JP7248896B2 - High strength steel plate for high heat input welding - Google Patents

Description

TECHNICAL FIELD The present invention relates to a high-strength steel plate to which high heat input welding is applied.

In recent years, the requirements for the steel frames of welded structures typified by high-rise buildings have been increasing from the viewpoint of increasing the size of buildings, increasing the efficiency of construction, and improving safety against destruction during earthquakes (earthquake resistance). . Thick steel plates used for the steel frames of welded structures are required to have high strength and thickness, as well as to ensure the toughness of the high heat input welding HAZ. The “high heat input welding HAZ” means a weld heat affected zone (HAZ) formed by high heat input welding. Hereinafter, the large heat input welding HAZ may be simply referred to as the large heat input HAZ. High heat input welding is welding with a high heat input, and examples thereof include highly efficient electroslag welding and submerged arc welding.

Conventionally, when applying the above-described high heat input welding to high-strength thick steel plates, it has been considered difficult to ensure good toughness in the HAZ. For example, Non-Patent Document 1 and Non-Patent Document 2 show the HAZ toughness of an electroslag welded portion of a steel plate having a tensile strength of 780 MPa. According to FIG. 6 of Non-Patent Document 1, the fusion line (Fusion Line, FL), 1 mm from FL (HAZ1), 3 mm from FL (HAZ3), and the average of Charpy absorbed energy at notch positions 5 mm from FL (HAZ5) The value is 40J or less. 3 and 5 of Non-Patent Document 2, the average value of Charpy absorbed energy at the notch position of FL is 50 J or less.

In response to such a problem, in Patent Document 1, by dispersing fine C-enriched regions, the generation of a martensite-austenite mixed phase (Martensite-Austenite constituent, MA) in the HAZ is suppressed, and the HAZ toughness is improved. is disclosed. In Patent Document 1, the content of Si and P contained in steel is reduced, and the conditions for accelerated cooling and heat treatment after hot rolling are controlled to suppress the formation of cementite and pearlite.

Further, Patent Document 2 discloses a technique for refining crystal grains by controlling the balance of the contents of Ti, Al, O and N and improving the toughness of the HAZ. This technology combines the effect of suppressing the growth of coarse austenite grains with fine TiN particles dispersed in the steel and the effect of promoting the precipitation of intragranular ferrite using Ti-containing inclusions as transformation nuclei. there is

JP 2017-155333 A WO2017/183720

Tokuno Kazunari, and 7 others, "Large heat input welding type preheating reduction 780 N/mm2 class high tensile strength steel plate for construction", Nippon Steel Technical Report, 1997, No. 365, p. 37-43 Minoru Hirota, 5 others, "Low Yield Ratio 780 N/mm Grade 2 Steel Material for Building Structures by Online Manufacturing Process Part 3: Large Heat Input Weld Joint Properties", Summaries of Technical Papers of Annual Meeting of Architectural Institute of Japan, 2012, No. 1017

In order to increase the strength of steel sheets, it is effective to increase the carbon equivalent CeqWES, which is an index of the hardenability of steel. However, when the contents of alloying elements such as Mn and Ni are increased, the high heat input HAZ becomes a hardened structure mainly composed of coarse bainite, and a martensite-austenite mixed phase (MA), which is an embrittlement phase. ) is promoted. The generation of MA results from micro-segregation formed by local concentration of alloying elements such as Mn and Ni contained in the steel sheet. The micro-segregations are heated by the welding heat effect, cooled, and then become MA through a phase transformation. MA is a hard phase and acts as a starting point for fracture to lower HAZ toughness.

In addition, since the high heat input HAZ is heated to a high temperature, the grain growth of austenite is promoted and the grains of the steel are coarsened. Furthermore, increasing the content of alloying elements hardens the HAZ. These also cause a decrease in HAZ toughness. As described above, when the carbon equivalent CeqWES is increased in order to strengthen the steel sheet, a coarse bainite-based structure formed by MA is formed in the high heat input HAZ, and the toughness tends to decrease.

As described above, in the case of steel plates containing Mn and Ni, which are alloying elements that increase strength, the HAZ toughness of high heat input welding is affected by the formation of MA due to microsegregation, coarsening of prior austenite, and hardening of bainite. significantly lower. Therefore, it has been difficult to achieve both high strength of the steel plate (base material) and ensuring toughness of the high heat input HAZ based on the conventional guideline for chemical composition design of the thick steel plate.
The present invention has been made in view of such circumstances, and it is an object of the present invention to propose a new guideline for composition design and to provide a thick steel plate for high heat input welding based on this.

The inventors of the present invention suppress the formation of MA, which significantly embrittles the high heat input HAZ of high strength steel sheets, and refine the HAZ structure. A study was conducted in order to ensure the toughness of the HAZ. As a result, the inventors have found that controlling the Mn/Ni ratio of the steel components to 0.80 or less is effective in reducing the MA in the micro-segregation part. Furthermore, it was found that Ti-based oxides acting as nuclei for intragranular transformation significantly refine the HAZ crystal grains, resulting in a smaller size of MA.

In addition, the crystal grains of the large heat input HAZ increase the hardenability of the steel sheet to a certain level or more, specifically, the carbon equivalent CeqIIW is 0.65% or more, and the hardenability multiple DI is preferably 10.0 inches or more. It was found that by In particular, Cu enhances the hardenability and has a small adverse effect on the HAZ toughness, so it was also found that an increase in the Cu content significantly improves the HAZ toughness. Limiting the content of C is effective in suppressing hardening of the HAZ. Also, it was found that when the B content is restricted, the difference in hardness between the surface of the steel sheet (base material) and the interior in the sheet thickness direction becomes smaller, and the surface properties and workability become superior.

The present invention was made based on such findings, and the gist thereof is as follows.

