JP2010111924A - Low yield ratio steel plate for building having excellent high heat input weld zone toughness and method for producing the same - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide a low yield ratio steel plate for building having high heat input weld heat affected zone toughness which has low surface hardness and excellent earthquake resistance, and to provide a method for producing the same. <P>SOLUTION: The steel plate has a composition comprising, by mass, 0.03 to 0.07% C, 0.05 to 0.5% Si, 0.6 to 2.0% Mn, ≤0.020% P, 0.0005 to 0.003% S, 0.005 to 0.03% Ti, 0.0003 to 0.0020% B, ≤0.1% Al, 0.0025 to 0.0070% N, 0.001 to 0.003% O, 0.0005 to 0.005% Ca, ≤0.01% Mo and ≤0.005% Nb, further comprising one or more selected from Cu, Ni, Cr, V, Mg and rare earth metals, satisfying 0.40 to 0.45% Ceq and 0.2 to 0.8 ACR, and the balance Fe with inevitable impurities, has a microstructure in which ferrite fraction is 10 to 40%, and has a surface hardness of ≤350 HV10: Ceq=C+Mn/6+(Cu+Ni)/15+(Cr+Mo+V)/5 and ACR=(Ca-(0.18+130×Ca)×O)/(1.25×S). <P>COPYRIGHT: (C)2010,JPO&INPIT

Description

  The present invention relates to a low yield ratio steel sheet for construction excellent in toughness of heat-affected zone by large heat input welding by submerged arc welding or electroslag welding with heat input of 400 kJ / cm or more, which is applied when manufacturing an architectural box column. In particular, the present invention relates to a steel sheet having a low surface hardness and excellent earthquake resistance.

  In recent years, with the increase in size of building structures, the use of steel materials has increased in thickness and strength, and in order to ensure the earthquake resistance of building structures, it has a low yield ratio of 80% or less. It is also required to be.

  A building structure is a welded structure that is assembled into a predetermined shape by welding, but if a large load is applied during an earthquake, brittle fracture may occur from the weld before sufficient plastic deformation occurs. In addition, the welded portion is required to have good toughness.

  In order to manufacture a welded structure with high efficiency, large heat input welding with a heat input of 400 kJ / cm or more such as submerged arc welding of corner joints and electroslag arc welding of diaphragm joints is performed in the production of box columns. .

  In general, such a high heat input welded part has a slow cooling rate after welding, so that the residence time in the high temperature region of the region heated up to the vicinity of the melting point becomes long, the structure becomes coarse, or called MA. Brittleness is caused by the formation of a hard brittle phase.

  The weld heat-affected zone is more likely to be brittle as the strength of the steel increases in the amount of alloying elements, and is often a problem in the case of TS590 MPa grade steel for building structural steels. Therefore, TS590 MPa provides excellent weld heat-affected zone toughness. Various grades of architectural steel have been proposed.

  Patent Documents 1 and 2 regulate the ACR value required by the formula consisting of Ca, O, and S, regarding the manufacturing method of high strength thick steel sheet for building with excellent heat input toughness of super high heat input welding exceeding 400 kJ / cm. It has been reported that by utilizing fine particles generated during welding as ferrite transformation nuclei, the structure of the heat affected zone is refined and the toughness is improved.

Further, quenching in the weld heat affected zone relates Patent Document 3 the method of manufacturing a low yield ratio 600N / mm ² class steel sheet construction which is excellent in high heat input welding heat affected zone toughness, the steel composition as the low C - B-free addition system It is described that the structure of the weld heat-affected zone is refined by using Ti oxide while reducing the properties. The strength of the base material is 600 N / mm ² by securing precipitation with Cu.

  Patent Document 4 relates to a high-tensile steel plate excellent in toughness of a high heat input welding heat-affected zone, and has a component composition appropriately containing Mn, Ni, Cr, etc. that are extremely low C and hardenability improving elements. Therefore, the toughness improvement of the weld heat affected zone exceeding 500 kJ / cm is achieved by suppressing and controlling the shape of the MA and making the block size of the transformed structure finer.

