KR20100107412A - Steel having excellent toughness in welding heat affected zone - Google Patents

Abstract

PURPOSE: A steel material with a weld heat-affected zone of superior toughness is provided to prevent the blockage of a nozzle when used as a casting material. CONSTITUTION: A steel material with a weld heat-affected zone of superior toughness comprises C 0.02~0.15 weight%, Si 0.5 weight% or less, Mn 2.5 weight% or less, P 0.03weight% or less, S 0.02 weight% or less, Al 0.050 weight% or less, N 0.01 weight% or less, T 0.005~0.10 weight%, Zr 0.0003~0.050 weight%, REM 0.0003~0.015 weight%, Ca 0.0003~0.010 weight%, and the rest Fe and inevitable impurities.

Description

STEEL HAVING EXCELLENT TOUGHNESS IN WELDING HEAT AFFECTED ZONE}

This invention is steel used for bridges, high-rise buildings, ships, etc., The steel material excellent in the toughness of the welding heat-affected part (henceforth simply called "HAZ") at the time of large heat welding. It is about.

The characteristics required for steel materials used in bridges, high-rise buildings, ships, and the like have become increasingly strict in recent years, and particularly good toughness is required. Although these steel materials are generally welded and joined, there is a problem that, among the welded joints, in particular, HAZ is affected by heat during welding and tends to be deteriorated in toughness. This toughness deteriorates remarkably as the amount of heat input during welding increases, and the cause is that the cooling rate of HAZ decreases as the amount of heat input during welding increases, and the hardenability decreases to produce coarse island-like martensite. It is becoming. Therefore, in order to improve the toughness of HAZ, it is thought that what is necessary is just to suppress the heat input at the time of welding. On the other hand, on the other hand, in view of increasing the welding work efficiency, it is desired to employ a high heat input welding method having a heat quantity of 50 kJ / mm or more, for example, electrogas welding, electro slag welding, and submerging welding.

Therefore, the present applicant proposes to the patent documents 1-3 the steel material which suppresses deterioration of HAZ toughness at the time of adopting a high heat input welding method. These steel materials are characterized by containing oxides and / or CaO of REM and ZrO ₂ as oxides. Since the oxide is in a liquid phase in molten steel, the oxide is finely dispersed in the steel, and in addition, the oxide does not lose solid solution even when subjected to heat effect during welding, contributing to the improvement of toughness of the HAZ.

On the other hand, Patent Documents 4 and 5 disclose a solvent method of molten steel for preventing nozzle clogging during casting. These patent documents point out that when Ti oxide effective in controlling the structure of the base metal and the weld heat affected zone is present in steel, nozzle clogging tends to occur at the time of injection, and productivity is deteriorated. Specifically, the composition of Ti oxide, Ca oxide, REM oxide, and Al ₂ O ₃ ) is adjusted to an optimum range to prevent clogging of the nozzle.

However, in Patent Documents 4 and 5, the toughness of the weld heat-affected portion in the small heat input welding in which the welding heat input amount is about 10 kJ / mm is only evaluated, and the welding heat input amount is about 50 kJ. It has been clarified by the inventors that the toughness of the weld heat affected zone deteriorates when the high heat input welding of / mm or more is performed.

In addition, although it is not a technique for improving the toughness of the weld heat affected zone, Patent Document 6 discloses that when REM-added steel is used to produce REM-containing steel used in fields such as building structures, bridges, offshore structures, shipbuilding, It has been pointed out that the ladle or the immersion nozzle is blocked and cannot be cast. In this document, nozzle occlusion is caused by REM sulfides; In order to avoid nozzle blockage, what is necessary is just to make REM sulfide into REM oxifide etc., for example.

However, these patent documents 4-6 do not consider enough about the prevention of the melting of a nozzle.