[1] in % by mass,
C: 0.030% or more and 0.080% or less,
Mn: 0.3% or more and 1.3% or less,
Ni: 1.3% or more and 7.0% or less,
Cu: 0.60% or more and 2.00% or less,
Ti: 0.005% or more and 0.020% or less,
O: 0.0010% or more and 0.0040% or less,
Cr: 0% or more and 1.0% or less,
Mo: 0% or more and 1.0% or less,
W: 0% or more and 1.0% or less,
Co: 0% or more and 1.0% or less,
Nb: 0% or more and 0.10% or less,
V: 0% or more and 0.10% or less,
B: 0% or more and 0.0050% or less,
Ca: 0% or more and 0.005% or less,
Mg: 0% or more and 0.005% or less,
REM: 0% or more and 0.005% or less,
Zr: containing 0% or more and 0.005% or less,
Si: 0.10% or less,
P: 0.010% or less,
S: 0.005% or less,
Al: 0.003% or less,
N: 0.0060% or less,
is limited to
The balance consists of Fe and impurities,
Mn/Ni, which is the ratio of the Mn content to the Ni content, is 0.80 or less,
Carbon equivalent CeqWES calculated by the following formula (1) is 0.45% or more and 0.70% or less,
A high-strength steel plate for large heat input welding, having a carbon equivalent CeqIIW calculated by the following formula (2) of 0.65% or more and 0.90% or less.
CeqWES (%) = C + Mn/6 + Si/24 + Ni/40 + Cr/5 + Mo/4 + V/14
... (1)
CeqIIW (%) = C + Mn/6 + Cu/15 + Ni/15 + Cr/5 + Mo/5 + V/5
... (2)
Here, C, Mn, Si, Ni, Cr, Mo, V, and Cu in the above formulas (1) and (2) are the contents in the steel sheet of each element represented by mass%, and are not contained 0 is substituted for the element term.
[2] The high-strength steel sheet for large heat input welding according to [1] above, wherein the hardenability factor DI calculated by the following formula (3) is 10.0 inches or more and 21.0 inches or less.
DI (inch) = 0.5 x fB x ^C0.5 x (1 + 0.64 x Si) x (1 + 4.1 x Mn) x (1 + 0.27 x Cu) x (1 + 0.52 x Ni) x (1 + 2 .33×Cr)×(1+3.14×Mo)
... (3)
Here, C, Si, Mn, Cu, Ni, Cr, and Mo in the above formula (3) are the contents in the steel sheet of each element represented by mass%, and 0 is entered in the term of the element not contained. substitute. fB is 1.0 when B is less than or equal to 0.0004% and 1.3 when B is greater than 0.0004%.
[3] Furthermore, in % by mass,
Cr: 0.1% or more and 1.0% or less,
Mo: 0.1% or more and 1.0% or less,
W: 0.1% or more and 1.0% or less,
Co: 0.1% or more and 1.0% or less,
Nb: 0.005% or more and 0.10% or less,
V: 0.005% or more and 0.10% or less,
The high-strength steel sheet for large heat input welding according to the above [1] or [2], containing one or more of
[4] Furthermore, in % by mass,
B: The high-strength steel sheet for large heat input welding according to any one of [1] to [3], containing 0% or more and 0.0004% or less.
[5] Furthermore, in mass %,
Ca: 0.0001% or more and 0.005% or less,
Mg: 0.0001% or more and 0.005% or less,
REM: 0.0001% or more and 0.005% or less,
Zr: 0.0001% or more and 0.005% or less,
The high-strength steel sheet for large heat input welding according to any one of [1] to [4] above, containing one or more of

ADVANTAGE OF THE INVENTION According to this invention, the high strength steel plate for large heat input welding based on the guideline of a new component design can be provided.

It is a figure which shows the collection point of the Charpy test piece in an electroslag welding T-shaped joint.

A high-strength steel sheet for large heat input welding according to one embodiment of the present invention will be described below. First, the study results of the present inventors who have completed the present invention and the new findings obtained will be described in detail.

The high-strength steel sheet for large heat input welding (hereinafter also simply referred to as "steel sheet") according to the present embodiment contains C, Mn, Ni, and Cu, which are alloying elements that improve hardenability. The steel plate according to the present embodiment is manufactured by subjecting a steel slab obtained by melting and casting steel to hot rolling. A steel sheet manufactured in this way has micro segregation formed at the interface of the solidified structure due to solidification during casting, as described above. The concentration of alloying elements such as Mn and Ni in the micro-segregated parts is difficult to be eliminated by short-time heating such as the heat effect of welding. Therefore, when high heat input welding is applied to a steel plate containing C, Mn, and Ni, micro-segregation tends to remain in the high heat input HAZ. The HAZ micro-segregation part locally formed in this manner becomes C-enriched retained austenite by heating, and becomes hard MA after cooling. Since such MA becomes a starting point of fracture and lowers the HAZ toughness, it is desirable to suppress the formation of stable residual austenite, in other words, the generation of residual austenite. As a result of intensive studies, the inventors of the present invention have obtained a new finding that Mn retards the decomposition of retained austenite during cooling of the high heat input HAZ compared to Ni.

As described above, when the high heat input HAZ is cooled, when the high heat input HAZ is cooled to room temperature without decomposition of the retained austenite in the micro-segregation part, this retained austenite becomes MA and deteriorates the toughness of the HAZ. Let Mn retards the decomposition of retained austenite as compared with Ni, and is therefore likely to increase MA. In other words, Ni is considered to have less adverse effect on the toughness of the high heat input HAZ than Mn. Therefore, the present inventors focused on the balance between the content of Mn and the content of Ni in the steel, and by optimizing the ratio of the two, the hardenability of the steel is improved and the amount of MA generated is suppressed. I thought I could. Specifically, the present inventors found that when Mn/Ni, which is the ratio obtained by dividing the Mn content in the steel by the Ni content, is 0.80 or less, the amount of MA produced in the high heat input HAZ We found a phenomenon to reduce This phenomenon is due to the decomposition of retained austenite, which is generated by the concentration of C in the micro-segregation zone during heating, that is, when the retained austenite transforms into ferrite and cementite. and Ni atoms.

In addition, the present inventors have found that the concentration of C at the start of decomposition of retained austenite in the micro-segregated part affects the type and amount of alloying elements such as Mn and Ni contained in the steel plate rather than the content of C in the entire steel plate. found to be In other words, the present inventors found that the lower the C content in the steel component, the more accelerated the bainite transformation, the smaller the amount of retained austenite that becomes MA, and the smaller the size of retained austenite. This phenomenon is presumed to be related to the mechanism of incomplete transformation of bainite. Further, as a result of further studies, the present inventors found that by limiting the Mn/Ni ratio to 0.80 or less in the steel composition and limiting the C content to 0.080% or less, the micro segregation part It was found that the production of MA in can be suppressed.

In addition, in high-strength steel sheets for high heat input welding, hardening of the HAZ and coarsening of grains cause deterioration of the toughness of the high heat input HAZ. Limiting the content of C is effective for suppressing HAZ hardening. On the other hand, one effective method for suppressing the coarsening of HAZ crystal grains is the use of intragranular transformation using Ti-based oxides as nuclei. The present inventors investigated the relationship between the metal structure and toughness of steel subjected to a simulated heat cycle simulating high heat input welding. As a result, the Ti-based oxides dispersed in the steel promote the intragranular transformation to refine the crystal grains, and limit the Mn/Ni to 0.80 or less to suppress the formation of MA. , It was found that the toughness of the large heat input HAZ can be significantly improved.

In this way, the present inventors made the Ti content of the steel sheet 0.005% or more to disperse the Ti-based oxides and refine the crystal grains of the high heat input HAZ. Then, in order to refine the crystal grains by the Ti-based oxide, the Al content is restricted. This is because when the Al content in the steel sheet increases, O (oxygen) in the steel sheet is likely to be consumed for the generation of Al-based oxides, and the generation of Ti-based oxides is suppressed. Therefore, the amount of Al contained in the high-strength steel sheet for high heat input welding according to this embodiment is limited to 0.003% or less. On the other hand, generation of micron-sized coarse TiN can be avoided by limiting the Ti content to 0.02% or less. Also, the O content is limited to 0.0040% or less so as not to form coarse inclusions that affect the HAZ toughness.

