TWI526545B - Steel material for welding - Google Patents

Description

Welding steel

The invention relates to a ship or a building. A steel material for welding of various steel structures in the field of civil engineering and the like, and a yield stress of 460 MPa or more, in particular, a steel material suitable for high heat input welding of a heat input amount exceeding 200 kJ/cm, in detail It relates to a steel material which has excellent weld toughness and joint strength even when the high heat input welding is performed.

Steel structures used in the fields of ships, marine structures, construction, and steel pipes are generally finished into a structure of a desired shape by fusion bonding. Therefore, from the viewpoint of ensuring safety, in these structures, in addition to ensuring the properties of the base material of the steel used, that is, the strength. In addition to toughness, the toughness of the welded portion is also required to be excellent.

In recent years, steel structures such as ships have become larger and larger, and the steel materials used have been actively promoted to increase strength and thickness. Along with this, in the welding construction, a high-efficiency and high-heat input welding method such as submerged arc welding, electro-gas welding, and electroslag welding is applied, but even by In the case where the high heat input welding is performed by welding, a steel material having excellent toughness of the welded portion is also required.

However, with regard to high-strength steel or thick-walled steel sheets, it is difficult to simultaneously realize the mechanical properties of the base material (especially low-temperature toughness) and the reports of the low-temperature toughness of the heat-affected zone (heat-affected zone, Heat Affected Zone; HAZ below). .

In the report, as disclosed in, for example, Patent Document 1 and Patent Document 2, it is disclosed that the low temperature toughness of the base material and the low temperature toughness of the HAZ are simultaneously achieved by controlling rolling or controlling cooling.

Next, the HAZ structure at the time of performing high heat input welding will be described. The portion of the HAZ that is in contact with the fused metal is generally referred to as a "bond portion." The HAZ in the vicinity of the adhesive portion is particularly exposed to a high temperature in the vicinity of the melting point in the heat-affected zone, and thus the crystal grain tends to coarsen and the toughness remarkably decreases. On the other hand, at a position slightly spaced from the bonding portion, since the crystal grains are fine-grained regions, a softened region is formed, which is a major factor for lowering the joint strength.

As described above, the toughness of the HAZ is lowered in the high heat input welding, and various countermeasures have been studied so far for the reduction of the HAZ toughness. For example, the following technique has been put into practical use in which TiN is finely dispersed in steel to suppress coarsening of austenite particles or as a ferrite iron core. Further, a technique has been developed in which the effect of suppressing the coarsening of the same Worstian iron particles as described above is achieved by dispersing the oxide of Ti.

However, in the above technique for effectively utilizing TiN, when the high heat input is welded, since the heat affected portion is heated to the melting temperature region of TiN, there is a problem that TiN is decomposed and the dispersion effect is lost, or cause Solid solution Ti and solid solution N formed by decomposition of TiN, and the bottom structure of steel is embrittled, or the heat affected part of fusion The toughness is significantly reduced.

Further, in the technique of effectively utilizing the Ti oxide, there is a problem that it is difficult to uniformly and finely disperse the oxide. As a technique for solving the above problem, for example, Patent Document 3 discloses a technique for controlling the toughness of a fusion heat affected portion in which high heat input welding of more than 200 kJ/cm is performed to control the form of sulfide. The addition amount is appropriately adjusted to crystallize CaS, and the CaS is effectively utilized as a ferrite iron metamorphic nucleus.

Since the CaS is crystallized at a temperature lower than that of the oxide, it can be finely dispersed in the steel, and when the steel sheet is cooled, the CaS is used as a core, and the MnS, TiN, BN, etc. Since it is dispersed, the structure of the heat-affected portion can be made into a fine ferrite-pearlite structure, and high toughness can be achieved. Therefore, according to the technique of Patent Document 3, the HAZ toughness reduction accompanying the high heat input welding can be suppressed to some extent.

In addition, it can be seen from the subsequent studies that in the case where the steel sheet has a high-strength stress of 460 MPa or more and a relatively large amount of C or an alloy element is added, the fusion heat input amount exceeds 200 kJ/cm. When the high heat input is welded, the HAZ in the vicinity of the bonding portion forms a hard volume embrittlement called a martensite (hereinafter also referred to as MA in the present invention), which obstructs the welded portion. The further improvement of resilience.

That is, it was found that in the improvement of the HAZ toughness in the vicinity of the bonding portion in the high heat input welded portion of the high-strength steel, in addition to the suppression of coarsening of the iron grain in the Vostian or the fine dispersion of the ferrite and the nucleus, the reduction of the solid solution N is required. In addition, it is necessary to suppress the island-like Ma Tiansan. Iron generation.

Regarding the technique of reducing the island-shaped escaping iron in the HAZ portion, for example, Patent Document 4 discloses that in addition to lowering the contents of C and Si, the reduction in the content of P is also effective.