[Patent Document 1] Japanese Patent Application Publication No. 2007-100213 [Patent Document 2] Japanese Patent Application Publication No. 2007-247004 [Patent Document 3] Japanese Patent Application Publication No. 2007-247005 [Patent Document 4] Japanese Patent Application Laid-Open No. 2001-20031 [Patent Document 5] Japanese Patent Application Laid-Open No. 2001-20033 [Patent Document 6] Japanese Patent Application Laid-Open No. 2005-60739

This invention is made | formed in view of the said situation, The objective is to provide the steel material which is excellent in HAZ toughness after a high heat input welding, and does not cause nozzle blockage and nozzle melt | dissolution during injection | pouring.

Steel materials excellent in the toughness of the weld heat-affected zone according to the present invention that can solve the present problem include C: 0.02 to 0.15% (the meaning of “mass%.” Below) and Si: 0.5% or less (including 0%). Mn: 2.5% or less (does not contain 0%), P: 0.03% or less (does not contain 0%), S: 0.02% or less (does not contain 0%), Al: 0.050% Or less (not including 0%), N: 0.01% or less (not including 0%), Ti: 0.005 to 0.10%, Zr: 0.0003 to 0.050%, REM: 0.0003 to 0.015%, Ca: 0.0003 to 0.010 %, The remainder being a steel material consisting of iron and unavoidable impurities, and the steel material contains a composite oxide containing REM, Zr, Ti, Al, and Ca, and measures the composition of all inclusions contained in the steel. When converted into a single oxide, it has a point which satisfy | fills the following (A) and (B).

(A) Oxide of REM (M ₂ O ₃ ): 5 to 50%, ZrO ₂ : 5.0 to 50%, TiO ₂ : 20.0% or less in ratio (mass%) relative to all inclusions (0% not included), Al ₂ O ₃ : 20.0% or less (not including 0%), and CaO: 50.0% or less (including 0%).

(B) The ratio (mass%) with respect to the total amount of oxides (M ₂ O ₃ ), Al ₂ O ₃ , and CaO of REM satisfies the following Equations 1 and 2 below. However, in following [Equation 1] and [Equation 2], [] shows the ratio (mass%) of each oxide.

[Equation 1]

[Equation 2]

The steel of the present invention, as another element, Cu: 2% or less (does not contain 0%), Ni: 3.5% or less (does not contain 0%), Nb: 0.25% or less (does not contain 0%) Mo: 1% or less (does not contain 0%), V: 0.1% or less (does not contain 0%), Cr: 3% or less (does not contain 0%), and B: 0.005% You may further contain 1 or more types of elements chosen from the group which consists of the following (it does not contain 0%).

According to the present invention, a predetermined complex oxide (in particular, a complex oxide containing REM, Zr, Ti, Al, and Ca), which becomes a nucleus of intra-ferrite ferrite transformation, is a ratio with respect to the total inclusions when converted into a single oxide. Since this appropriately controlled complex oxide) is contained in the steel, the HAZ toughness after the high heat input welding is excellent. Further, according to the present invention, the composition of the inclusions ((REM oxides) -Al ₂ O ₃ -CaO inclusions) composed of an oxide of REM, Al ₂ O ₃ , and CaO converted into the above-described oxide is appropriately controlled. Therefore, nozzle clogging and nozzle melt during injection can be effectively prevented.

MEANS TO SOLVE THE PROBLEM In order to provide the steel material excellent in HAZ toughness after a high heat input welding, this inventors examined from the viewpoint of effectively utilizing an interference | inclusion. As a result, (I) the composite oxide containing REM and Zr is very excellent in refining the HAZ structure and stable even at high temperature, compared with the case of REM oxide alone or ZrO ₂ alone. It was found to be effective and defined the ratio of the oxides alone of REM and Zr to effectively exert the effect. In addition, (II) this composite oxide contained Ti, Al, and Ca, and it was found that, if the composition described above when converted into a single oxide is properly controlled, it does not adversely affect the improvement of the HAZ toughness after the high heat input. In addition, the ratio of these single oxides was also prescribed | regulated. It is the following requirement (A) that these results were put together.