  Patent Document 5 relates to a low-yield-ratio high-tensile steel sheet with excellent high heat input welding toughness, and lowers the carbon equivalent of the base material composition for welding with heat input of 250 kJ / cm or more, and uses Ti carbonitride. Thus, it is described that the structure of the heat-affected zone is refined to improve toughness. The ferrite fraction is adjusted for lower yield ratio, and Nb carbonitride is used for higher strength.

  Patent Document 6 relates to a steel plate for low-yield-ratio building structures excellent in super high heat input welding HAZ toughness and a method for producing the same, and in the component composition of a steel plate having a thickness of 30 mm or more to be welded at a heat input exceeding 400 kJ / cm, When the fine particles containing composite sulfide (sulfide) in which MnS is deposited on the surface of CaS produced during welding is used as a ferrite transformation nucleus by regulating the ACR value obtained by the formula consisting of S And specifying the distribution state.

  As described above, in low yield ratio steel with excellent toughness of existing high heat input welds, the improvement in toughness of high heat input welds is achieved by adjusting the base material components to fine particles (sulfides). (Sulfide) or oxide (oxycide) is precipitated and dispersed to refine the structure (Patent Documents 1, 2, 3, 5, 6), and the production of MA is suppressed (Patent Document 4).

Low yield ratio is achieved by adjusting the ferrite structure fraction in steel by performing two-phase region heat treatment (Patent Documents 1, 2, 6) or quenching and tempering a low Ceq component system (Patent Document 5). .
JP 2005-68519 A JP 2005-68478 A JP-A-6-128635 JP 2007-126725 A JP 2001-172736 A JP 2003-183767 A

  However, the two-phase region heat treatment has a complicated manufacturing process and decreases productivity. On the other hand, in the case of quenching and tempering without performing a two-phase heat treatment, as in the steel described in Patent Document 5, a high C component system in which C is 0.12% or more to ensure strength: 0.12% or more Therefore, even if a low yield ratio is achieved, the surface hardness is extremely high, the ductility deterioration near the surface layer is significant, cracks occur near the surface layer when stress is applied due to earthquakes, etc., and fracture occurs due to the notch effect There is a case.

  In addition, in Patent Documents 1, 2, and 6 in which two-phase region heat treatment is performed, in order to obtain high strength in the examples, the amount of C added is as large as over 0.07%, and the surface ductility is reduced as in Patent Document 5. There is a concern to do.

  Accordingly, the present invention provides a low yield ratio steel sheet having improved seismic resistance by reducing the hardness near the surface layer and improving the ductility near the surface layer without subjecting the two-phase region heat treatment, which is disadvantageous in terms of the production period, and a method for producing the same. The purpose is to provide.

  As a result of intensive studies to achieve the above-mentioned problems, the present inventors set the ACR value represented by the following formula consisting of Ca, O, and S to 0.2 to 0.8, and appropriate amounts of Ti and N. By adding accelerated cooling to steel having a component composition with C content of 0.07% or less, Nb of 0.005% or less, and Mo of 0.01% or less, an excellent high heat input heat affected zone It was found that a steel sheet having a surface hardness near the surface layer of 350 HV10 or less and having a yield ratio of 80% or less and exceeding TS590 MPa can be produced without performing a two-phase region heat treatment.

  ACR = (Ca− (0.18 + 130 × Ca) × O) / (1.25 × S), where Ca, O and S are steel contents.