Further, in Patent Document 5, by actively adding Mn and reducing P as much as possible, the island-like granulated iron of the HAZ in the vicinity of the bonded portion is lowered, and a steel material having an excellent toughness and a stress of 460 MPa is obtained.

On the other hand, regarding the technique of suppressing HAZ softening accompanying high heat input welding, HAZ toughness countermeasures and the like have not been revealed too much. In any of Patent Document 3, Patent Document 4, and Patent Document 5, there is no description about HAZ softening. This is considered to be because the design of the steel for high heat input welding is based on the premise that the strength of the joint can be ensured.

Therefore, the technique disclosed for the suppression of HAZ softening will be described.

Among these techniques, there are techniques in which a strengthening element such as Nb or V is precipitated, and a technique in which the effect of improving the hardenability of B is utilized.

For example, in Patent Document 6, the amount of C is increased and Si and Mn are lowered to contain Nb or V, thereby reducing HAZ softening.

On the other hand, in Patent Document 7, in order to improve the hardenability of B, a component formula is defined as follows, that is, a large amount of Ti, B, and Nb is contained with respect to the amount of N, thereby suppressing HAZ softening.

Further, in Patent Document 8, by defining the amount of solid solution B, the hardenability of B is improved, and the HAZ softening is suppressed.

[Prior Art Literature] [Patent Literature]

[Patent Document 1] Japanese Patent Laid-Open Publication No. SHO 57-134518

[Patent Document 2] Japanese Patent Laid-Open No. 59-83722

[Patent Document 3] Japanese Patent No. 3546308

[Patent Document 4] Japanese Patent Laid-Open Publication No. 2008-163446

[Patent Document 5] Japanese Patent Laid-Open Publication No. 2011-6772

[Patent Document 6] Japanese Patent Laid-Open No. 60-67622

[Patent Document 7] Japanese Patent Laid-Open Publication No. 2007-177327

[Patent Document 8] Japanese Patent No. 4233033

However, as described above, the technique described in Patent Document 3 is a technique for improving the toughness of the bonded portion when the steel having a creep stress of 390 MPa is subjected to high heat input welding, but the following may not be sufficiently satisfied. That is, the high-heat input HAZ toughness and HAZ softening of the steel material having a relief stress of 460 MPa class are higher than the case where the lodging strength is higher than the above.

Further, in the technique described in Patent Document 4, the steel material having a relief stress of 460 MPa is used, and the content of C, Si, and P is lowered to reduce the island-like granulated iron of the HAZ in the vicinity of the bonded portion, and an appropriate amount is added. Ca is finely dispersed in the ferrite iron metamorphic core to ensure HAZ toughness. However, HAZ softening is not described, and Ni needs to be added, so that there is a possibility that the alloy cost is increased.

Furthermore, in the technique described in the patent document 5, the steel material having a relief stress of 460 MPa is used, and it is possible to reduce the island-shaped granulated iron by actively using Mn, thereby obtaining the required steel material at low cost, but Patent Document 5 and Patent Document 4 also does not describe HAZ softening in the same manner.

On the other hand, in the technique described in Patent Document 6, the amount of C is high, and the strengthening element is precipitated by Nb or V to sufficiently cope with HAZ softening. However, when high heat input is welded, a large number of island-shaped 麻田 is formed in the HAZ near the bonding portion. As a result of the loose iron, it is feared that the toughness of the HAZ in the vicinity of the bonded portion is remarkably lowered.

Further, the techniques described in Patent Document 7 and Patent Document 8 are techniques for suppressing HAZ softening by using the hardenability of B. Patent Document 7 is premised on the addition of a large amount of Ti, B, and N, and has problems in manufacturability. In the region where TiN is melted in the vicinity of the bonded portion, there is concern that the toughness of the HAZ is lowered due to solid solution N.

Further, the technique described in Patent Document 8 is based on the premise that Nb is not present, and in the case of a steel material having a relief stress of 460 MPa, there is still a problem that it is difficult to secure the joint strength.

The present invention has been made in view of the above-described state of the art, and an object of the present invention is to provide a steel material for high heat input welding at a low cost, and to perform high heat input welding in which the heat input amount of welding exceeds 200 kJ/cm, and the hardness of the heat affected portion of the welded portion is not lowered. The HAZ toughness near the property and the adhesive portion is also excellent, and the stress is 460 MPa or more.

In order to solve the above problem, the inventors have examined in detail the influence of the tissue factor on the following, that is, the high-strength steel having a relief stress of 460 MPa or more. When the material is subjected to high heat input welding in which the heat input amount exceeds 200 kJ/cm, the HAZ toughness in the vicinity of the bonded portion and the hardness in the HAZ softened portion region are obtained. As a result, it was found that, with regard to the HAZ toughness in the vicinity of the bonded portion, although a small amount of the existing island-like ramification iron has an adverse effect on the toughness, the hardness of the softened portion is improved by the formation of the island-shaped granulated iron. .