(A) The ratio of all the inclusions is oxide of REM (M ₂ O _{3 when} REM is represented by M symbol): 5 to 50%, ZrO ₂ : 5.0 to 50%, TiO ₂ : 20.0% or less (0% Not included), Al ₂ O ₃ : 20.0% or less (not including 0%), and CaO: 50.0% or less (including 0%).

Next, the present inventors are concerned about the blockage of the nozzle by the inclusion in an actual mechanical process in the effective utilization of the inclusion as described above; In view of the fact that depending on the inclusions, there may be a risk of melting of the nozzle, the casting can be performed without causing clogging of the nozzle and consequently no nozzle loss by considering not only the HAZ toughness improvement after the high heat input welding but also the actual mechanical operability. In view of providing the technology at the same time, the review was repeated. As a result, (III) the composition of the inclusion (in particular, the inclusion of (REM oxide) -Al ₂ O ₃ -CaO) prescribed by the following requirement (B) is appropriately controlled as follows, and the melting point of the inclusion is When it was adjusted to within the range useful for the prevention of clogging of the nozzle and melting, it was found that the desired purpose was achieved, and thus the present invention was completed.

(B) The ratio with respect to the total amount of oxides (M ₂ O ₃ ), Al ₂ O ₃ , and CaO of REM satisfies the following Equations 1 and 2 below. However, in following [Equation 1] and [Equation 2], [] shows the ratio of each oxide.

[Equation 1]

[Equation 2]

In this specification, a complex oxide is an oxide containing 2 or more types of elements, and is distinguished from the single oxide which contains only 1 type of element. In the present specification, when REM is represented by the symbol M, the single oxide of REM is represented by "M ₂ O ₃ ", the single oxide of Zr is represented by "ZrO ₂ ", and the single oxide of Ti is "TiO ₂ ". is represented by ", alone the Al oxide is represented by" Al ₂ O ₃ ", a single oxide of Ca is assumed to be indicated by the" CaO ". These single oxides may simply be called "REM oxide".

And the steel material of this invention contains the composite oxide containing REM, Zr, Ti, Al, and Ca. The composite oxide containing these elements does not lose solid solution even when subjected to thermal effects during welding, and is a starting point of intra-ferrite ferrite transformation, which is particularly useful for improving HAZ toughness after high heat input welding. Specifically, the complex oxide is a single oxide (M ₂ O ₃ ) of REM, a single oxide (ZrO ₂ ) of Zr, a single oxide of Ti, Al, and Ca (TiO ₂ , Al ₂ O ₃ , and CaO). These individual oxides may be aggregated with each other. Further, the composite oxide is good may be composed only of an oxide may contain the oxides (e.g., SiO _2, etc.) other than the above elements. Alternatively, the complex oxide may be present in the form of complex precipitation of other compounds such as sulfides and nitrides in addition to the oxides.

EMBODIMENT OF THE INVENTION Hereinafter, the requirements (A) and (B) which characterize this invention are demonstrated in detail.

[(A) Regarding Average Composition of Single Oxide with respect to All Inclusions]

The steel materials of the present invention satisfy the following requirements (A).

(A) The ratio of all the inclusions is an oxide of REM (M ₂ O _{3 when} REM is represented by the symbol M): 5 to 50%, ZrO ₂ : 5.0 to 50%, and TiO ₂ : 20.0% or less (0% ), Al ₂ O ₃ : 20.0% or less (not including 0%), CaO: 50.0% or less (including 0%).

Here, the "all inclusions" mean the inclusions which are observed within the observation visual field by observing the cross section of steel, for example with an Electron Probe X-ray Micro Analyzer (EPMA). The detail of a measurement condition is demonstrated in the column of the Example mentioned later. According to the method, the oxides of the elements contained in the steel material of the present invention [particularly, an oxide specified in the requirement (A) or the oxide of the other elements other than the above (for example, such as MnO and SiO _2)] And sulfides (eg, CaS or REM sulfides, MnS, etc.), carbides, nitrides and the like.