The present invention has been made by further study based on the obtained knowledge. That is, the gist of the present invention is as follows.
1. In mass%, C: 0.03-0.07%, Si: 0.05-0.5%, Mn: 0.6-2.0%, P: 0.020% or less, S: 0.0005 -0.003%, Ti: 0.005-0.03%, B: 0.0003-0.0020%, Al: 0.1% or less, N: 0.0025-0.0070, O: 0.0. 001 to 0.003%, Ca: 0.0005 to 0.005%, Mo: 0.01% or less, Nb: 0.005% or less, Cu: 0.5% or less, Ni: 1.0% Hereinafter, one or two or more of Cr: 0.5% or less and V: 0.08% or less are included, and Ceq according to the following formula (1) is 0.40 to 0.45%, according to the following formula (2) ACR satisfies 0.2 to 0.8, has a composition comprising the balance Fe and inevitable impurities and a microstructure with a ferrite fraction of 2 to 30% 80% yield ratio, wherein a surface hardness of 350HV10 less or less, a tensile strength 590MPa or more low yield ratio steel sheet excellent architectural structures in high heat input weld toughness.

Ceq = C + Mn / 6 + (Cu + Ni) / 15 + (Cr + Mo + V) / 5 − (1)
ACR = (Ca− (0.18 + 130 × Ca) × O) / (1.25 × S) −−− (2)
However, each element in the formulas (1) and (2) has a content (% by mass).
2. Further, the component composition contains one or two of Mg: 0.005% or less and REM: 0.02% or less, wherein the yield ratio is 80% or less and the tensile strength is 590 MPa or more. Low yield ratio steel sheet for building structures with excellent heat input weld toughness.
After the steel material having the composition described in 3.1 or 2 is heated to 1000 to 1200 ° C., rolling is performed so that the rolling end temperature is equal to or higher than the Ar ₃ transformation point, and then accelerated cooling is performed at an average cooling rate of 3 to 12 ° C. / s, a construction that is excellent in toughness of high heat input welds, characterized in that when tempering is not performed after cooling stop, the cooling stop temperature is 400 to 200 ° C., and when tempering is performed, the cooling stop temperature is 400 to 50 ° C. A method for producing a structural low yield ratio steel sheet.
After heating the steel material having the composition described in 4.1 or 2 to 1000 to 1200 ° C., rolling is performed so that the rolling end temperature is equal to or higher than the Ar ₃ transformation point, and then cooling is stopped at an average cooling rate of 15 ° C./s or higher. Temperature: 650 to 500 ° C. Accelerated cooling, air cooling or tempering is performed, and a method of manufacturing a low yield ratio steel sheet for building structures having a thickness of 19 to 40 mm excellent in toughness of large heat input welds .

  According to the present invention, a steel plate having a high heat input weld toughness exceeding TS 590 MPa and having a surface hardness of 350 HV10 or less and excellent surface ductility without subjecting the two-phase region heat treatment, which is disadvantageous in terms of manufacturing construction period, It can be produced economically and is extremely useful industrially.

Hereinafter, the present invention will be described in detail.
[Ingredient composition] In the description, “%” means “mass%”.
C: 0.03-0.07%
C is an important element affecting the strength, surface hardness and toughness, and is 0.03 to 0.07%.

  1 to 4 are views showing the influence of the C amount on the strength, surface hardness and toughness, FIG. 1 is the influence of the C amount on the high heat input welding heat affected zone toughness, and FIG. 2 is the amount of the C amount on the surface hardness. FIG. 3 shows the effect of C content on ductility (surface tensile test elongation), and FIG. 4 shows the effect of C content on strength (YS, TS).

  When the C content is 0.04 to 0.12%, the high heat input weld heat-affected zone toughness has a high energy value of 70 J or more (FIG. 1), and the TS of 1 / 4t and 1 / 2t parts is 590 MPa. As described above, YS is 450 MPa or more and a yield ratio (not shown) of 80% or less is obtained (FIG. 4).

  The difference in strength (TS) between the 1 / 4t part and the 1 / 2t part is less than 60 MPa and the material difference in the plate thickness direction is reduced when the C amount is 0.07% or less (FIG. 4).

  On the other hand, the hardness near the surface layer exceeds 350HV10 when the C content exceeds 0.07% (FIG. 2), and the ductility near the surface layer also decreases when the C content exceeds 0.07% (FIG. 3).