Furthermore, in the present invention, the crystal grains can be made finer by increasing the contents of Cu and Ni to ensure sufficient hardenability. Specifically, the lower limits of the carbon equivalents CeqWES and CeqIIW are appropriately set, and preferably the lower limit of the hardenability multiple DI is appropriately set. On the other hand, the upper limits of CeqWES and CeqIIW are appropriately set, and preferably the upper limit of DI is set appropriately, in order to prevent an extreme decrease in ductility and a decrease in absorbed energy. The carbon equivalents CeqWES and CeqIIW and DI are controlled by the C, Mn, Si, Cu, Ni, Cr, Mo, V content. As a result of intensive studies, the present inventors have found that the carbon equivalent CeqWES determined by the following formula (1) is 0.45% or more and 0.70% or less, and the CeqIIW determined by the following formula (2) is 0.65% or more. , is controlled to 0.90% or less, the toughness of the large heat input HAZ is ensured. Preferably, the hardenability multiple DI determined by the following formula (3) is controlled within the range of 10.0 inches or more and 21.0 inches or less for grain refinement.

CeqWES (%) = C + Mn/6 + Si/24 + Ni/40 + Cr/5 + Mo/4 + V/14
... (1)
CeqIIW (%) = C + Mn/6 + Cu/15 + Ni/15 + Cr/5 + Mo/5 + V/5
... (2)
DI (inch) = 0.5 x fB x ^C0.5 x (1 + 0.64 x Si) x (1 + 4.1 x Mn) x (1 + 0.27 x Cu) x (1 + 0.52 x Ni) x (1 + 2 .33×Cr)×(1+3.14×Mo)
... (3)
Here, C, Mn, Si, Ni, Cr, Mo, V, and Cu in the above formulas (1), (2), and (3) are the contents in the steel sheet of each element represented by mass%. 0 is substituted for elements not contained. fB is 1.0 when B is 0.0004% or less, and 1.3 when B is greater than 0.0004%.

Next, the chemical composition (steel composition) of the high-strength steel sheet for high heat input welding according to this embodiment will be described. In addition, in the following explanation of the chemical components, mass % is simply expressed as %.

(C: 0.030% or more and 0.080% or less)
C is an element that enhances the hardenability of steel and contributes to high strength. In this embodiment, the C content is 0.030% or more. The content of C is preferably 0.035% or more, more preferably 0.040% or more. On the other hand, the C content is 0.080% or less from the viewpoint of suppressing HAZ hardening and ensuring toughness. The C content is preferably 0.075% or less, more preferably 0.070% or less.

(Mn: 0.30% or more and 1.30% or less)
Mn is an element that enhances the hardenability of steel and contributes to high strength. In this embodiment, the Mn content is 0.30% or more. The Mn content is preferably 0.40% or more, more preferably 0.50% or more. On the other hand, from the viewpoint of suppressing excessive generation of MA in the high heat input HAZ, the Mn content is 1.30% or less in the present embodiment. The Mn content is preferably 1.20% or less, more preferably 1.10% or less.

(Ni: 1.30% or more and 7.00% or less)
Ni is an element that enhances the hardenability of steel and contributes to high strength, and at the same time, it is an element that enhances the toughness of the high heat input HAZ. From the viewpoint of ensuring strength and toughness, the Ni content is 1.30% or more in the present embodiment. The Ni content is preferably 1.80% or more, more preferably 2.00% or more, and still more preferably 2.50% or more. On the other hand, Ni is an expensive element, and from the viewpoint of suppressing an increase in manufacturing cost, the Ni content is 7.00% or less in the present embodiment. The Ni content is preferably 6.50% or less, more preferably 6.00% or less, and still more preferably 5.50% or less.

(Mn/Ni: 0.80 or less)
Both Mn and Ni are elements that contribute to increasing the strength of steel. is preferably less. From the viewpoint of ensuring toughness while increasing the strength of the high heat input HAZ, in the steel sheet of the present embodiment, Mn/Ni, which is the ratio obtained by dividing the Mn content in the steel by the Ni content, is 0.5. 80 or less. Mn/Ni is preferably 0.70 or less, more preferably 0.60 or less. The lower limit of Mn/Ni may be a ratio obtained by dividing the lower limit of the Mn content by the upper limit of the Ni content, that is, it may be 0.04 or more. Mn/Ni may be 0.10 or more, or may be 0.20 or more.

(Cu: 0.60% or more and 2.00% or less)
Cu is an element that has a small adverse effect on weldability and HAZ toughness and increases the hardenability of steel to improve the strength and toughness of the base material. From the viewpoint of ensuring strength and toughness, the steel sheet of the present embodiment has a Cu content of 0.60% or more. The Cu content is preferably 0.70% or more, more preferably 0.80% or more. On the other hand, from the viewpoint of suppressing the generation of Cu cracks during hot rolling of the steel sheet, the Cu content is 2.00% or less in the present embodiment. The Cu content is preferably 1.90% or less, more preferably 1.80% or less.

(Ti: 0.005% or more and 0.020% or less)
Ti is an element that forms Ti oxide and TiN. TiN suppresses coarsening of γ grains by a pinning effect, and Ti oxides serve as intragranular transformation nuclei and contribute to refinement of HAZ crystal grains. In addition, since Ti forms TiN to suppress the formation of BN, it is also effective in ensuring solid solution B that improves hardenability. In order to ensure the toughness of the high heat input HAZ, the Ti content is 0.005% or more in this embodiment. The content of Ti is preferably 0.007% or more. On the other hand, in the present embodiment, the Ti content is 0.020% or less from the viewpoint of suppressing the deterioration of the toughness of the base metal and HAZ and the deterioration of the surface quality of the slab. The Ti content is preferably 0.018% or less, more preferably 0.016% or less.

(O: 0.0010% or more and 0.0040% or less)
O combines with a deoxidizing element such as Ti to form an oxide. Ti oxides act as intragranular transformation nuclei and contribute to grain refinement. In order to obtain this effect, the O content in the steel sheet of the present embodiment is 0.0010% or more. However, the content of O is 0.0040% or less from the viewpoint of suppressing the deterioration of the toughness of the base metal and HAZ due to the deterioration of the cleanliness of the steel. The content of O is preferably 0.0030% or less.

(Si: 0.10% or less)
Si is an element contained in steel for deoxidizing and increasing strength. On the other hand, Si is also an element that promotes the formation of MA, and the inventors of the present invention have obtained knowledge that Si greatly affects the formation of MA in the micro-segregation part of the high heat input HAZ. Therefore, in order to ensure the toughness of the high heat input HAZ, it is necessary to limit the Si content, and in the present embodiment, the Si content is 0.10% or less. The Si content is preferably 0.08% or less, more preferably 0.05% or less. Although the lower limit of the Si content is not particularly limited, the Si content may be 0.01% or more from the viewpoint of manufacturing cost.