When the ratio of the said single oxide with respect to all the inclusions satisfy | fills the requirements of said (A), a composite oxide becomes effective as a nucleus of intra-ferrite ferrite transformation, and HAZ toughness after a high heat input welding improves further. When the ratio of the said single oxide is less than the said lower limit, the amount of oxides which become a nucleus of intragranular ferrite at the time of welding will be insufficient, and the HAZ toughness improvement effect after high heat input welding will not be exhibited effectively. On the other hand, when the ratio of the said single oxide exceeds the said upper limit, the number of the fine oxides which coarsen an oxide and act effectively as a production nucleus of a ferrite in a mouth becomes small, and the HAZ toughness improvement effect after a high heat input welding is exhibited effectively. It doesn't work.

The detail of the said single oxide is as follows.

First, the ratio of oxides of REM is made 5 to 50%. Preferably it is 10% or more, More preferably, it is 15% or more, More preferably, it is 20% or more. On the other hand, preferably an upper limit is 45%, More preferably, it is 40%. When the REM element is represented by the symbol M, the oxide of REM is present in steel in the form of M ₂ O ₃ , M ₃ O ₅ , MO _2, etc. However, as described above, in the present invention, all oxides of REM are M _2. Mean amount when converted to O ₃ .

The ratio of ZrO ₂ is 5.0 to 50%. Preferably it is 10% or more, More preferably, it is 13% or more, More preferably, it is 15% or more. On the other hand, preferably an upper limit is 45%, More preferably, it is 40%.

The ratios of TiO ₂ , Al ₂ O ₃ , and CaO are TiO ₂ : 20.0% or less (not including 0%), Al ₂ O ₃ : 20.0% or less (not including 0%), CaO: 50.0 It may be% or less (including 0%). Each single oxide has the effect of promoting transformation of ferrite in the mouth, and in order to increase HAZ toughness, all oxides are essential in the present invention. The range of each individual oxide is as follows.

The oxide of Ti is made 20.0% or less (not containing 0%). Preferably it is 18% or less, More preferably, it is 16% or less. It is preferable to contain 0.5% or more of oxides of Ti, More preferably, it is 1% or more. In addition, it is sufficient, and the oxide of Ti is, the steel material from the Ti ₂ O ₃ and Ti ₃ O _5, TiO ₂ present in the form of, but is a value in terms of an oxide of Ti as TiO ₂ all satisfied the above range.

The said Al ₂ O ₃ shall be 20.0% or less (not containing 0%). Preferably it is 15% or less, More preferably, it is 10% or less. If the concentration is moderate, Al ₂ O ₃ has a function of suppressing coarse TiN crystallization on the oxide and suppressing deterioration of toughness caused by coarse inclusions. Preferably it is 0.5% or more.

The CaO is 50.0% or less (including 0%). When it exceeds 50.0%, the transformation ability of the intra-ferrite ferrite is rather deteriorated, and it becomes a cause which causes the melt loss of the nozzle at the time of casting. Preferably it is 45% or less, More preferably, it is 40% or less, Especially preferably, it is 35% or less.

[About ratio of (B) three component inclusion]

The steel materials of the present invention further satisfy the following requirements (B).

(B) The ratio with respect to the total amount of oxides (M ₂ O ₃ ), Al ₂ O ₃ , and CaO of REM satisfies the following Equations 1 and 2 below. However, in following [Equation 1] and [Equation 2], [] shows the ratio of each oxide.

[Equation 1]

[Equation 2]

The three-component inclusions defined in the above requirement (B), that is, inclusions consisting of (oxides of REM) -Al ₂ O ₃ -CaO are very useful for the prevention of clogging of nozzles and melting and are controlled within the above ranges. While maintaining the HAZ toughness after welding, it is possible to cast without causing clogging of the nozzle or melting during casting. Although the reason is not clear in detail, it is thought that it was because the composition within the said range could be adjusted in the range of melting | fusing point useful for preventing the blockage of a nozzle, when the melting | fusing point becomes low or it becomes remarkably high when it leaves out the composition of the said range. do.