  Therefore, in order to improve the ductility near the steel sheet surface, it is effective to reduce the hardness near the surface, and the C content in the steel composition must be 0.07% or less.

  Therefore, in the present invention, the amount of C is specified as 0.03 to 0.07%. Desirably, it is 0.04 to 0.07%.

  The results shown in FIGS. 1 to 4 are Mass%, including 0.04 to 0.12% C, and Ceq (= C + Mn / 6 + (Cu + Ni) / 15 + (Cr + Mo + V) in Si, Mn, Cu, Ni, and Cr. ) / 5) is substantially constant at 0.42 to 0.43, and ACR (= (Ca− (0.18 + 130 × Ca) × O) / (1.25 × S)) is 0.4 to 0. After heating the steel material having the composition of .5 to 1150 ° C. and finishing rolling at 850 ° C. to form a 60 mm steel plate, the average cooling rate from 810 ° C. to 370 ° C. is 10 ° C./s accelerated cooling. It is an experimental result which uses the steel plate which gave it as test steel. The average cooling rate was the cooling rate at a thickness of 1/4 t.

  About the obtained steel plate, the hardness measurement of the 0.5 mm position under the surface layer, the tensile test, and the investigation of the high heat input heat affected zone toughness were carried out. The hardness under the surface layer was Vickers hardness, 20 points were measured at 0.5 mm below the surface layer, and the maximum value was taken as the representative value.

  The tensile test was performed according to JISZ2241 using JIS No. 4 test specimens (collection position: 1 / 4t position, 1 / 2t position) specified in JISZ2201, and the yield stress (YS) and tensile strength ( The yield ratio (YR) was determined from TS).

  For evaluation of the ductility of the surface layer portion, a small round bar tensile test piece having a rating distance of 6 mm × 24 mm was taken from the position directly below the surface layer (0.5 to 6.5 mm position), and the elongation value after the tensile test was measured. .

  Large heat input weld heat-affected zone toughness is obtained by collecting Charpy impact test pieces with a notch position of 1 mm from the BOND part to the base metal side from an electroslag weld joint with a heat input of 1000 kJ / cm. The evaluation was based on the average value of three tests.

Si: 0.05-0.5%
Si is an effective element as a deoxidizing element, and 0.05% or more is necessary to exert its effect. Moreover, when adding over 0.5%, MA of a high heat input welding heat affected zone will increase, and heat affected zone toughness will deteriorate. Therefore, it regulates to 0.05 to 0.5%. Desirably, it is 0.05 to 0.4%.

Mn: 0.6 to 2.0%
Mn is an element effective for securing strength by solid solution strengthening, and 0.6% or more is necessary to exert its effect. Moreover, if it exceeds 2.0%, weldability deteriorates. Therefore, it regulates to 0.6 to 2.0%. Desirably, it is 0.6 to 1.6%.

P: 0.020% or less P is mixed as an impurity element. When the mixed amount increases, the base material toughness deteriorates. Therefore, it regulates to 0.020% or less. Desirably, it is 0.015% or less.

S: 0.0005 to 0.003%
S is an element necessary for controlling the ACR value, and forms CaS which is a nucleus of MnS formation, and the produced MnS has an effective effect on the formation of intragranular ferrite and refinement of the microstructure of the high heat input weld. . In order to obtain the effect, 0.0005% or more is necessary. Addition exceeding 0.003% degrades the material in the thickness direction due to MnS generation. Therefore, it limits to 0.0005 to 0.003%. Desirably, it is 0.0010 to 0.003%.

Ti: 0.005 to 0.03%
Ti is effective in refining the structure of the weld heat affected zone by generating TiN. In order to exert this effect, 0.005% or more is necessary. If added over 0.03%, the base metal toughness and the heat-affected zone toughness are deteriorated by TiC precipitation. Therefore, it is set as 0.005 to 0.03%. Desirably, it is 0.008 to 0.015%.