(P: 0.010% or less)
P is an impurity harmful to toughness. The P content must be limited in order to stably ensure the toughness of the high heat input HAZ, and is 0.010% or less in the present embodiment. The P content is preferably 0.008% or less. Although the lower limit of the P content is not limited, the P content may be 0.001% or more from the viewpoint of manufacturing cost.

(S: 0.005% or less)
S is an impurity, and if it is contained in a large amount in steel, it may form coarse inclusions and lower the toughness. Therefore, the S content needs to be limited in order to stably ensure the toughness of the high heat input HAZ, and in this embodiment, the S content is 0.005% or less. The S content is preferably 0.004% or less. Although the lower limit of the amount of S is not limited, the content of S may be 0.0001% or more from the viewpoint of manufacturing cost. The S content may be 0.001% or more.

(Al: 0.003% or less)
Al is an element that forms an oxide and is used for deoxidation. However, as the Al content increases, the formation of Ti-based oxides is suppressed. Therefore, the content of Al is 0.003% or less in the present embodiment from the viewpoint of promoting the formation of Ti-based oxides. The Al content is preferably 0.002% or less, more preferably 0.001% or less. As described above, Al is a deoxidizing element, but deoxidation is possible with Si, Mn, and Ti, and the Al content may be 0%.

(N: 0.0060% or less)
N is an element that constitutes TiN. Fine TiN suppresses the coarsening of γ grains by pinning, but coarse TiN may act as fracture initiation points in the HAZ and reduce toughness. From the viewpoint of suppressing the formation of coarse TiN and ensuring HAZ toughness, the N content is 0.0060% or less in the present embodiment. The N content is preferably 0.0040% or less. Although the lower limit of the N content is not limited in the present embodiment, the N content may be 0.0001% or more from the viewpoint of manufacturing cost. From the viewpoint of exhibiting the effect of suppressing the growth of γ grains in the HAZ, the N content is preferably 0.0010% or more.

(Carbon equivalent CeqWES: 0.45% or more and 0.70% or less)
The carbon equivalent CeqWES is an index of hardenability that greatly affects the strength of the steel sheet (base material) and the grain size of the HAZ. In the present embodiment, the carbon equivalent CeqWES is 0.45% or more from the viewpoint of increasing the hardenability of the steel, ensuring the strength of the base material, and refining the crystal grains of the HAZ. Carbon equivalent CeqWES is preferably 0.50% or more, more preferably 0.55% or more. On the other hand, from the viewpoint of suppressing hardening of the high heat input HAZ and ensuring toughness, the carbon equivalent CeqWES is 0.70% or less in the present embodiment. The carbon equivalent CeqWES is preferably 0.65% or less. The carbon equivalent CeqWES is calculated by the following formula (1) depending on the contents of alloying elements.

CeqWES (%) = C + Mn/6 + Si/24 + Ni/40 + Cr/5 + Mo/4 + V/14
(1)
Here, C, Mn, Si, Ni, Cr, Mo, and V in the above formula (1) are the contents in the steel sheet of each element represented by mass %, and 0 is substituted for the element not contained. do.

(Carbon equivalent CeqIIW: 0.65% or more and 0.90% or less)
The carbon equivalent CeqIIW is an index of hardenability that greatly affects the strength of the steel sheet (base material) and the grain size of the HAZ. Since the steel sheet according to the present embodiment contains Cu, the carbon equivalent CeqIIW is an important index. In the present embodiment, the carbon equivalent CeqIIW is 0.65% or more from the viewpoint of enhancing the hardenability of the steel, ensuring the strength of the base material, and refining the crystal grains of the HAZ. The carbon equivalent CeqIIW is preferably 0.70% or more, more preferably 0.75% or more. On the other hand, from the viewpoint of suppressing hardening of the high heat input HAZ and ensuring toughness, the carbon equivalent CeqIIW is 0.90% or less in the present embodiment. The carbon equivalent CeqIIW is preferably 0.89% or less, more preferably 0.85% or less. The carbon equivalent CeqWES is calculated by the following formula (2) depending on the contents of alloying elements.

CeqIIW (%) = C + Mn/6 + Cu/15 + Ni/15 + Cr/5 + Mo/5 + V/5
... (2)
Here, C, Mn, Cu, Ni, Cr, Mo, and V in the above formula (2) are the contents in the steel sheet of each element expressed in mass%, and 0 is substituted for the elements not contained. do.

(Hardenability multiple DI: 10.0 inch or more and 21.0 inch or less)
The hardenability factor DI is an index of hardenability that affects the strength of the steel sheet (base material) and the grain size of the HAZ. The hardenability multiple DI is preferably 10.0 inches or more from the viewpoint of enhancing the hardenability of the steel, ensuring the strength of the base material, and refining the crystal grains of the HAZ. The hardenability multiple DI is more preferably 12.0 inches or more, and still more preferably 14.0 inches or more. On the other hand, from the viewpoint of suppressing hardening of the high heat input HAZ and ensuring toughness, the hardenability multiple DI is preferably 21.0 inches or less. The hardenability multiple DI is more preferably 20.0 inches or less, and still more preferably 19.0 inches or less. The hardenability factor DI is calculated by the following formula (3) depending on the contents of alloying elements. fB is a coefficient indicating the effect of B on hardenability, and varies depending on the B content. When the content of B is 0.0004% or less, the effect of B on hardenability is not considered and fB is 1.0. When the content of B exceeds 0.0004%, the effect of B on hardenability is taken into account, and fB is 1.3.

DI (inch) = 0.5 x fB x ^C0.5 x (1 + 0.64 x Si) x (1 + 4.1 x Mn) x (1 + 0.27 x Cu) x (1 + 0.52 x Ni) x (1 + 2 .33×Cr)×(1+3.14×Mo)
... (3)
Here, C, Si, Mn, Cu, Ni, Cr, and Mo in the above formula (3) are the contents in the steel sheet of each element represented by mass%, and do not contain the selective elements Cr and Mo described later. 0 is substituted for each term. fB is 1.0 when B is 0.0004% or less, and 1.3 when B is greater than 0.0004%.

The rest of the chemical composition of the steel sheet according to this embodiment is iron (Fe) and impurities. The term "impurities" refers to components that are mixed from raw materials such as ores, scraps, and other factors when steel sheets are manufactured industrially, and are permissible within a range that does not adversely affect the steel sheet according to the present embodiment. means. However, among the impurities, the upper limit of the content of P and S is restricted as described above.

In order to improve the strength and toughness of the steel sheet (base material), the steel sheet of the present embodiment may optionally contain one or two of the selective elements Cr, Mo, W, Co, Nb, V, and B shown below. More than one seed may be included.