Therefore, the inventors of the present invention have studied the countermeasures for increasing the amount of generation of the island-shaped kenian loose iron in the softened portion region after suppressing the generation of the island-shaped japan loose iron in the HAZ in the vicinity of the bonded portion. As a result, it is understood that the amount of C, Si, and P is low in the HAZ in the vicinity of the bonding portion, and the Mn is actively contained in order to compensate for the decrease in the strength of the base material which is worried about the decrease in the amount of C. The HAZ toughness in the vicinity of the bonded portion causes the island-shaped numb iron to be adversely affected, thereby effectively increasing the strength of the base material.

Further, it has been found that in the softened portion region, by controlling Ti, N, and B in an appropriate range, the effect of improving the hardenability of B is effectively utilized, thereby not increasing the island-like granulated iron of the HAZ in the vicinity of the bonded portion, which can be promoted. The formation of island-shaped granulated iron in the softest part region.

That is, in the case of B, the HAZ in the vicinity of the bonding portion exposed to the high temperature in the vicinity of the melting point does not cause the formation of the upper bunite or the movement of the grain boundary accompanying the deposition, and does not increase the change. The quenching property of the undeformed Worth iron remaining between the bainite-lath, and on the other hand, in the HAZ softening region where the temperature rise caused by the heat influence is relatively small, the B is accompanied by the ferrite iron metamorphosis. Diffusion, segregation at the grain boundary of the untransformed Worth iron, thereby increasing the hardenability of the B, thereby having Promote the effect of the formation of scattered iron in island-like kenes.

However, the temperature rise caused by the heat influence in the HAZ softening region is relatively small, so that the precipitation of the precipitate is hardly caused, and the amount of the B which contributes to the hardenability is dependent on the state at the time of the production step. Further, in each stage of controlling the rolling and cooling of the base material production step, B may form a nitride depending on the production conditions. In this case, the effect of improving the hardenability cannot be exhibited.

Therefore, as a result of further research by the inventors, it has been found that, in the steel sheet manufacturing step, rolling is first performed in the recrystallization temperature region of the Worthite iron, and then accelerated cooling is performed until the Worstian iron is not recrystallized, and then Rolling is performed in the non-recrystallization temperature region of the Worthfield iron, and then accelerated cooling is performed again, thereby suppressing the precipitation of the B nitride as much as possible, and obtaining excellent HAZ characteristics by combining with the optimization of the components. Thus, the present invention has been developed.

That is, the gist of the present invention is as follows.

1. A steel material for welding, containing C: 0.030% to 0.080%, Si: 0.01% to 0.10%, Mn: 1.80% to 2.40%, P: 0.010% or less, and S: 0.0005% to 0.0040% by mass%. , Al: 0.005% to 0.100%, Nb: 0.003% to 0.030%, Ti: 0.010% to 0.050%, N: 0.0030% to 0.0120%, and B: 0.0005% to 0.0025%, and then the mass ratio of Ti to N ( Ti/N) is 2.0 or more and less than 4.0, and the A value defined by the following formula (1) is in the range of 3 or more and 25 or less, and the C _eq defined by the following formula (2) is in the range of 0.38 to 0.43, and the remainder a component containing Fe and an unavoidable impurity, a stress of 460 MPa or more, a solid solution B of 5 mass ppm or more, and a heat-affecting zone when heat input is performed at a heat input amount of 200 kJ/cm or more. In the structure in the vicinity of the adhesive portion, the island-shaped kenaf loose iron is 1 vol% or less, and the island-shaped masita loose iron in the structure of the most softened portion in the heat-affected zone is 5 vol% or more: A = 2256 × Ti-7716 ×N+10000×B...(1)

C _eq =C+Mn/6+(Cr+Mo+V)/5+(Cu+Ni)/15...(2)

Here, each element symbol indicates the content (% by mass) of each element in steel.

2. The steel material for welding according to 1, wherein

Further, the component composition contains one or more selected from the group consisting of V: 0.20% or less, Cu: 0.30% or less, Ni: 0.30% or less, Cr: 0.40% or less, and Mo: 0.40% or less.

3. The steel material for welding according to 1 or 2, wherein

Further, the component composition is selected from the group consisting of Ca: 0.0005% to 0.0050%, Mg: 0.0005% to 0.0050%, Zr: 0.0010% to 0.0200%, and rare earth metal (RM): 0.0010%. One or more of ~0.0200%.