In the present invention, when the ratio of Al ₂ O ₃ - Al ₂ O _3] does not satisfy the above Equation 1 is, because the amount of Al ₂ O ₃ is too large, when the Al ₂ O ₃ Injection It adheres to the inner wall of the nozzle to be used, which causes the nozzle to be blocked. Therefore, the amount of Al ₂ O ₃ generated needs to satisfy the above equation (1). Preferably it is good to satisfy following [Equation 1a], More preferably, it is good to satisfy following [Equation 1b].

Equation 1a

[Equation 1b]

In addition, when the ratio of the oxide of REM [oxide of REM (M ₂ O ₃ )] and the ratio of CaO [CaO] does not satisfy the relationship of Equation 2, the amount of CaO produced is compared with that of REM. In this case, excessive CaO reacts with Al ₂ O ₃ constituting the nozzle used at the time of injection to form an oxide having a low melting point composition, which causes the nozzle to be melted. Preferably, the following Equation 2a is satisfied, and more preferably, the following Equation 2b is satisfied.

Equation 2a

[Equation 2b]

Next, the component composition in the steel material (base material) of this invention is demonstrated. The steel materials of the present invention are C: 0.02 to 0.15%, Si: 0.5% or less (0%), Mn: 2.5% or less (0%), P: 0.03% or less as a basic component. (Does not contain 0%), S: 0.02% or less (does not contain 0%), Al: 0.050% or less (does not contain 0%), N: 0.01% or less (does not contain 0%) , Ti: 0.005 to 0.10%, Zr: 0.0003 to 0.050%, REM: 0.0003 to 0.015%, Ca: 0.0003 to 0.010%. The reason for determining this range is as follows.

C is an element that cannot be lacked in order to secure the strength of the steel (base material). In order to exhibit such an effect, it is necessary to contain 0.02% or more. It is preferable to contain C 0.04% or more, More preferably, it is 0.05% or more. However, when C exceeds 0.15%, not only the island-like martensite (MA) is generated in the HAZ during welding, but also causes deterioration of the toughness of the HAZ, and adversely affects the weldability. Therefore, C is made into 0.15% or less. Preferably it is 0.13% or less, More preferably, you may be 0.1% or less.

Si is an element which has a deoxidation effect and contributes to ensuring the strength of steel by solid solution strengthening. In order to exhibit such an effect effectively, it is preferable to contain Si 0.02% or more. More preferably, it is 0.05% or more, More preferably, it is good to contain 0.1% or more. However, when Si exceeds 0.5%, since weldability and toughness of steel materials (base material) deteriorate, it is necessary to suppress Si to 0.5% or less. Preferably it is 0.45% or less, More preferably, it is 0.4% or less. Moreover, when high toughness is calculated | required by HAZ at the time of welding, it is recommended to suppress Si to 0.3% or less. Preferably it is 0.05% or less, More preferably, it is 0.01% or less. However, when Si amount is reduced too much, there exists a tendency for the intensity | strength of the base material itself to fall.

Mn is an element which contributes to the strength improvement of steel materials (base materials). In order to exhibit such an effect effectively, it is preferable to contain 0.5% or more. Mn is more preferably 0.7% or more, and still more preferably 0.8% or more. However, when Mn amount exceeds 2.5%, since the weldability of steel materials (base material) deteriorates, it is necessary to suppress Mn to 2.5% or less. Preferably it is 2.3% or less, More preferably, you may be 2% or less.

P is an element which tends to segregate, and in particular, it is segregated at grain boundaries in steel materials and deteriorates HAZ toughness. Therefore, P needs to be suppressed to 0.03% or less, Preferably it is 0.02% or less, More preferably, it is 0.015% or less. In addition, P usually contains about 0.001% inevitably.