(Cr: 0% or more and 1.0% or less)
Cr is an element that may be mixed into a steel sheet as an impurity from scrap or the like. However, the lower limit of the Cr content is not limited, and may be 0%. Cr is also an element that improves the strength of the base material. Therefore, in this embodiment, the Cr content may be 0.1% or more. The Cr content is preferably 0.2% or more, more preferably 0.3% or more. However, from the viewpoint of suppressing deterioration of the toughness and weldability of the large heat input HAZ, the Cr content is 1.0% or less in the present embodiment. The Cr content is preferably 0.8% or less, more preferably 0.5% or less.

(Mo: 0% or more, 1.0% or less)
Mo is an element that may be mixed into a steel sheet as an impurity from scrap or the like. However, the lower limit of the Mo content is not limited, and may be 0%. Mo is also an element that improves the strength and toughness of the base material. Therefore, in this embodiment, the Mo content may be 0.1% or more. The Mo content is preferably 0.2% or more, more preferably 0.3% or more. However, in the present embodiment, the content of Mo is 1.0% or less from the viewpoint of suppressing the deterioration of the toughness and weldability of the high heat input HAZ and suppressing the increase of the alloy cost. The Mo content is preferably 0.5% or less.

(W: 0% or more, 1.0% or less)
W is an element that may be mixed into the steel sheet as an impurity from scrap or the like. However, the lower limit of the W content is not limited, and may be 0%. W is also an element that increases the strength and toughness of the base material. Therefore, in this embodiment, the W content may be 0.1% or more. The W content is preferably 0.2% or more, more preferably 0.3% or more. However, in the present embodiment, the W content is 1.0% or less from the viewpoint of suppressing deterioration of the toughness and weldability of the high heat input HAZ and suppressing an increase in alloy cost. The content of W is preferably 0.5% or less.

(Co: 0% or more, 1.0% or less)
Co is an element that may be mixed into a steel sheet as an impurity from scrap or the like. However, the lower limit of the Co content is not limited, and may be 0%. Co is also an element that has little adverse effect on weldability and HAZ toughness and improves the strength and toughness of the base material. Therefore, in this embodiment, the Co content may be 0.1% or more. However, the Co content is 1.0% or less from the viewpoint of suppressing an increase in alloy cost. The Co content is preferably 0.5% or less.

(Nb: 0% or more and 0.10% or less)
Nb is an element that may be mixed into a steel sheet as an impurity from scrap or the like. However, the lower limit of the Nb content is not limited, and may be 0%. Nb is also an element that improves the strength and toughness of the base material. Therefore, in this embodiment, the Nb content may be 0.005% or more. However, the content of Nb is 0.10% or less from the viewpoint of suppressing deterioration of toughness and weldability in the high heat input HAZ. The Nb content is preferably 0.05% or less, more preferably 0.03% or less.

(V: 0% or more, 0.10% or less)
V is an element that may be mixed into a steel sheet as an impurity from scrap or the like. However, the lower limit of the V content is not limited, and may be 0%. V is also an element that improves the strength of the base material. Therefore, in the present embodiment, the V content may be 0.005% or more. However, the V content is 0.10% or less from the viewpoint of suppressing deterioration of the toughness and weldability of the high heat input HAZ and suppressing an increase in alloy cost. The V content is preferably 0.08% or less, more preferably 0.06% or less.

(B: 0% or more, 0.0050% or less)
B is an element that may be mixed into the steel sheet as an impurity from scrap or the like. However, the lower limit of the content of B is not limited, and may be 0%. B is an element that significantly improves the hardenability of steel. Even a very small amount significantly improves the hardenability of steel, so the B content is preferably 0.0003% or more. On the other hand, from the viewpoint of suppressing deterioration of the toughness and weldability of the high heat input HAZ, the B content is 0.0050% or less in the present embodiment. The content of B is preferably 0.0030% or less, more preferably 0.0020% or less. However, the B content may be 0.0004% or less from the viewpoint of suppressing an increase in the hardness of the surface layer of the steel sheet and preventing deterioration of surface properties, workability, and the like.

Furthermore, the steel sheet according to the present embodiment can contain one or more of the selective elements Ca, Mg, REM, and Zr shown below, if necessary, in order to control the form of inclusions.

(Ca: 0% or more, 0.005% or less)
Ca is an element that forms oxides, sulfides, and oxysulfides, suppresses the formation of coarse inclusions, and increases the toughness of the base metal and HAZ. Therefore, in this embodiment, the content of Ca may be 0.0001% or more. However, in the present embodiment, the Ca content is 0.005% or less from the viewpoint of suppressing an increase in Ca-based inclusions that act as starting points for brittle fracture. The content of Ca is preferably 0.004% or less. Note that the Ca content may be 0%.

(Mg: 0% or more, 0.005% or less)
Mg, like Ca, is an element that forms oxides, sulfides, and oxysulfides, suppresses the formation of coarse inclusions, and increases the toughness of the base metal and HAZ. Therefore, in this embodiment, the content of Mg may be 0.0001% or more. However, in the present embodiment, the Mg content is 0.005% or less from the viewpoint of suppressing an increase in Mg-based inclusions that act as starting points for brittle fracture. The content of Mg is preferably 0.003% or less. Note that the content of Mg may be 0%.

(REM: 0% or more, 0.005% or less)
REM (rare earth element) is a general term for two elements, Sc and Y, and fifteen lanthanoid elements, such as La, Ce, and Nd. The REM referred to in this embodiment is composed of one or more selected from these rare earth elements, and the REM content described below is the total content of the rare earth elements.
REM, like Ca and Mg, is an element that forms oxides, sulfides, and oxysulfides, suppresses the formation of coarse inclusions, and increases the toughness of the base metal and HAZ. Therefore, the content of REM may be 0.0001% or more. However, in the present embodiment, the REM content is 0.005% or less from the viewpoint of suppressing an increase in REM inclusions that act as starting points for brittle fracture. The REM content is preferably 0.003% or less. Note that the content of REM may be 0%.

(Zr: 0% or more and 0.005% or less)
Zr, like Ca, Mg, and REM, is an element that forms oxides, sulfides, and oxysulfides, suppresses the formation of coarse inclusions, and increases the toughness of the base metal and HAZ. Therefore, the Zr content may be 0.0001% or more. However, in the present embodiment, the Zr content is 0.005% or less from the viewpoint of suppressing an increase in Zr-based inclusions that act as starting points for brittle fracture. The Zr content is preferably 0.003% or less. Note that the Zr content may be 0%.