According to the present invention, when the high heat input welding is performed, a steel material having both good joint strength and toughness of the heat affected portion can be obtained, and therefore, it is advantageous to improve the construction by high heat input welding such as submerged arc welding or electroslag welding. Ship or large structure The quality of the object. In particular, when the present invention is applied to a steel material having a thickness of more than 50 mm, it is more remarkable in terms of the joint strength of the welded joint and the toughness of the welded heat-affected portion at the same time as compared with the steel material of the prior art.

Hereinafter, the present invention will be specifically described. Further, the steel material to be used in the present invention refers to a steel material produced by hot rolling.

In the present invention, it is important that the composition of the steel material, the strength, and the minimum hardness in the softened region of the heat-affected portion of the welded portion formed by welding with a high heat of more than 200 kJ/cm (hereinafter also referred to as the HAZ softening region) The hardness is controlled.

First, the volume fraction of the island-like granulated iron which is a heat-affected zone which is a characteristic of the steel material of this invention is demonstrated.

The island-like numb loose iron in the structure near the adhesive portion in the heat-affected zone is 1 vol% or less

In the heat-affected zone (HAZ), it is possible to suppress the formation of island-like escaping iron in the vicinity of the adhesion portion in the heat-affected zone where the Worthite iron is coarsened at a high temperature, thereby improving the high-heat input welding portion. toughness. In order to obtain the above effect, it is necessary to suppress the volume fraction of the island-like stalk iron in the vicinity of the bonded portion to 1 vol% or less. Further, the lower limit of the volume fraction of the island-like japan loose iron is not particularly limited, and may be 0 vol%. Further, in the present invention, the vicinity of the adhesion portion in the heat-affected portion means a fusion heat-affected portion within a range of 600 μm from the adhesion portion, and the structure is as follows The known tissue, that is, in addition to the island-like granulated iron, is also mainly composed of acicular ferrite iron or toughened iron, and contains ferrite iron or ferrite.

The island-shaped masita loose iron in the softest part of the heat-affected zone is 5 vol% or more

In the joint obtained by welding a steel material having a relief stress of 460 MPa or more, the tensile strength equivalent to that of the base material is required, that is, the tensile strength is 570 MPa or more. Here, as a factor affecting the tensile strength of the joint, there are mainly the strength or thickness of the welded metal, the hardness of the HAZ softening portion region, and the like, and the influence of the structure of the softened portion in the heat affected portion is particularly large. Further, the structure of the softened region in the steel material having the relief stress of 460 MPa or more is the ferrite iron and the second phase structure, and as the second phase structure, the island-shaped kenada loose iron having a volume fraction of 5 vol% or more is produced. Obtain the required joint strength.

In the present invention, the softened region in the heat-affected zone refers to a heat-affected zone in which the Worthite iron is finely divided by heating after welding by about 10 mm from the bonded portion.

In the present invention, the softened portion region in the heat-affected zone is a region in which the Vickers hardness HV is measured in a lattice shape at equal intervals of about 1 mm (Japanese Industrial Standards (JIS) Z). 2244 (1998)), which is formed by connecting the four measurement points closest to the center, centering on the point indicating the lowest hardness.

In the present invention, the structure of the softened portion region of the HAZ is controlled as described above, and in order to achieve high strength, the composition of the steel material is defined as follows. In addition, the following % related to the composition of the steel is indicative of the amount%.

C: 0.030%~0.080%

C is an element for increasing the strength of the steel material, and it is necessary to contain 0.030% or more in order to secure the strength required for the structural steel. On the other hand, when C exceeds 0.080%, MA of HAZ in the vicinity of the adhesive portion is likely to be formed, so the upper limit is made 0.080%.

Si: 0.01%~0.10%

Si is an element added as an oxygen scavenger when the steel is melted, and needs to be added in an amount of 0.01% or more. On the other hand, when it exceeds 0.10%, in addition to the toughness of the base material, the formation of MA in the HAZ in the vicinity of the bonded portion welded by the high heat input tends to lower the toughness. Thus, Si is set in the range of 0.01% to 0.10%.

Mn: 1.80% to 2.40%

Similarly to C, Mn is an element which increases strength, and is cheaper than alloying elements such as Mo or V, and does not promote MA formation in the HAZ in the vicinity of the bonded portion. Therefore, Mn can be actively added in the present invention. Further, in order to secure the required strength and obtain the above effect, it is necessary to add 1.80% or more, more preferably 1.90% or more, and further preferably 2.00% or more. On the other hand, if it is contained excessively, the toughness of the welded portion is broken, so that it is required to be 2.40% or less, more preferably 2.20% or less, still more preferably 2.10% or less.

P: 0.010% or less

P is one of the elements contained as an impurity, and since the toughness of the steel sheet base material and the HAZ is lowered, it is preferable to reduce the content in the range as much as possible in consideration of the economical efficiency in melting the raw material. Therefore, the amount of P is limited to 0.010% or less. It is preferably 0.008% or less.

