% of niobium (Nb), 0.3 to 0.6% of chromium (Cr), 0.005 to 0.03% of titanium (Ti), 0.1 to 0.35% of copper (Cu), 0.05 to 0.3% of nickel (Ni), 0.01 to 0.15% of molybdenum (Mo), 0.007% or less of nitrogen (N), 0.001 to 0.006% of calcium (Ca), 0.01 to 0.05% of aluminum (Al), and a balance of iron (Fe) and other unavoidable impurities, the alloy elements satisfying Relational Expressions 1 to 3,
1.6≤(Mo/96)/(P/31)≤6,  Relational Expression 1:
1.6≤(Ca/S)≤3, and  Relational Expression 2:
3.5≤(3*C/12+Mn/55)*100≤5  Relational Expression 3:

(4) C: 0.07 to 0.13 wt % (Hereinafter, also Referred to “%”)

(5) Carbon (C) is an element increasing hardenability of a steel material. When the content of C is less than 0.07%, the hardenability is insufficient, and thus, desired strength of the present disclosure may not be secured. On the other hand, when the content of C is greater than 0.13%, yield strength is too high, which may cause difficulty in working or deteriorated low-temperature toughness. Therefore, the above contents are not preferable. Therefore, in the present disclosure, the content of C may be controlled to be 0.07 to 0.13%.

(6) Si: 0.20 to 0.50%

(7) Silicon (Si) increases activity of C in a ferrite phase, promotes ferrite stabilization, and is effective in securing strength as a result of solid-solution strengthening. In addition, Si forms an oxide having a low melting point such as Mn.sub.2SiO.sub.4, or the like, during ERW welding and allows the oxide to be easily discharged during welding. When the content of Si is less than 0.2%, a cost problem in steelmaking may occur. Meanwhile, when the content of Si is greater than 0.5%, the amount of formation of a SiO.sub.2 oxide having a high melting point, other than Mn.sub.2SiO.sub.4, may be increased and toughness of a welding zone may be reduced during electric resistance welding. Therefore, the content of Si may be limited to a range of, in detail, 0.20 to 0.50%.

(8) Mn: 0.5 to 0.9%

(9) Manganese (Mn) is an element having a significant effect on an austenite/ferrite transformation initiation temperature and lowering a transformation initiation temperature. In addition, Mn has an effect on toughness of a pipe base portion and a welding zone, and contributes to an increase in strength as a solid-solution strengthening element. When the content of Mn is less than 0.5%, it may be difficult to obtain the above effect. Meanwhile, when the content of Mn is greater than 0.9%, there is a high possibility that a segregation zone is formed. Therefore, the content of Mn may be limited to a range of 0.5 to 0.9%.

(10) P: 0.03% or Less (Including 0%)

(11) Phosphorus (P) is an element unavoidably included when manufacturing steel. When P is added, P may be segregated in a central portion of the steel sheet and may be used as a cracking initiation point or a cracking propagation path. It is theoretically advantageous to limit the content of P to 0%, but P is unavoidably added as an impurity in a manufacturing process. Therefore, it is important to manage an upper limit and, in the present disclosure, the upper limit of the content of P may be limited to, in detail, 0.03%.

(12) S: 0.02% or Less (Including 0%)

(13) Sulfur (S) is an impurity element present in steel and binds to Mn, or the like, to form a nonmetallic inclusion, which leads to significant damage to toughness of the steel. Therefore, since the content of S is preferably reduced as much as possible, an upper limit of the content of S may be set to, in detail, 0.02%.

(14) Nb: 0.005 to 0.03%

(15) Niobium (Nb) is an element significantly useful in suppressing recrystallization during rolling to refine grains and serves to improve strength of steel. Therefore, at least 0.005% or more of Nb should be added. However, when the content of Nb is greater than 0.03%, a Nb carbonitride is precipitated to be harmful to the toughness of the steel. Therefore, the content of Nb may be controlled to be 0.005 to 0.03%.

(16) Cr: 0.3 to 0.6%

(17) Chromium (Cr) is an element improving hardenability and corrosion resistance. When the content of Cr is less than 0.3%, an effect of improving corrosion resistance due to addition of Cr is insufficient. Meanwhile, when the content of Cr is greater than 0.6%, the content is not preferable because weldability may be rapidly reduced. Therefore, the content of Cr may be controlled to be, in detail, 0.3 to 0.6%.