B: 0.0003 to 0.0020%
B is an element effective in improving hardenability and ensuring the strength of the base material. In order to exhibit the effect, 0.0003% or more is necessary. Addition exceeding 0.0020% deteriorates weldability. Therefore, it is set as 0.0003 to 0.0020%. Preferably, it is 0.0005 to 0.0015%.

Al: 0.1% or less When Al exceeds 0.1%, Al ₂ O ₃ is generated and the cleanliness of the steel is deteriorated. Therefore, it is made 0.1% or less. Desirably, it is 0.020 to 0.060%.

N: 0.0025 to 0.0070
N is effective in refining the structure of the heat affected zone by generating TiN. In order to exhibit this effect, 0.0025% or more is necessary. Moreover, when adding exceeding 0.0070%, the solid solution N of a welding heat affected zone will increase, and heat affected zone toughness deterioration will be exerted. Therefore, it is set as 0.0025 to 0.0070%. Desirably, it is 0.0030 to 0.0060%.

O: 0.001 to 0.003%
O is an element mixed as an impurity element, and it is desirable that O be low. However, excessively reducing oxygen leads to an increase in manufacturing cost in the melting process. Moreover, when it exceeds 0.003% and an oxide type inclusion increases, the cleanliness degree of steel will be degraded. Therefore, the content is set to 0.001 to 0.003%. Desirably, it is 0.001 to 0.0025%.

Ca: 0.0005 to 0.005%
Ca is an element necessary for controlling the ACR value, and forms CaS as a nucleus of MnS formation. The generated MnS has an effective effect on intragranular ferrite formation and microstructure refinement in a high heat input weld. . In order to obtain the effect, 0.0005% or more is necessary. Addition in excess of 0.005% increases Ca-based oxides and degrades the steel cleanliness. Therefore, it is set as 0.0005 to 0.005%. Preferably, it is 0.0005 to 0.005%.

Mo: 0.01% or less Mo is added in a small amount to increase the hardenability of the weld heat-affected zone. As a result, the formation of ferrite is suppressed, the upper bainite is formed, and the toughness is deteriorated. If it exceeds 0.01%, such an action is produced, and the weld heat affected zone toughness is deteriorated. Therefore, when adding, it is 0.01% or less. It is desirable to add substantially no additives.

Nb: 0.005% or less Nb increases the hardenability of the weld heat-affected zone by adding a small amount, and as a result, suppresses the formation of ferrite, causes upper bainite, and deteriorates toughness. When it exceeds 0.005%, such an effect is produced, and the weld heat-affected zone toughness is deteriorated. Therefore, it is made 0.005% or less. It is desirable to add substantially no additives.

Further, one or more of Cu, Ni, Cr and V Cu: 0.5% or less Cu is an element effective as a solid solution strengthening, but addition exceeding 0.5% deteriorates hot ductility. Or manufacturing problems such as an increase in surface defects. Therefore, when adding, it controls to 0.5% or less.

Ni: 1.0% or less Ni is an element effective as a solid solution strengthening, but addition exceeding 1.0% increases the alloy cost and the manufacturing cost. Therefore, when adding, it is 1.0% or less.

Cr: 0.5% or less Cr is an element effective for solid solution strengthening, but addition exceeding 0.5% lowers weldability. Therefore, it is 0.5% or less.

V: 0.08% or less V is an effective element for solid solution strengthening or precipitation strengthening, but addition exceeding 0.08% increases the alloy cost and the manufacturing cost. Therefore, it is 0.08% or less.

Ceq: 0.40 to 0.45%
Ceq (= C + Mn / 6 + (Cu + Ni) / 15 + (Cr + Mo + V) / 5, where each element content (% by mass) is regulated from the viewpoints of strength and toughness of heat-affected zone heat-affected zone. If it is less than 0.40%, the strength cannot be ensured, and if it exceeds 0.45%, the toughness of the heat-affected zone affected by high heat input welding deteriorates. Therefore, it regulates to 0.40 to 0.45%.