The high-strength steel sheet for large heat input welding according to the present embodiment is suitable for applications that require a high-strength and thick steel sheet. The high-strength steel sheet for large heat input welding according to the present embodiment is particularly suitable for applications in which large heat input welding with high welding work efficiency is performed and the required level of HAZ toughness is high. Specifically, the high-strength steel plate for large heat input welding according to the present embodiment is subjected to diaphragm welding (electroslag welding) such as four-sided box columns for building steel frames, and has a high-strength thickness that requires HAZ toughness. Suitable for steel plates.
Demands for thick steel plates for welded structures are becoming more sophisticated as buildings become larger, construction becomes more efficient, and safety is required to be improved. Therefore, in the high-strength steel sheet for high heat input welding according to the present embodiment, it is preferable that the plate thickness is 50 mm or more and 100 mm or less and the yield strength is 630 MPa or more from the viewpoint of strength. The upper limit of the yield strength is not limited, and the yield strength may be 750 MPa or less, for example. Moreover, from the viewpoint of earthquake resistance, the yield ratio of the high-strength steel sheet for large heat input welding according to the present embodiment is preferably 85% or less. The lower limit of the yield ratio is not limited, and the yield ratio may be 70% or more, for example. Furthermore, from the viewpoint of high efficiency of construction and earthquake resistance, the average value of the Charpy absorbed energy (test temperature 0° C.) in the HAZ of the large heat input weld is preferably 70 J or more. The high heat input welding includes, for example, electroslag welding and submerged arc welding.

Next, a method for manufacturing a high-strength steel sheet for high heat input welding according to this embodiment will be described.

The high-strength steel sheet for high heat input welding according to the present embodiment is manufactured by melting steel, casting it to manufacture a steel slab, and hot rolling the obtained steel slab. The manufacturing method of the steel slab is not limited, and it may be manufactured by a known method. For example, steel slabs are produced by a method such as continuous casting, ingot casting-slabbing, or the like after being melted by a normal refining process such as a converter or an electric furnace. After being hot rolled, the billet may be directly subjected to controlled cooling such as water cooling, or may be subjected to heat treatment after air cooling. Also, the steel slab may be hot-rolled as it is after being manufactured by smelting and casting steel. However, as will be described later, the billet is preferably cooled after casting, reheated to a temperature of Ac3 or above, and subjected to hot rolling.

Preferred manufacturing conditions for the high-strength steel sheet for high heat input welding according to the present embodiment will be described below.

A steel slab having a thickness of 200 mm or more, which is composed of the chemical components described above and is manufactured by a continuous casting method, is once cooled to 400° C. or less. After that, the billet is heated to a temperature range of 900° C. or higher and 1250° C. or lower and subjected to hot rolling to produce a steel plate having a thickness of 50 mm or higher and 100 mm or lower. The steel plate is subjected to various heat treatments as required.

If the steel slab after continuous casting is hot-charged into a heating furnace without being cooled to 400°C or less, the coarse γ structure generated during casting will remain in the steel slab after heating, and the structure of the steel sheet will deteriorate. may not be sufficiently refined, resulting in deterioration of low-temperature toughness. Therefore, it is preferable that the steel slab after continuous casting is once cooled to 400° C. or lower.

The heating temperature of the steel slab is preferably 900° C. or higher in order to dissolve carbides and nitrides precipitated on the steel slab after casting and promote the formation of TiN during hot rolling. In particular, when B is included, N in the heated billet forms TiN during hot rolling, suppressing the formation of BN. As a result, in the steel sheet, solid-solution B, which improves the hardenability of steel, and TiN, which suppresses grain growth, are sufficiently secured. On the other hand, the heating temperature of the billet is preferably 1250° C. or less from the viewpoint of suppressing coarsening of γ grains, refining the metal structure after hot rolling, and suppressing deterioration of low temperature toughness. preferable. The heating temperature is more preferably 1200° C. or less.
When quenching is performed directly after hot rolling, the end temperature (finishing temperature) of hot rolling is preferably in the austenite (γ) single phase region, that is, the Ar ₃ transformation point at which ferrite transformation starts or higher. At this time, even if the surface layer temperature of the steel sheet is in the austenite (γ)/ferrite (α) two-phase region at the end of hot rolling, there is no problem if the temperature at the center in the thickness direction is in the γ single-phase region. do not have. The finishing temperature of hot rolling may be 750° C. or higher. The finishing temperature of hot rolling is preferably 900° C. or lower from the viewpoint of refinement of the metal structure. The Ar ₃ transformation point (°C) can be obtained by the following formula (4).

Ar ₃ transformation point=868−396×C+24.6×Si−68.1×Mn−36.1×Ni−20.7×Cu−24.8×Cr+29.1×Mo (4)
Here, C, Si, Mn, Ni, Cu, Cr, and Mo in the above formula (4) are the contents in the steel sheet of each element represented by mass%, and 0 is substituted for the element not contained. do.

Furthermore, when quenching is performed directly after hot rolling, hot rolling is finished in the γ single-phase region, and water cooling is subsequently performed to adjust the quality of the steel sheet. On the other hand, when the steel sheet is air-cooled after hot rolling, it is subjected to reheating to the γ single phase region and subsequent quenching (γ reheating and quenching). Further, steel sheets that have been subjected to direct quenching or γ reheating quenching after hot rolling may be subjected to various heat treatments in order to adjust the material properties.

Steel sheets subjected to these quenching treatments (direct quenching or γ reheating quenching) are reheated to a two-phase region in which austenite (γ) and ferrite (α) coexist, and then reheated to reduce the yield ratio. In some cases, subsequent quenching (γ/α reheating quenching) is applied. Here, the two-phase region is the Ac ₁ transformation point or more and less than the Ac ₃ transformation point, and the Ac ₁ transformation point and the Ac ₃ transformation point can be obtained by the following equations (5) and (6), respectively.

Ac ₁ transformation point=750.8-26.6C+17.6Si-11.6Mn-22.9Cu-23.0Ni+24.1Cr+22.5Mo-39.7V-5.7Ti+232.4Nb-169.4Al-894.7B .・(5)
Ac ₃ transformation point=910-203√C+44.7Si-30Mn-400Al-15.2Ni+104V+31.5Mo+13.1W+11Cr+20Cu-700P-400Ti (6)
Here, C, Si, Mn, Cu, Ni, Cr, Mo, V, Ti, Nb, Al, B, W, and P in the above formulas (5) and (6) are expressed in mass%. is the content in the steel sheet, and 0 is substituted for elements that are not contained.

In addition, the steel sheet may be tempered in order to finally adjust the strength, yield ratio and toughness of the steel sheet. When tempering is performed, the tempering temperature is preferably 350°C or higher and 600°C or lower.

Here, the finishing temperature of hot rolling, the γ reheating quenching temperature, the γ/α reheating quenching temperature, and the tempering temperature all refer to the temperature at the center in the plate thickness direction. The temperature at the center in the plate thickness direction can be obtained by heat transfer calculation from the temperature of the steel plate surface measured with a radiation thermometer.

The high-strength steel sheet for large heat input welding according to the present embodiment can be manufactured by the manufacturing method described above.

The high-strength steel sheet for high heat input welding according to the present embodiment has good HAZ toughness even when subjected to high heat input welding such as electroslag welding and submerged arc welding, in which the welding heat input exceeds 50 kJ / mm. Secured.