(18) Ti: 0.005 to 0.03%

(19) Titanium (Ti) is an element binding to nitrogen (N) in steel to form a TiN precipitate. In the present disclosure, certain austenite grains may be excessively coarsened during hot-rolling at a high temperature. Thus, the TiN may be appropriately precipitated to suppress growth of the austenite grains. To this end, at least 0.005% of Ti needs to be added. However, when the content of Ti is greater than 0.03%, the effect may be saturated and coarse TiN may be crystallized. Therefore, the content of Ti greater than 0.03% is not preferable. Therefore, in the present disclosure, the content of Ti may be limited to a range of, in detail, 0.005 to 0.03%.

(20) Cu: 0.1 to 0.35%

(21) Copper (Cu) is effective in improving hardenability and corrosion resistance of a base material or a welding zone. However, when the content of Cu is less than 0.1%, it is disadvantageous to secure corrosion resistance. Meanwhile, when the content of Cu is greater than 0.35%, manufacturing costs may be increased to result in economical disadvantage. Therefore, the content of Cu may be limited to a range of, in detail, 0.1 to 0.35%.

(22) Ni: 0.05 to 0.3%

(23) Nickel (Ni) is effective in improving the hardenability and corrosion resistance. When Ni is added together with Cu, Ni may react with Cu to suppress formation of a Cu phase having a low melting point, and thus, may suppress occurrence of cracking during hot working. In addition, Ni is an element effective in improving toughness of a base material. To obtain the above-described effects, Ni needs to be added in an amount of 0.05% or more. However, since Ni is an expensive element, excessive addition of Ni in an amount greater than 3% is economically disadvantageous. The content of Ni may be limited to a range of, in detail, 0.05 to 0.3%.

(24) Mo: 0.01 to 0.15%

(25) Molybdenum (Mo) is significantly effective in increasing strength of a material, and may suppress formation of a pearlite structure to secure excellent impact toughness. To this end, Mo should be added in an amount of 0.01% or more. However, since Mo is an expensive element, the content of Mo may be limited to 0.15% or less to suppress welding low-temperature cracking and to prevent toughness from being lowered by formation of a low-temperature transformation phase in the base material.

(26) N: 0.007% or Less

(27) Since nitrogen (N) causes aging deterioration in a solid-solubilized state, N is fixed as a nitride such as Ti, Al, or the like. When the content of N is greater than 0.007%, the amount of Ti, Al, or the like, may be unavoidably increased. Therefore, the amount of N may be limited to, in detail, 0.007% or less.

(28) Ca: 0.001 to 0.006%

(29) Calcium (Ca) is added to control morphology of sulfide. When the content of Ca is greater than 0.006%, CaS of a CaO cluster may be generated with respect to the amount of S in the steel. Meanwhile, when the amount of Ca is less than 0.001%, MnS may be formed and toughness may be reduced. In addition, when the amount of S is large, the amount of S may be preferably controlled at the same time to prevent generation of a CaS cluster. Therefore, the content of Ca may be limited to a range of, in detail, 0.001 to 0.006%.

(30) Al: 0.01 to 0.05%

(31) Aluminum (Al) is added for deoxidation during steelmaking. When the content of Al is less than 0.01%, such an action is insufficient. Meanwhile, when the content of Al is greater than 0.05%, formation of a composite oxide, including alumina or an alumina oxide may be promoted in a welding zone during electrical resistance welding and toughness of the welding zone may be deteriorated. Therefore, the content of Al may be limited to a range of, in detail, 0.01 to 0.05%.

(32) The elements Mo and P should satisfy Relational Expression 1.
1.6≤(Mo/96)/(P/31)≤6  Relationship 1:

(33) Relational Expression 1 is given to prevent grain boundary segregation of P. When a value of Relational Expression 1 is less than 1.6, a P grain boundary segregation effect resulting from formation of a Fe—Mo—P compound is insufficient. When the value of Relational Expression 1 is greater than 6, impact energy is reduced because a low-temperature transformation phase is formed due to an increase in hardenability.

(34) The elements Ca and S should satisfy Relational Expression 2.
1.6≤(Ca/S)≤3  Relationship 2:

(35) Relational Expression 2 is given to suppress formation of a nonmetallic inclusion acting as a crack formation and propagation path during an impact test and expansion of a steel pipe. When a value of Relation Expression 2 is less than 1.6, MnS is easily formed and elongated during rolling to act as a crack propagation path. When the value of Relational Expression 2 is greater than 3, Ca-based nonmetallic inclusion may be increased. Thus, separation may occur on a fracture surface of an impact specimen during an impact test of a steel material and a steel pipe to reduce impact energy. In certain cases, the value of Relational Expression 2 may be 1.7 or more.