S: 0.0005%~0.0040%

S is an element required to form MnS or CaS which functions as a nucleation site of the ferrite iron. Therefore, 0.0005% or more is added. However, excessive addition causes a decrease in the toughness of the base material, and the upper limit is made 0.0040%.

Al: 0.005%~0.100%

Al is an element added for deoxidation of steel and needs to be contained in an amount of 0.005% or more. On the other hand, when the content exceeds 0.100%, not only the toughness of the base material but also the toughness of the weld metal is lowered. Thus, Al is set in the range of 0.005% to 0.100%. It is preferably in the range of 0.010% to 0.100%.

Nb: 0.003%~0.030%

Nb is an element effective for securing the strength of the base material and the hardness of the HAZ softening portion and further the strength of the welded joint. However, when the addition is less than 0.003%, the effect is small. On the other hand, when the content exceeds 0.030%, MA is formed in the HAZ in the vicinity of the bonded portion to lower the toughness. Thus, Nb is set in the range of 0.003% to 0.030%.

Ti: 0.010%~0.050%

Ti precipitates as TiN during solidification, and coarsens the Worthfield iron particles of the HAZ in the vicinity of the bonded portion. Moreover, Ti becomes an abnormal core of the ferrite iron, which contributes to the high toughness of the HAZ, and at the same time, reduces the N which may be bonded to the B, and ensures the solid solution B, thereby ensuring the hardness of the HAZ softening portion, Further, the strength of the welded joint is effective. In order to obtain the above effect, it is necessary to add 0.010% or more, preferably 0.015% or more. On the other hand, when the content exceeds 0.050%, the precipitated TiN is coarsened, and the above effect cannot be obtained. Thereby, Ti is set in the range of 0.010% to 0.050%.

N: 0.0030%~0.0120%

N forms TiN during solidification, which contributes to suppression of coarsening of Worthfield iron particles of HAZ in the vicinity of the adhesive portion, and at the same time, BN is produced, and this BN acts as a ferrite iron metamorphic nucleus, thereby making the bonding portion The microstructure of the nearby HAZ is fine, which contributes to the high toughness of the steel. Further, in order to secure the necessary amount of the TiN, it is necessary to contain 0.0030% or more of N, preferably 0.0050% or more. More preferably, it is 0.0070% or more. On the other hand, if it is excessively contained, the amount of solid solution N increases in the region where TiN is melted due to the fusion heat input condition, and the toughness of the HAZ is lowered. Therefore, the upper limit is made 0.0120% or less. It is preferably 0.0100% or less.

B: 0.0005%~0.0025%

B is an element which improves the hardenability of steel, and lowers the metamorphic temperature of the Worthite iron, thereby promoting the formation of a hard structure such as toughened iron or granulated iron, thereby contributing to the increase in strength of the base material steel sheet. Similarly, the formation of the ferrite iron as the soft phase is suppressed in the HAZ softening portion, and the strength of the HAZ softened portion is increased. In order to obtain the above effect, it is necessary to contain B or more of 0.0005%. On the other hand, when the content of B exceeds 0.0025%, the hardenability is too high, and the toughness of the base material steel sheet and the HAZ is lowered. Therefore, B is set in the range of 0.0005% to 0.0025%.

The amount of solid solution B is 5 mass ppm or more

In the present invention, the amount of solid solution B in the steel material is set to 5 ppm by mass or more. When the amount of solid solution B in the steel material is less than 5 ppm by mass, the effect of improving the hardenability of the untransformed Worthite iron during the formation of the HAZ softened region is insufficient, so that the island-like Ma Tiansan which is used to obtain the desired hardness cannot be obtained. The amount of iron.

Mass to mass ratio of Ti to N (Ti/N): 2.0 or more and less than 4.0

In the present invention, Ti/N is an important requirement together with the specification of the A value described later. Ti/N has a large influence on the fine dispersion state of TiN and the toughness deterioration by solid solution N in the adhesion portion of the HAZ, and thus needs to be appropriately controlled. In other words, when Ti/N is 4.0 or more, BN is not precipitated, and boron carbides of Ti or the like are precipitated, whereby HAZ toughness is largely lowered. On the other hand, when it is less than 2.0, HAZ toughness due to solid solution N is lowered. The BN in the HAZ precipitates, and the hardenability of B cannot be ensured, so that it is difficult to secure the desired HAZ softening portion hardness. Therefore, the value of Ti/N is set to 2.0 or more and less than 4.0. It is preferably in the range of 2.5 or more and 3.5 or less.