In addition, the high-strength steel sheet for large heat input welding according to the present embodiment preferably has a yield strength of 630 MPa or more, and Charpy absorbed energy (test temperature 0 ° C. ) is 70 J or more. Therefore, the high-strength steel sheet for large heat input welding according to the present embodiment is suitable for building steel frames, and the high-strength steel sheet for large heat input welding according to the present embodiment contributes to the progress of tall buildings and large spans. In addition, construction efficiency and seismic safety can be improved.

Examples of the present invention are shown below. However, the examples shown below are examples of the present invention, and the present invention is not limited to the examples described below.

Steel smelting and continuous casting in a converter have a thickness of 300 mm. After the continuous casting, the steel slab was cooled to room temperature, reheated to a temperature range of 1000° C. or higher and 1200° C. or lower, and hot rolled. The finishing temperature of hot rolling is 750° C. or higher and 900° C. or lower. When the hot-rolled steel sheet is directly quenched, the hot-rolling finishing temperature is in the γ single-phase region (Ar ₃ transformation point or higher).
Next, the steel sheets after hot rolling were heat-treated under the conditions shown in Tables 3 and 4. In Tables 3 and 4, "γ reheating and quenching temperature" is the heating temperature when a steel sheet air-cooled after hot rolling is subjected to γ reheating and quenching. On the other hand, the "γ/α reheating quenching temperature" is the heating temperature when direct quenching or γ reheating quenching is performed after hot rolling, and then γ/α reheating quenching is performed.

Samples were taken from the steel plates thus produced and chemical analysis was carried out. The chemical composition of each steel plate is shown in Tables 1 and 2, and the plate thickness is shown in Tables 5 and 6. The carbon equivalents CeqWES, CeqIIW, and DI shown in Tables 1 and 2 were determined by the following formulas (1), (2), and (3), respectively.

CeqWES (%) = C + Mn/6 + Si/24 + Ni/40 + Cr/5 + Mo/4 + V/14
... (1)
CeqIIW (%) = C + Mn/6 + Cu/15 + Ni/15 + Cr/5 + Mo/5 + V/5
... (2)
DI (inch) = 0.5 x fB x ^C0.5 x (1 + 0.64 x Si) x (1 + 4.1 x Mn) x (1 + 0.27 x Cu) x (1 + 0.52 x Ni) x (1 + 2 .33×Cr)×(1+3.14×Mo)
... (3)
Here, C, Mn, Si, Ni, Cr, Mo, V, and Cu in the above formulas (1), (2), and (3) are the contents in the steel sheet of each element represented by mass%. 0 is substituted for elements not contained. fB in the formula (3) is 1.0 when B is 0.0004% or less, and 1.3 when it exceeds 0.0004%.

<Mechanical Properties of Base Material>
The test piece used for the evaluation of the mechanical properties of the base metal, that is, the tensile test and the Charpy impact test, was taken from a position of 1/4 of the plate thickness of the thick steel plate.
The tensile test was performed at room temperature using two test pieces in accordance with JIS Z 2241:2011. YS (0.2% yield strength) and TS (tensile strength) are each average values of two test pieces. YR (yield ratio) is the ratio of YS to TS and is expressed as a percentage, ie, 100*(YS/TS). The unit of YR (yield ratio) is %.
The Charpy impact test was performed using three V-notch test pieces in accordance with JIS Z 2242:2018, and absorbed energy was measured. The test temperature is 0°C. The absorbed energy (KV ₂ (0° C.)) of the base material is the average value (arithmetic mean) of the absorbed energies of the three test pieces thus measured.

A sample was prepared by mechanically polishing a plate thickness section (L section) parallel to the rolling direction of the steel sheet, and the Vickers hardness was measured according to JIS Z 2244:2009. The positions where the Vickers hardness was measured were positions within 3 mm in the plate thickness direction from the steel plate surface and positions 1/4 thickness from the steel plate surface in the plate thickness direction. The Vickers hardness measurement load was 10 kgf, and three measurements were performed at each position. The average value of the measurement results at positions within 3 mm in the plate thickness direction from the steel plate surface was taken as the surface layer hardness Hvs. Also, Hvq was the average value of the measurement results at a position 1/4 thickness from the steel plate surface in the plate thickness direction. The hardness difference ΔHv is calculated by the following formula (7).

ΔHv = Hvs - Hvq (7)

<HAZ toughness of welded joint>
Evaluation of HAZ toughness of welded joints was performed using welded joints of each thick steel plate produced by electroslag welding (ESW).
The tee joint illustrated in FIG. 1 was made by electroslag welding (ESW). Welding was performed in one pass, and high heat input welding with a welding heat input of 70 kJ/mm or more and 150 kJ/mm or less was applied. The amount of heat input is the average value of the amount of heat input over the entire welding length of the T-shaped joint shown in FIG.
The tee joint of FIG. 1 is made by ESW as follows. First, a diaphragm 2 made of a thick steel plate is arranged in a T-shape with a gap from a skin plate 1 made of a thick steel plate. Next, backing metals 3 and 4 are arranged along the diaphragm 2 so as to sandwich the gap from the longitudinal direction of the skin plate 1 . The backing metals 3, 4 surround the gap so that molten slag and molten metal during welding do not flow out of the weld. A welding wire is then fed into the molten slag bath within this gap. The welding wire is melted mainly by the resistance heat of the molten slag to form a welded metal portion 5, thereby producing a T-shaped joint.
A test piece 7 for a Charpy impact test was taken along the plate thickness center line of the diaphragm 2 at the welded portion of this T-shaped joint. Specifically, as shown in FIG. 1 , from the weld metal portion 5 , it passes through the welding heat affected zone (HAZ) 6 on the side of the skin plate 1 beyond the fusion line (FL) to the inside of the skin plate 1 . Test pieces 7 were collected from various sites. FIG. 1 shows the sampling position of a Charpy test piece in which the position of the notch is 1 mm from FL. In addition, although not shown, a Charpy test piece with a notch position FL was also collected. The skin plate 1 and the diaphragm 2 are made of the same steel type and have the same plate thickness.

The test piece 7 thus prepared is a V-notch test piece with a notch in the HAZ part 1 mm away from the melting line (FL), and a V-notch test piece with a notch on the FL, The test results using these are indicated as "FL+1 mm" and "FL" in Tables 5 and 6, respectively. Using each V-notch test piece, a Charpy impact test was performed at 0° C. and −20° C. in accordance with JIS Z 2242:2018. A Charpy impact test was performed using three V-notch test pieces for each notch position and one test temperature, and the average value (arithmetic mean) of absorbed energy under each condition was adopted as the evaluation result. Tables 5 and 6 show the plate thickness of the thick steel plate, the mechanical properties of the base material, the heat input in electroslag welding, and the HAZ toughness of the electroslag welded joint. KV ₂ (0° C.) and KV ₂ (−20° C.) are the absorbed energies at 0° C. and −20° C., respectively.