(36) The elements C and Mn should satisfy Relation Expression 3.
3.5≤(3*C/12+Mn/55)*100≤5  Relation Expression 3:
Relation Expression 3 is given to suppress the formation of the light phase 2, bainite and MA (martensite and/or austenite) phases. Due to an increase in C and Mn, a solidification temperature of a slab may be reduced to promote segregation in a center of the slab and a section of delta ferrite may be narrowed to make it difficult to homogenize the slab during continuous casting. In addition, Mn is a representative element segregated in the center portion of the slab and promotes formation of a second phase, deteriorating ductility of a pipe, and due to an increase in C, a coexistence section of a solid phase and a liquid phase is widened during the continuous casting to result in severe segregation. Therefore, when a value of Relational Expression 3 is greater than 5, strength may be increased but inhomogeneity of the slab may be increased due to the above reason. Thus, a second phase, a hard phase, is formed in the slab to deteriorate low-temperature toughness of a steel material and a pipe. For this reason, the value of Relational Expression 3 may be, in detail, 5 or less to secure impact toughness of the steel material. However, when the value of Relational Expression 3 is less than 3.5, the strength may be decreased.

(37) A high-strength high-toughness hot-rolled steel sheet according to an aspect of the present disclosure includes, by area fraction, 85% or more of polygonal ferrite and 15% or less of pearlite and includes a microstructure in which a crystal grain size of the polygonal ferrite is 10 μm or less.

(38) When the fraction of the pearlite is greater than 15%, an initiation point of occurrence of cracking and separation is formed during an impact test to reduce impact energy. Therefore, the fraction of the pearlite may be limited to, in detail, 15% or less.

(39) When a grain size of the polygonal ferrite is greater than 10 μm, resistance to crack propagation may be decreased to deteriorate impact characteristics and to reduce the strength. Therefore, the grain size of the polygonal ferrite may be limited to, in detail, 10 μm or less.

(40) When the fraction of the polygonal ferrite is less than 85%, a fraction of a soft phase is decreased, so that strength may be improved but impact characteristics may be insufficient. Therefore, the fraction of the polygonal ferrite may be limited to, in detail, 85% or more.

(41) In the hot-rolled steel sheet, the number of precipitates of 20 nm or less per mm.sup.2 may be 7×10.sup.8 or more.

(42) In a high-strength high-toughness hot-rolled steel sheet according to an aspect of the present disclosure, a deviation in yield strength in a width direction is 35 MPa or less.

(43) In the hot-rolled steel sheet, an impact toughness value measured through a Charpy impact test at temperature of −60° C. may be 95 J or more.

(44) In the hot-rolled steel sheet, separation on the fracture surface of the impact specimen may be 0.01/mm or less.

(45) The hot-rolled steel sheet may have a yield strength at room temperature of 520 MPa or more and a tensile strength at room temperature of 640 MPa or more.

(46) Hereinafter, a method for manufacturing a high-strength high-toughness hot-rolled steel sheet according to another aspect of the present disclosure will be described.

(47) A method for manufacturing a high-strength high-toughness hot-rolled steel sheet according to another aspect of the present disclosure includes: preparing a steel slab comprising, by weight percentage (wt %), 0.07 to 0.13% of carbon (C), 0.20 to 0.50% of silicon (Si), 0.5 to 0.9% of manganese (Mn), 0.03% or less of phosphorus (P), 0.02% or less of sulfur (S), 0.005 to 0.03% of niobium (Nb), 0.3 to 0.6% of chromium (Cr), 0.005 to 0.03% of titanium (Ti), 0.1 to 0.35% of copper (Cu), 0.05 to 0.3% of nickel (Ni), 0.01 to 0.15% of molybdenum (Mo), 0.007% or less of nitrogen (N), 0.001 to 0.006% of calcium (Ca), 0.01 to 0.05% of aluminum (Al), and a balance of iron (Fe) and other unavoidable impurities, the alloy elements satisfying Relational Expressions 1 to 3; heating the steel slab to a temperature within a range of 1100 to 1300° C. and maintaining the heated steel slab at temperature of 1160° C. or higher for 30 minutes or more, and then extracting; primarily hot rolling the heated and extracted steel slab under conditions of a finish rolling temperature of 900 to 1000° C. and a reduction ratio of 10% or more per pass in a recrystallization region and secondarily hot rolling the primarily hot-rolled steel slab under conditions of a finish rolling temperature of 750 to 870° C. and a cumulative reduction ratio of 85% or more in a non-recrystallization region to obtain a hot-rolled steel sheet; and water cooling the hot-rolled steel sheet to a cooling end temperature within a range of 500 to 580° C. at a cooling rate of 10 to 50° C. and then coiling,
1.6≤(Mo/96)/(P/31)≤6,  Relational Expression 1:
1.6≤(Ca/S)≤3, and  Relational Expression 2:
3.5≤(3*C/12+Mn/55)*100≤5  Relational Expression 3:

(48) wherein heat energy is applied to both edge portions of the steel sheet to reduce a difference in cooling rates between a center portion and an edge portion of a steel material.

(49) Heating Slab and Extracting

(50) A steel slab having the above-described composition is heated to a temperature within a range of 1100 to 1300° C., maintained at temperature of 1160° C. or more for 30 minutes or more, and then extracted.

(51) Since the heating process of the steel slab is a process in which steel is heated to smoothly perform a subsequent rolling process and to sufficiently obtain desired mechanical properties of a steel sheet, the heating process should be performed within an appropriate temperature range according to purpose.

(52) In the operation of heating the steel slab, the steel slab should be uniformly heated to sufficiently solid-solubilize precipitated elements in the steel sheet, and coarse grains caused by a significantly high heating temperature should be prevented. The reheating temperature of the steel slab may be, in detail, 1100 to 1300° C., which is set for a casting structure and segregation formed in a slab manufacturing process and solid solution and homogenization of second phases. When the reheating temperature of the steel slab is less than 1100° C., homogenization may be insufficient or a heating furnace temperature is significantly low, causing deformation resistance to be increased during hot rolling. When the reheating temperature of the steel slab is higher than 1300° C., surface quality may be deteriorated.

(53) Therefore, the heating temperature of the steel slab may have a range of, in detail, 1100 to 1300° C. In addition, when the steel slab is maintained at temperature of 1160° C. or higher for less than 30 minutes, the degree of cracking in thickness and length directions of the steel slab is low, which may result in poor rollability and a deviation of mechanical properties of a finally obtained steel sheet.

(54) Obtaining Hot-Rolled Steel Sheet

(55) The heated and extracted steel slab is primarily hot rolled under conditions of a finish rolling temperature of 900 to 1000° C. and a reduction ratio of 10% or more per pass in a recrystallization region, and is then secondarily hot rolled under conditions of a finish rolling temperature of 750 to 870° C. and a cumulative reduction ratio of 85% or more in a non-recrystallization region to obtain a hot-rolled steel sheet.

(56) For example, it is important to finish primary rolling of the heated and extract steel slab at temperature within a range of 900 to 1000° C., to roll the steel slab at a reduction ratio of 10% or more per pass in the recrystallization region, and to secondarily roll the primarily rolled steel slab at a cumulative reduction ratio of 85% or more in a non-recrystallization region and finish the secondary rolling at temperature within a range of at 750 to 870° C. Hot rolling should be performed in the above-mentioned temperature range to effectively refine grains. In particular, when the finish rolling temperature is significantly high, a final structure may be coarsened to prevent desired strength from being obtained. Meanwhile, when the finish rolling temperature is significantly low, a load on a finishing rolling mill facility may be problematic. In addition, when the reduction per pass is less than 10% or when a rolling rate in the non-recrystallization region is less than 85%, impact toughness may be decreased.

(57) In addition, it is important that a deviation in thickness at an edge portion of the steel sheet and a point of 100 mm from the edge portion is adjusted to be 90 mm or less.

(58) When a thickness of the edge portion of the steel sheet is significantly reduced, a deviation of mechanical property may occur due to a structure deviation caused by supercooling during water cooling.

(59) Cooling Hot-Rolled Steel Sheet and Coiling

(60) The hot-rolled steel sheet is water cooled to a cooling end temperature of 500 to 580° C. at a cooling rate of 10 to 50° C./sec and is then coiled. During the water cooling, heat energy is applied to both edge portions of the steel sheet to reduce a difference in cooling rates between a center portion and the edge portion of the steel sheet.

(61) When the cooling end temperature is higher than 580° C., surface quality is deteriorated and coarse carbide is formed to deteriorate toughness and strength. When the cooling end temperature is lower than 500° C., a large amount of cooling water is required during coiling and a load is significantly increased during the coiling. Therefore, the cooling end temperature may be limited to a range of, in detail, 500 to 580° C.