A value: 3 or more and 25 or less

The A value defined by the formula (1) shown below is one of the most important items in the present invention. When the steel material receives the heat history of the heat-affected zone corresponding to the high heat input welding, even when the formation reaction such as TiN or BN is not carried out according to the equilibrium theory, the effect of improving the hardenability by the solid solution B can be exhibited. Ti, N, and B satisfy the addition amount of the steel material, and the A value needs to be 3 or more. However, when the A value exceeds 25, the hardenability of the steel material becomes excessive, which adversely affects the toughness of the HAZ. Therefore, in the present invention, the A value is set to 3 or more and 25 or less. It is preferably in the range of 6 to 15.

A=2256×Ti-7716×N+10000×B...(1)

Among them, each element symbol (Ti, N, B) indicates the content of each element in steel (quality the amount%).

C _eq :0.38~0.43

The steel material for high heat input welding of the present invention is ineffective in heat transfer at the time of welding, and the effects of the tissue control such as the thermo mechanical control process (TMCP) performed at the time of production of the base material are all invalid. Therefore, in the heating and cooling at the time of welding, it is necessary to simultaneously achieve the strength and toughness of the welded joint. Therefore, it is necessary to control the carbon equivalent C _eq as an index of hardenability to an appropriate range.

Specifically, it is necessary to control the composition of each component so that the carbon equivalent C _eq defined by the following formula (2) is in the range of 0.38 to 0.43. When the C _{eq is} less than 0.38, the hardenability is insufficient, and the hardness of the softened portion is remarkably lowered, so that the strength of the desired welded joint cannot be ensured. On the other hand, when C _eq exceeds 0.43, the hardenability is excessive, and the formation of the ferrite iron in the vicinity of the bonded portion is suppressed, and the formation of the island-shaped granulated iron is promoted, so that sufficient toughness cannot be ensured. Preferably, C _eq is in the range of 0.39 to 0.42.

C _eq =C+Mn/6+(Cr+Mo+V)/5+(Cu+Ni)/15...(2)

Here, each element symbol in the formula represents the content (mass%) of each element (C, Mn, Cr, Mo, V, Cu, Ni).

The above is the basic component composition of the present invention, and the remainder is Fe and unavoidable impurities. Further, as an unavoidable impurity, for example, O is allowed to be 0.0050% or less.

In addition to the above components, the steel material of the present invention may further increase strength and the like. One or more selected from the group consisting of V, Cu, Ni, Cr, and Mo are included as the selected elements in the following ranges.

V: 0.20% or less, Cu: 0.30% or less, Ni: 0.30% or less, Cr: 0.40% or less, and Mo: 0.40% or less

V, Cu, Ni, Cr, and Mo are elements effective for high strength of the base material. In order to obtain this effect, it is preferable to add 0.05% or more of V, Cu, and Ni, and to add 0.02% or more of Cr and Mo. However, if a large amount of any element is added, the toughness is adversely affected, and Ni also causes an increase in the alloy cost. Therefore, when it is contained, it is preferable that V is 0.20% or less and Cu is set to 0.30% or less. Ni is set to 0.30% or less, and Cr and Mo are set to 0.40% or less.

Furthermore, the steel material of the present invention may contain one or more selected from the group consisting of Ca, Mg, Zr and REM as a selected element in the following range.

Ca: 0.0005%~0.0050%

Ca may be contained in order to obtain the effect of improving the toughness of S or the dispersion of oxides and sulfides. In order to obtain the effect, it is preferably at least 0.0005%. However, even if the addition exceeds 0.0050%, the effect is saturated. Therefore, when Ca is contained, it is preferably in the range of 0.0005% to 0.0050%.

Mg: 0.0005%~0.0050%, Zr: 0.0010%~0.0200%, REM: 0.0010%~0.0200%

Mg, Zr, and REM are all elements having an effect of improving the toughness by dispersion of an oxide. In order to exhibit the effect, it is preferred to contain 0.0005% or more of Mg, and Contains 0.0010% or more of Zr and REM. On the other hand, even if Mg is added in excess of 0.0050%, the addition of Zr and REM exceeds 0.0200%, and the effect is saturated. Therefore, in the case where the element is contained, it is preferable to set it as the above range.

Production method

It is preferable to melt a steel having the above-described composition by a usual welding method such as a converter or an electric furnace, and to form a billet raw material for steel sheet production by a usual procedure such as a continuous casting method or an agglomeration method. Hereinafter, the manufacturing conditions of the steel sheet to be preferably applied to the present invention will be described.

Heating temperature: 1050 ° C ~ 1200 ° C

In order to completely dissolve the Nb carbonitride in the steel material, it is preferred to set the heating temperature of the steel material to 1050 ° C or higher. On the other hand, when the heating temperature exceeds 1200 ° C, the particle size of the Worstian iron is coarsened during heating and adversely affects the toughness of the base material. Therefore, the upper limit is preferably 1200 ° C.