As shown in Table 5, the steel sheet of the present invention has a yield strength (YS) of 630 MPa or more and a yield ratio (YR) of 85% or less when the thickness is 50 mm or more and 100 mm or less. Furthermore, the ESW joint produced using the steel plate of the present invention has an excellent HAZ toughness of 70 J or more at 0°C. In addition, the ESW joint produced using the steel plate of the present invention has a very excellent HAZ toughness of 27 J or more even when the test temperature is -20°C.

On the other hand, as shown in Table 6, the chemical composition of the conventional steel plate (comparative steel) is out of the range of the present invention, so the mechanical properties of the base metal and the HAZ toughness of the ESW joint are inferior.

Code B1 has too low a C content, resulting in poor yield strength. Code B2 has too high a C content, resulting in poor HAZ toughness. Code B3 has an excessively low Mn content, resulting in poor yield strength. Code B4 has an excessively high Mn content, resulting in poor HAZ toughness. Code B5 is inferior in HAZ toughness because the amount of Ni is too low. Code B6 has a too low Cu content, and code B7 has a too high Cu content, resulting in poor HAZ toughness. Code B8 has too low Ti content, Code B9 has too much Ti content, Code B10 has too high N content, Code B11 has too low O content, and Code B12 has too low O content. HAZ toughness is poor because it is too high. B13 has an excessively high Si content, B14 has an excessively high P content, B15 has an excessively high S content, and B16 has an excessively high Al content, resulting in poor HAZ toughness.

Code B17 has too high CeqIIW and code B18 has too high CeqWES, resulting in poor HAZ toughness. Code B19 has too low CeqWES and Code B20 has too low CeqIIW, resulting in poor yield strength and HAZ toughness. Code B21 is inferior in HAZ toughness because Mn/Ni is too high.

Reference Signs List 1 Skin plate 2 Diaphragm 3, 4 Backing plate 5 Weld metal part 6 Weld heat affected zone (HAZ)
7 ... test piece

INDUSTRIAL APPLICABILITY The present invention is applied to thick steel plates manufactured in the steel industry, and can also be applied to steel products other than thick steel plates, such as shaped steel. The high-strength and thick steel plate to which the present invention is applied is mainly used as the steel frame of high-rise buildings, and is particularly suitable as the steel frame of a four-sided box column that is roughly composed of four skin plates and a diaphragm placed inside. be. In the joining of the members of the four-sided box column, so-called high heat input welding, in which the welding heat input is large, is performed. For example, high-efficiency large heat input welding such as electroslag welding and submerged arc welding is applied to diaphragm welding for attaching a diaphragm to a skin plate and corner welding for assembling skin plates, respectively. Moreover, the high-strength steel plate for large heat input welding according to the present invention can also be used for welded structures such as bridges, shipbuilding, tanks, offshore structures, and line pipes.

The steel plate according to the present invention is suitable for a high-strength, thick steel plate subjected to high heat input welding with high welding work efficiency, and when the required level of HAZ toughness is high. Specifically, the steel sheet according to the present invention has a yield strength of 630 MPa or more, a thickness of 50 mm or more and 100 mm or less, and an average value of Charpy absorbed energy (test temperature 0 ° C.) in the HAZ of the electroslag welded part of 100 J or more. It is a thick steel plate for high heat input welding. Therefore, the steel plate according to the present invention is suitable for high-strength thick steel plates that require the toughness of a large heat input welding HAZ, such as a building steel four-sided box column diaphragm to which a large heat input such as electroslag welding is applied. .

Claims (5)

in % by mass,
C: 0.030% or more and 0.080% or less,
Mn: 0.30% or more and 1.30% or less,
Ni: 1.30% or more and 7.00% or less,
Cu: 0.60% or more and 2.00% or less,
Ti: 0.005% or more and 0.020% or less,
O: 0.0010% or more and 0.0040% or less,
Cr: 0% or more and 1.0% or less,
Mo: 0% or more and 1.0% or less,
W: 0% or more and 1.0% or less,
Co: 0% or more and 1.0% or less,
Nb: 0% or more and 0.10% or less,
V: 0% or more and 0.10% or less,
B: 0% or more and 0.0050% or less,
Ca: 0% or more and 0.005% or less,
Mg: 0% or more and 0.005% or less,
REM: 0% or more and 0.005% or less,
Zr: containing 0% or more and 0.005% or less,
Si: 0.10% or less,
P: 0.010% or less,
S: 0.005% or less,
Al: 0.003% or less,
N: 0.0060% or less,
is limited to
The balance consists of Fe and impurities,
Mn/Ni, which is the ratio of the Mn content to the Ni content, is 0.80 or less;
Carbon equivalent CeqWES calculated by the following formula (1) is 0.45% or more and 0.70% or less,
A high-strength steel plate for large heat input welding, having a carbon equivalent CeqIIW calculated by the following formula (2) of 0.65% or more and 0.90% or less.
CeqWES (%) = C + Mn/6 + Si/24 + Ni/40 + Cr/5 + Mo/4 + V/14
... (1)
CeqIIW (%) = C + Mn/6 + Cu/15 + Ni/15 + Cr/5 + Mo/5 + V/5
... (2)
Here, C, Mn, Si, Ni, Cr, Mo, V, and Cu in the above formulas (1) and (2) are the contents in the steel sheet of each element represented by mass%, and are not contained 0 is substituted for the element term. The high-strength steel sheet for large heat input welding according to claim 1, wherein the hardenability multiple DI calculated by the following formula (3) is 10.0 inches or more and 21.0 inches or less.
DI (inch) = 0.5 x fB x ^C0.5 x (1 + 0.64 x Si) x (1 + 4.1 x Mn) x (1 + 0.27 x Cu) x (1 + 0.52 x Ni) x (1 + 2 .33×Cr)×(1+3.14×Mo)
... (3)
Here, C, Si, Mn, Si, Cu, Ni, Cr, and Mo in the above formula (3) are the contents in the steel sheet of each element expressed in mass%, and the elements not contained are Substitute 0. fB is 1.0 when B is 0.0004% or less, and 1.3 when B is greater than 0.0004%. Furthermore, in mass %,
Cr: 0.1% or more and 1.0% or less,
Mo: 0.1% or more and 1.0% or less,
W: 0.1% or more and 1.0% or less,
Co: 0.1% or more and 1.0% or less,
Nb: 0.005% or more and 0.10% or less,
V: 0.005% or more and 0.10% or less,
The high-strength steel sheet for large heat input welding according to claim 1 or 2, containing one or more of Furthermore, in mass %,
B: The high-strength steel sheet for large heat input welding according to any one of claims 1 to 3, containing 0% or more and 0.0004% or less. Furthermore, in mass %,
Ca: 0.0001% or more and 0.005% or less,
Mg: 0.0001% or more and 0.005% or less,
REM: 0.0001% or more and 0.005% or less,
Zr: 0.0001% or more and 0.005% or less,
The high-strength steel sheet for large heat input welding according to any one of claims 1 to 4, containing one or more of

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