(62) The applying heat energy to both edge portions of the steel sheet may be performed such that a deviation in temperature in a width direction of the steel sheet during water cooling is 150° C. or less.

(63) For example, heat energy may be applied to both edge portions of the steel sheet such that a deviation in internal temperature at the edge portion of the steel sheet and a point of 100 mm from the edge portion is 150° C. by heating the edge portion of the steel sheet using an edge heater during water cooling.

(64) The applying heat energy to both edge portions of the steel sheet may be performed using an edge heater and an edge mask.

(65) When heat energy is not applied to both edge portions of the steel sheet using an edge heater, or the like, during water cooling, a temperature of both edge portions is decreased to be lower than a temperature of a center portion. Thus, a deviation in strength in a width direction of the steel sheet may be increased to cause a deviation in strength a circumferential direction of a steel pipe after production of the steel pipe.

(66) In a high-strength high-toughness hot-rolled steel sheet manufactured by the method according to another aspect of the present disclosure, a microstructure includes, by area fraction, 85% or more of polygonal ferrite and 15% or less of pearlite and a grain size of the polygonal ferrite is 10 μm or less, and a deviation in yield strength in a width direction is 35 MPa or less.

(67) In the hot-rolled steel sheet, the number of precipitates of 20 nm or less per mm.sup.2 may be 7×10.sup.8 or more.

(68) In the hot-rolled steel sheet, an impact toughness value measured through a Charpy impact test at temperature of −60° C. may be 95 J or more, separation on the fracture surface of the impact specimen may be 0.01/mm or less, and a yield strength at room temperature may be 520 MPa or more and a tensile strength at room temperature may be 640 MPa or more.

BEST MODE FOR INVENTION

(69) Hereinafter, the present disclosure will be described more specifically through examples.

(70) Steel having chemical components shown in Tables 1 and 2 was prepared a slab by continuous casting, and the slab was then rolled under hot-rolling conditions shown in Table 3 to manufacture a hot-rolled steel sheet having a thickness of 4 mm.

(71) In the hot-rolled steel sheet, the number of precipitates of 20 nm or less (number/mm.sup.2), fractions of ferrite and pearlite, a fraction of MA (%), a separation length (mm), and a ferrite grain size (μm) were measured, and results thereof are listed in Table 4.

(72) In addition, in the hot-rolled steel sheet, yield strength YS, tensile strength TS, a device of mechanical property of the yield strength, and impact energy full size conversion (@−60° C.) were measured, and results thereof are listed in Table 5. In Table 5, strength was measured according to a commonly used ASTM A370, and the impact energy was measured by performing a Charpy impact test at temperature of −60° C.

(73) TABLE-US-00001 TABLE 1 Steel Remark Type C Si Mn P S Nb Cr Ti Cu Ni Mo N Ca Al Inventive A1 0.12 0.35 0.55 0.008  0.001  0.02  0.55 0.015 0.27  0.15  0.08 0.005 0.0021 0.032 Steel A2 0.08 0.33 0.90 0.0089 0.0013 0.03  0.54 0.02  0.272 0.14  0.08 0.004 0.0025 0.038 A3 0.10 0.35 0.89 0.0067 0.0017 0.02  0.52 0.018 0.279 0.142 0.08 0.003 0.0028 0.034 A4 0.11 0.34 0.85 0.0124 0.0013 0.022 0.52 0.019 0.262 0.148 0.08 0.004 0.0025 0.034 A5 0.12 0.35 0.70 0.0107 0.0015 0.021 0.54 0.011 0.274 0.141 0.08 0.005 0.0029 0.035 Comparative B1 0.14 0.32 1.1  0.015  0.0019 0.02  0.55 0.012 0.3   0.23  0.01 0.004 0.015  0.035 Steel B2 0.15 0.32 1.2  0.012  0.002  0.02  0.59 0.013 0.28  0.17  0.03 0.006 0.002  0.035 B3 0.09 0.32 0.28 0.011  0.0021 0.01  0.52 0.014 0.29  0.24  0.02 0.007 0.0014 0.035 B4 0.11 0.35 0.52 0.011  0.0015 0.011 0.6  0.014 0.3  0.17  0.04 0.004 0.0018 0.035 B5 0.12 0.35 0.9  0.011  0.002  0.02  0.6  0.014 0.3  0.17  0.03 0.004 0.002  0.035