Rolling of the recrystallization temperature zone of the Worthite iron

The rolling of the Worthite iron recrystallization temperature region has an effect of refining the Worthfield iron particles to a certain degree in the heating, and is preferably carried out at a minimum of one pass or more, preferably in a cumulative rolling. The rate is 20% or more. In the case of the steel of the component range, the lower limit temperature of the re-crystallization temperature region of the Worthite iron is approximately in the range of 900 ° C to 1000 ° C.

Primary cooling from the recrystallization temperature zone of the Worthite iron to the unrecrystallized temperature zone of the Worthite iron

This step is one of the most important items in the manufacturing step. As described in HAZ The amount of solid solution B which can improve the hardenability of the structure in the softened region corresponds to the amount of solid solution B which is secured in the state in which the steel sheet is produced.

Therefore, when a large amount of B nitride is precipitated in the production of a steel sheet, there is a case where the amount of solid solution B for ensuring hardenability is insufficient, and sufficient hardness cannot be obtained in the HAZ softened region.

Further, it is desirable to accelerate the cooling rate of the Worstian iron recrystallization temperature region to the Worthite iron non-recrystallization temperature region as much as possible in the temperature region corresponding to the B nitride formation during the cooling process in the production of the steel sheet. Usually, this step is air-cooled as the temperature reduction standby time of hot rolling, but in the present invention, the time until the control rolling step as the next step is shortened by performing accelerated cooling having a cooling rate larger than air cooling, and It is possible to prevent a decrease in solid solution B caused by precipitation of B nitride. In addition, the accelerated cooling is particularly effective in the temperature range of 1000 ° C to 600 ° C.

In the present invention, in order to distinguish the cooling after rolling in the non-recrystallization temperature region of the Worthite iron to be described later, the accelerated cooling performed after the rolling in the re-crystallization temperature region of the Worthite is referred to as primary cooling. In the primary cooling, it is preferable to achieve a cooling rate larger than that of air cooling by an accelerated cooling device using water cooling or a so-called descaling device that removes rust generated on the surface of the steel sheet during rolling. Specifically, it is preferably a cooling rate of 3 ° C /sec or more.

Rolling of the cumulative rolling reduction rate of the Worthite iron in the non-recrystallization temperature region of 40% or more

After the accelerated cooling, control is carried out in the area where the Vostian iron is not recrystallized. Rolling. When the cumulative rolling reduction ratio in the rolling is controlled to be small, it is difficult to obtain a predetermined base material toughness. Therefore, the lower limit of the cumulative rolling reduction ratio is set to 40%. The higher the cumulative rolling reduction ratio, the more desirable, but industrially there is an upper limit of about 80%, and thus it is preferably 50% to 80%.

After rolling in the non-recrystallization temperature zone, the Worthite iron is re-cooled at a temperature above the Ar ₃ metamorphic point to a temperature below 550 ° C.

The secondary cooling is for the cooling of the Worthite iron structure processed by controlling the rolling. Further, in order to complete the phase transformation state of the steel structure and to cool to a temperature region of 550 ° C or lower, the lower limit of the cooling end temperature is preferably 550 ° C. The cooling rate in the secondary cooling requires a cooling rate greater than that of the air cooling, and is preferably a strong cooling of 5 ° C/sec or more. Further, it is preferably a strong cooling of 10 ° C /sec or more. The cooling method is not particularly limited, but it is desirable to use water-cooled cooling.

Here, the steel material temperature of the present invention represents the average temperature of the surface temperature of the steel material and the temperature of the center portion of the thickness. Since the Ar ₃ metamorphic point differs depending on the composition of the steel material, it can be easily obtained by the following formula. In the following formula, each element symbol indicates the content (% by mass) of each element in steel. Set the case that is not included to 0.

Ar ₃ (°C)=910-273C-74Mn-56Ni-16Cr-9Mo-5Cu

[Examples]

After the steel having the composition shown in Table 1 was melted in a converter, a slab was formed by a continuous casting method, and controlled by the rolling and controlling cooling conditions shown in Table 2 A steel plate with a thickness of 40 mm to 80 mm is produced. The branch numbers shown in Table 2 indicate that the steel components are the same and the manufacturing conditions are different. Further, primary cooling was performed by a water-cooling apparatus provided on the outlet side of the rolling mill, and it was confirmed that the average cooling rate during cooling was 3 ° C/sec or more.

A tensile test piece having a parallel portion of 14 mm Φ was taken from the position of 1/4 of the thickness direction in the thickness of the steel plate produced by the manufacturing process, and the tensile test was carried out in accordance with JIS Z 2241 (1998). 0.2% endurance (YS) and tensile strength (TS).