S is a harmful element that combines with Mn to form sulfide (MnS) and deteriorates the toughness of the base material and the ductility in the sheet thickness direction. In addition, S is an element that combines with rare earth elements (eg, La or Ce) to form sulfides (eg, LaS or CeS), inhibits the formation of oxides of rare earth elements, and deteriorates HAZ toughness. . Therefore, S needs to be suppressed to 0.02% or less. Preferably it is 0.015% or less, More preferably, it is 0.01% or less, More preferably, it is 0.006% or less. S is usually inevitably contained in about 0.0005%.

Al is an element that forms a complex oxide together with REM and Zr and acts to improve HAZ toughness. Al is an element that acts as a deoxidizer. However, when excessively added, the oxide is reduced to form coarse Al oxide, which deteriorates HAZ toughness. Therefore, Al needs to be suppressed to 0.050% or less. Al becomes like this. Preferably it is 0.03% or less, More preferably, it is 0.01% or less. In addition, Al usually inevitably contains about 0.0005%.

N is an element which precipitates nitride (for example, ZrN, TiN, etc.), and the nitride prevents coarsening of the austenite grains formed in the HAZ during welding (pinning effect) and also promotes ferrite transformation. Contribute to the improvement of HAZ toughness. In order to exhibit such an effect effectively, it is preferable to contain 0.003% or more. More preferably, it is 0.004% or more. As the N content increases, the formation of nitride promotes miniaturization of the austenite grains, and thus effectively acts to improve the toughness of the HAZ. However, when N exceeds 0.01%, the amount of solid solution N will increase, the toughness of the base material itself will deteriorate, and HAZ toughness will also fall. Therefore, N needs to be suppressed to 0.01% or less. Preferably it is 0.009% or less, More preferably, you may be 0.008% or less.

Ti is an element that forms a complex oxide together with REM and Zr and acts to improve HAZ toughness. In addition, Ti is an element which produces nitrides, such as TiN, and oxide of Ti in steel materials, and contributes to the improvement of HAZ toughness. In order to exhibit such an effect, it is necessary to contain Ti 0.005% or more. Preferably it is 0.007% or more, More preferably, you may be 0.01% or more. However, excessive addition of Ti generates excessively large amounts of oxides of Ti and degrades the toughness of the steel (base metal). Therefore, Ti should be suppressed to 0.10% or less. Ti is preferably 0.07% or less, and more preferably 0.06% or less.

Zr is an element which forms the complex oxide containing Zr and contributes to the improvement of HAZ toughness. In order to exhibit such an effect, it is necessary to contain 0.0003% or more. Preferably it is 0.001% or more, More preferably, it is 0.002% or more. However, when excessively added, coarse Zr carbides are produced, which lowers the toughness of the base material itself. Therefore, it is necessary to suppress Zr to 0.050% or less. Preferably it is 0.04% or less, More preferably, it is 0.03% or less.

REM (rare earth element) is an element which forms the composite oxide containing REM and contributes to the improvement of HAZ toughness. In order to exhibit such an effect, it is necessary to contain REM 0.0003% or more. Preferably it is 0.001% or more, More preferably, it is 0.002% or more. However, when added excessively, since solid solution REM will segregate and base metal toughness will deteriorate, REM needs to be suppressed to 0.015% or less. Preferably it is 0.01% or less, More preferably, it is 0.007% or less.

In the present invention, REM means a lanthanoid element (15 elements from La to Lu) and Sc (scandium) and Y (yttrium). Among these elements, it is preferable to contain at least one element selected from the group consisting of La, Ce, and Y, and more preferably La and / or Ce.

Ca is an element which forms a complex oxide with REM and Zr, and acts to improve HAZ toughness. In order to exhibit such an effect, Ca needs to contain 0.0003% or more. Preferably it is 0.001% or more, More preferably, it is 0.0015% or more. However, when Ca is excessively added, coarse Ca sulfide is formed and the toughness of the base material is degraded. Therefore, Ca needs to be suppressed to 0.010% or less. Ca is preferably 0.009% or less, and more preferably 0.008% or less.