(74) TABLE-US-00002 TABLE 2 Remark Steel Type (Mo/93)/(P/31) Ca/S (3 * C/12 + Mn/55) * 100 Inventive A1 3.3 2.1 4.5 Steel A2 3.0 1.9 3.6 A3 4.0 1.6 4.1 A4 2.0 1.9 4.3 A5 2.5 1.9 4.2 Com- B1 0.2 0.8 5.5 parative B2 0.8 1.0 5.9 Steel B3 0.6 0.7 3.9 B4 1.2 1.2 4.2 B5 0.9 1.0 4.6

(75) TABLE-US-00003 TABLE 3 Furnace Average Maintain- Reduction Reduction Re- ing Ratio of Ratio of Primary Secondary heating Time at Recrystal- Recrystal- Rolling Rolling Cooling Coiling Use of Temper- 1160° C. lization lization Temper- Temper- Rate Temper- Use of 150 mm Steel ature or higher Region Region ature ature (° C./ ature Edge Edge Remark Type (° C.) (min) (%) (%) (° C.) (° C.) sec) (° C.) Heater Mask Inventive A1 1195 65 15 90 930 520 15 520 Used Used Steel A2 1187 66 15 85 955 835 20 530 Used Used A3 1187 61 20 92 945 555 22 545 Used Used A4 1195 60 25 92 935 523 31 529 Used Used A5 1193 66 15 90 923 831 26 546 Used Used Comparative B1 1277 78 15 92 944 828 18 550 Used Used Steel B2 1105 62 15 91 968 519 22 564 Used Used B3 1310 63 13 87 932 822 24 576 Not Used Not Used B4 1186 68 20 88 923 861 25 590 Not Used Not Used B5 1192 71 15 92 943 562 15 561 Not Used Not Used A1 1080 58 15 91 948 833 20 620 Not Used Not Used A2 1124 53 15 88 937 867 18 630 Not Used Not Used

(76) TABLE-US-00004 TABLE 4 Number Temper- of Thickness ature Precipitates Deviation Deviation of in in 20 nm Separa- Ferrite Width Width or less Ferrite Pearlite MA tion Grain Steel Direction Direction (number/ Fraction Fraction Fraction Length Size Remark Type (mm) (° C.) mm.sup.2) (%) (%) (%) (mm) (μm) Inventive A1  32  80 7.2 × 10.sup.8 89 11   0 0.005  7 Steel A2  45  95 7.5 × 10.sup.8 88 12   0 0     8 A3  89 120 8.7 × 10.sup.8 90 10   0 0     9 A4  30 111 7.9 × 10.sup.8 92 8  0 0.006  8 A5  65 123 8.1 × 10.sup.8 88 12   0 0     9 Comparative B1 101 190 5.3 × 10.sup.8 78 21   1 0.15  11 Steel B2 102 220 6.8 × 10.sup.8 77 21.8 1.2 0.25  12 B3 112 245 6.3 × 10.sup.8 88 12   0 0.1  14 B4 123 310 5.8 × 10.sup.8 87 13   0 0.05  16 B5 123 285 6.1 × 10.sup.8 82 18   0 0.13  12 A1 142 387 6.2 × 10.sup.8 76 24   0 0.08  18 A2 121 293 5.8 × 10.sup.8 75 25   0 0.09  19

(77) TABLE-US-00005 TABLE 5 Deviation of Impact Energy Mechanical Full Size Steel YS TS Property of YS Conversion Remark Type (MPa) (MPa) (MPa) (8-60° C.) Inventive A1 548 676 25 100 Steel A2 552 677 22 108 A3 552 681 16 116 A4 556 682 27 120 A5 531 667 30 124 Comparative B1 589 691 26  52 Steel B2 601 712 22  40 B3 562 691 64  84 B4 515 628 62  88 B5 540 647 26  92 A1 490 613 78  48 A2 485 609 72  44

(78) As shown in Tables 1 to 5, in the case of inventive steels prepared according to components and component ranges, component relational expression, and manufacturing conditions conforming to the present disclosure, polygonal ferrite and pearlite having appropriate fractions were formed to have yield strength of 520 MPa or more and tensile strength 640 MPa or more. In addition, as a result of preventing supercooling of both edge portions using an edge heater, a deviation in yield strength in a width direction could be suppressed to 35 MPa or less and it can be seen that impact energy of 95 J or more was secured at temperature of −60° C.