Further, according to JIS Z 2202 (1998), a Charpy impact test piece of a V-notch standard size is taken from a position of 1/4 of the thickness direction, and an impact test is performed in accordance with JIS Z 2242 (1998) to obtain a fracture surface. Fracture surface transition temperature (vTrs).

Here, the target value of vTrs is set to -60 ° C or lower.

Further, in order to evaluate the hardness of the softened portion in the heat-affected zone when the heat input amount of the welding heat input amount is 200 kJ/cm or more, a small test of 3 mm Φ × 10 mm is taken from the thickness direction 1/4 position. The sheet was heat-treated at 900 ° C after heating to a temperature immediately above the transformation point, and then cooled at 800 ° C to 500 ° C for 390 seconds. The Vickers hardness HV (JIS Z 2244 (1998)) of the small test piece subjected to the above treatment was measured in a lattice shape at intervals of about 1 mm, and the lowest hardness was defined as the softening portion hardness. The target value of the softening portion hardness is set to 160 or more. In addition, the HAZ softening portion region is a region in which the measurement points closest to the point are connected to each other around the point at which the lowest hardness is displayed.

Further, a portion corresponding to the HAZ softening portion region is etched by a nitric acid etching solution (Nital) to exhibit a structure. Scanning Electron Microscope (SEM) to take 3 shots at 1000 times The photograph of the wild tissues was subjected to image analysis of the photographs, and the average area fraction of MA was determined, and the average area fraction was defined as the MA volume fraction (vol%) of the HAZ softening portion region.

In order to evaluate the toughness of the vicinity of the adhesion portion in the heat-affected zone when the heat input of the welding heat input amount is 200 kJ/cm or more, the width of the thick steel plate is taken: 80 mm × length: 80 mm × thickness : 15 mm test piece, after heating to 1450 ° C, cooled between 800 ° C and 500 ° C for 390 seconds, and then taking a 2 mm V notched Charpy test piece, and performing the Charpy impact test temperature test in the same manner as described above. Set to -40 ° C and evaluate by the average of 3 trials. The target value is -40. The average absorbed energy (vE - ₄₀ ° C) at ° C is 50 J or more. Further, in the same manner as described above, the area fraction of the MA of the test piece profile after the heat history was evaluated.

Table 3 shows the measurement results of the base material characteristics, the HAZ characteristics, and the MA volume fraction (vol%) in the HAZ evaluated in the order described.

According to this table, in the example of the sub-number A of the steel sheet composition No. 1 to No. 12, excellent characteristics were obtained in the base material and the HAZ. On the other hand, in the steel sheet of the sub-number B of the steel sheet compositions No. 1 to No. 4, the requirements of the present invention are not satisfied by the influence of the production conditions, and the base material characteristics and the HAZ characteristics are deteriorated. Further, in the steel sheet compositions No. 13 to No. 27, since the chemical composition is outside the range defined by the present invention, even if the sub-number A is used, the HAZ characteristics are deteriorated.

Claims (3)

A steel material for welding, containing C: 0.030% to 0.080%, Si: 0.01% to 0.10%, Mn: 1.80% to 2.40%, P: 0.010% or less, S: 0.0005% to 0.0040%, and Al by mass% : 0.005%~0.100%, Nb: 0.003%~0.030%, Ti: 0.010%~0.050%, N: 0.0030%~0.0120%, and B: 0.0005%~0.0025%, and then the mass% ratio of Ti to N (Ti/ N) is 2.0 or more and less than 4.0, and the A value defined by the following formula (1) is in the range of 3 or more and 9.8 or less, and the C _eq defined by the following formula (2) is in the range of 0.38 to 0.43, and the remainder includes The component composition of Fe and unavoidable impurities, the undulation stress is 460 MPa or more, and the amount of solid solution B is 5 ppm by mass or more, and in the heat-affected zone when the heat input amount of the fusion heat input is 200 kJ/cm or more The island-like numb loose iron in the structure in the vicinity of the adhesive portion is 1 vol% or less, and the island-shaped masita loose iron in the structure of the most softened portion in the heat-affected zone is 5 vol% or more: A = 2256 × Ti - 7716 × N +10000×B...(1) C _eq =C+Mn/6+(Cr+Mo+V)/5+(Cu+Ni)/15...(2) where each element symbol indicates each element Content in steel (% by mass). The steel material for welding according to the first aspect of the invention, wherein the component composition further contains, in mass%, V: 0.20% or less, Cu: 0.30% or less, Ni: 0.20% or less, and Cr: 0.40. Below % and Mo: 0.40% One or more of the following. The steel material for welding according to the first or second aspect of the invention, wherein the component composition further contains, in mass%, Ca: 0.0005% to 0.0050%, Mg: 0.0005% to 0.0050%, Zr. : 0.0010% to 0.0200%, and rare earth metals: one or more of 0.0010% to 0.0200%.