ACR: 0.2-0.8
ACR (= (Ca− (0.18 + 130 × Ca) × O) / (1.25 × S), where each element content (% by mass)) is from the viewpoint of high heat input welding heat affected zone toughness regulate. If it is less than 0.2%, the amount of Ca-based sulfide required for ferrite formation decreases, and the effect of improving the toughness of the high heat input heat affected zone cannot be obtained. On the other hand, when it exceeds 0.8%, even if a Ca-based granulated material is generated, MnS having the core as a core is not generated, and the heat-affected zone refinement effect due to ferrite generation cannot be obtained. Therefore, it regulates to 0.2 to 0.8%.

  The above is the basic component composition, but when further improving the toughness of the weld heat affected zone, one or two of Mg and REM are added.

  Mg forms oxysulfide and improves the toughness of the weld heat affected zone with an element effective for ferrite formation and microstructure refinement in the weld heat affected zone. However, when added in excess, the quality of the steel deteriorates. Therefore, when adding, it is 0.005% or less.

REM generates oxysulfide and improves the toughness of the weld heat-affected zone with an element effective for ferrite formation and microstructure refinement in the weld heat-affected zone. Therefore, when adding, it is 0.02%.
[Microstructure]
The low yield ratio steel sheet for construction according to the present invention has a microstructure with a ferrite fraction of 2 to 30%. The ferrite fraction is regulated from the viewpoint of lowering the yield ratio. If the ferrite fraction is less than 2%, a yield ratio of 80% or less cannot be obtained, and if it exceeds 30%, it is difficult to ensure the strength. 2 to 30%.
[surface hardness]
The low yield ratio steel sheet for building according to the present invention has a surface hardness of 350 HV10 or less. The surface hardness is regulated from the viewpoint of improving the ductility of the surface. As shown in FIGS. 2 and 3 described above, when the C content exceeds 0.08% and the surface hardness exceeds 350 HV10, the ductility near the surface layer is 25% or less. And the earthquake resistance deteriorates. Therefore, it shall be 350HV10 or less.

Hereinafter, the manufacturing conditions of the low yield ratio steel sheet for construction according to the present invention will be described.
Heating temperature: 1000-1200 ° C
If the heating temperature is less than 1000 ° C., the hot deformation resistance is high and rolling is difficult, whereas if it exceeds 1200 ° C., the initial structure during heating becomes coarse, the base material structure becomes coarse, and the toughness deteriorates. Therefore, it shall be 1000-1200 degreeC.
Rolling end temperature: Ar ₃ transformation point or higher When the rolling end temperature is lower than the Ar ₃ transformation point, the ferrite generated during rolling is refined and the yield ratio is increased. Therefore, the Ar ₃ transformation point or higher is set.

Accelerated cooling: Cooling rate: 3-12 ° C / s, Cooling stop temperature: 400-50 ° C
If the cooling rate of accelerated cooling is less than 3 ° C./s, the ferrite fraction exceeds 30%, and it is difficult to ensure the strength. On the other hand, if it exceeds 12 ° C./s, the ferrite fraction becomes less than 2%, and it becomes difficult to reduce the yield ratio. Therefore, it is set as 3-12 degrees C / s.

  The cooling stop temperature of accelerated cooling is 400 to 200 ° C. when tempering is not performed, and 400 to 50 ° C. when it is performed. Regardless of the presence or absence of tempering, when the cooling stop temperature exceeds 400 ° C., it is difficult to ensure the strength, and when tempering is not performed, it is difficult to ensure the shape of the steel sheet due to cooling strain or the like if it is less than 200 ° C.

  When tempering is performed, the steel plate shape can be corrected during tempering heating, so that the stop temperature can be increased to a lower temperature and the cooling stop temperature is increased to 50 ° C.

  When tempering is performed, the tempering temperature is 450 ° C. or lower. When the tempering temperature exceeds 450 ° C., the strength decreases and the yield ratio increases. Therefore, it shall be 450 degrees C or less.

  Even if tempering is not performed, the surface hardness becomes 350 HV10 or less due to the combination of the above component composition and accelerated cooling conditions, and further decreases when tempering is performed.

  When the plate thickness of the steel plate is reduced, a structure similar to that when the plate thickness is thick can be obtained even if the cooling rate is increased and the cooling stop temperature is increased as compared with the case where the plate thickness is thick. About the steel plate of plate | board thickness 19-40mm, it is preferable to set it as the following manufacturing methods.

Accelerated cooling: Cooling rate: 15 ° C / s or more, Cooling stop temperature: 650-500 ° C
If the cooling rate of accelerated cooling is less than 15 ° C./s, it is difficult to ensure the strength. Therefore, it is set to 15 ° C./s or more.

  If the cooling stop temperature exceeds 650 ° C., the ferrite fraction exceeds 30%, and thus strength cannot be ensured. If the cooling stop temperature is less than 500 ° C., ferrite is not generated, and a low yield ratio is not achieved. Therefore, it is set as 650-500 degreeC. After accelerated cooling, tempering at 450 ° C. or lower may be performed.

  Even if tempering is not performed, the surface hardness becomes 350 HV10 or less due to the combination of the above component composition and accelerated cooling conditions, and further decreases when tempering is performed.

  The molten steel having the composition shown in Table 1 was melted in a vacuum melting furnace, then made into a slab, and a steel plate having a predetermined thickness was obtained by hot rolling. Thereafter, the obtained steel plate was subjected to accelerated cooling to obtain a test material. Some steel plates were tempered after accelerated cooling and used as test materials.

  Each test material was subjected to ferrite fraction measurement, surface hardness measurement, tensile test, and Charpy impact test of the heat affected zone of the electroslag weld.

  The ferrite fraction was obtained by observing ¼ part of each steel sheet 500 times with an optical microscope and 5 fields of 180 μm × 150 μm, and taking the average value of the ferrite fractions therein.

  The surface hardness was a Vickers hardness test with a load of 10 kgf in accordance with JISZ2244, 20 points were measured at 0.5 mm below the surface layer, and the maximum value was taken as the representative value. Tensile tests were conducted on steel sheets with a thickness of 40 to 80 mm in accordance with JIS Z2201 by taking JIS No. 4 test pieces from two locations, 1 / 4t position and 1 / 2t position, and tensile properties (yield stress (YS)). , Tensile strength (TS), yield ratio (YR)). The test piece was taken in the L direction.

  For a steel sheet having a thickness of 19 to 40 mm, a full thickness JIS No. 5 test piece was taken in the L direction in accordance with JIS Z2201, and tensile properties (yield stress (YS), tensile strength (TS), yield ratio ( YR)) was investigated.

  Large heat input weld heat affected zone toughness: steel plate with thickness of 40-80mm is subjected to electroslag welding with heat input of 960kJ / cm and Charpy impact with weld heat affected zone 1mm away from BOND part as notch position It was evaluated by testing.

  Steel plates having a thickness of 19 to 40 mm were evaluated by a Charpy impact test in which electroslag welding with a heat input of 400 kJ / cm was performed and a weld heat affected zone 1 mm away from the BOND portion was a notch position. All Charpy impact tests were conducted at a test temperature of 0 ° C. and three test pieces, and the average value was evaluated as a representative value.

  Table 2 shows the test conditions with a thickness of 40 to 80 mm, and Table 3 shows the manufacturing conditions (slab heating temperature, rolling conditions, accelerated cooling conditions) of the test thickness with a thickness of 19 to 40 mm and the test results.

  From Tables 2 and 3, according to the present invention examples (steel 1 to 3, steel 5, 6, steel 8, steel 15, 16, and 18), the surface hardness is 350 HV10 or less, the tensile strength is 590 MPa or more, and the yield ratio is 80%. The following was obtained, and the high heat input heat affected zone toughness was 112 J or more.

  On the other hand, the comparative examples (Steel 4, 7, Steel 9-14, Steel 17) are inferior to those of the present invention in terms of surface hardness, tensile strength, yield ratio and / or high heat input heat affected zone toughness.

  In Comparative Example Steel 4, the cooling stop temperature for accelerated cooling was as high as 450 ° C., the ferrite fraction was high, and the tensile strength was less than 590 MPa. Comparative Example Steel 7 had a high accelerated cooling rate of 16 ° C./s, a low ferrite fraction, a high yield strength with respect to the tensile strength, and was over YR 80%.

  Comparative Example Steels 9 to 14 have component compositions outside the scope of the present invention, low large heat input heat affected zone toughness, and Comparative Examples Steels 9 and 10 having a high C content of 0.08% have high surface hardness, The ductility of the surface layer is inferior. In Comparative Example Steel 17, the cooling stop temperature for accelerated cooling was low, and it was over YR 80%.

The figure which shows the influence of the amount of C exerted on the high heat input welding heat affected zone toughness. The figure which shows the influence of C amount which acts on surface layer hardness. The figure which shows the influence of C amount which affects ductility (surface layer tensile test elongation). The figure which shows the influence of the amount of C which acts on intensity | strength (YS, TS).

Claims (4)

In mass%, C: 0.03-0.07%, Si: 0.05-0.5%, Mn: 0.6-2.0%, P: 0.020% or less, S: 0.0005 -0.003%, Ti: 0.005-0.03%, B: 0.0003-0.0020%, Al: 0.1% or less, N: 0.0025-0.0070, O: 0.0. 001 to 0.003%, Ca: 0.0005 to 0.005%, Mo: 0.01% or less, Nb: 0.005% or less, Cu: 0.5% or less, Ni: 1.0% Hereinafter, one or two or more of Cr: 0.5% or less and V: 0.08% or less are included, and Ceq according to the following formula (1) is 0.40 to 0.45%, according to the following formula (2) ACR satisfies 0.2 to 0.8, has a composition comprising the balance Fe and inevitable impurities, and a microstructure with a ferrite fraction of 2 to 30%. 80% yield ratio, wherein a surface hardness of 350HV10 less or less, a tensile strength 590MPa or more low yield ratio steel sheet excellent architectural high heat input weld toughness.
Ceq = C + Mn / 6 + (Cu + Ni) / 15 + (Cr + Mo + V) / 5 − (1)
ACR = (Ca− (0.18 + 130 × Ca) × O) / (1.25 × S) −−− (2)
However, each element in the formulas (1) and (2) has a content (% by mass).   Furthermore, the component composition contains one or two of Mg: 0.005% or less and REM: 0.02% or less. The yield ratio is 80% or less and the tensile strength is 590 MPa or more. Low yield ratio steel sheet for construction with excellent high heat input weld toughness. After the steel material having the composition according to claim 1 or 2 is heated to 1000 to 1200 ° C, rolling is performed such that the rolling end temperature is equal to or higher than the Ar ₃ transformation point, and then accelerated cooling is performed at an average cooling rate of 3 to 12 ° C / s, a construction that is excellent in toughness of high heat input welds, characterized in that when tempering is not performed after cooling stop, the cooling stop temperature is 400 to 200 ° C., and when tempering is performed, the cooling stop temperature is 400 to 50 ° C. A method for producing a structural low yield ratio steel sheet. After the steel material having the composition according to claim 1 or 2 is heated to 1000 to 1200 ° C, rolling is performed so that the rolling end temperature is not lower than the Ar ₃ transformation point, and then the average cooling rate is 15 ° C / s or higher and the cooling is stopped. Temperature: 650-500 degreeC After performing accelerated cooling, air cooling or tempering is performed, The manufacturing method of the low-yield-ratio steel plate for construction of the plate | board thickness of 19-40 mm excellent in the high heat input weld toughness characterized by the above-mentioned.

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