The steel material of this invention contains the said element as an essential component, and remainder is iron and an unavoidable impurity (for example, Mg, As, Se, etc.).

In order to increase the strength of the steel, the steel of the present invention includes Cu: 2% or less (0%), Ni: 3.5% or less (0%), Nb: 0.25% or less (0%). Mo: 1% or less (does not contain 0%), V: 0.1% or less (does not contain 0%), Cr: 3% or less (does not contain 0%), and B: It is also effective to contain at least one element selected from the group consisting of 0.005% or less (not containing 0%). The reason for determining this range is as follows.

Cu is an element which solid-dissolves steel materials, and in order to exhibit such an effect effectively, it is preferable to contain Cu or more. More preferably, it is 0.1% or more, More preferably, it is 0.2% or more. When 0.6% or more is contained in particular, in addition to solid solution strengthening, aging precipitation strengthening is also exhibited, and a significant strength improvement is attained. However, when it contains exceeding 2%, since the toughness of steel materials (base material) will fall, it is good to suppress Cu to 2% or less. Preferably it is 1.8% or less, More preferably, you may be 1.6% or less.

Ni is an element which works effectively to raise the strength of steel materials and to improve the toughness of steel materials. In order to exhibit such an effect effectively, it is preferable to contain 0.05% or more. More preferably, it is 0.1% or more, More preferably, it is 0.2% or more. Although more Ni is preferable, it is an expensive element, and it is preferable to suppress it to 3.5% or less from an economic viewpoint. More preferably, it is 3.3% or less, More preferably, it is 3% or less.

In order to increase the strength by adding Nb, it is preferable to contain 0.003% or more. More preferably, it is 0.005% or more, More preferably, it is 0.01% or more, Especially preferably, it is 0.03% or more. However, when exceeding 0.25%, carbides (NbC) will precipitate and the toughness of a base material will deteriorate, It is preferable to suppress Nb to 0.25% or less. More preferably, it is 0.23% or less, More preferably, it is 0.2% or less.

In order to add Mo and to raise strength, it is preferable to contain 0.01% or more. More preferably, it is 0.02% or more, More preferably, it is recommended to contain 0.03% or more. However, when it exceeds 1%, since weldability deteriorates, it is preferable to make Mo 1% or less. More preferably, it is 0.9% or less, More preferably, it is recommended to suppress it to 0.8% or less.

In order to increase the strength by adding V, it is preferable to contain 0.003% or more. More preferably, it is 0.005% or more, More preferably, it is 0.01% or more, Especially preferably, it is 0.03% or more. However, when it exceeds 0.1%, since weldability will deteriorate and the toughness of a base material will deteriorate, it is preferable to make V 0.1% or less. More preferably, it is 0.08% or less, More preferably, it is 0.06% or less.

In order to increase Cr by adding Cr, it is preferable to contain 0.01% or more. More preferably, it is 0.02% or more, More preferably, it is 0.03% or more, Especially preferably, it is 0.1% or more. However, since weldability deteriorates when it exceeds 3%, it is preferable to suppress Cr to 3% or less. More preferably, it is 1.5% or less, More preferably, it is 1% or less.

B increases the strength of the steel and simultaneously binds with N in the steel to precipitate BN in the process of cooling the HAZ heated at the time of welding, thereby promoting ferrite transformation from the austenite grain. In order to exhibit such an effect effectively, it is preferable to contain 0.0003% or more. More preferably, it is 0.0005% or more, More preferably, it is 0.0008% or more, Especially preferably, it is 0.001% or more. However, if it exceeds 0.005%, the toughness of the steel (base material) deteriorates, so it is preferable that B be 0.005% or less. More preferably, it is 0.004% or less, More preferably, it is 0.003% or less.

Next, the manufacturing method which can be suitably employ | adopted for manufacturing the steel material of this invention is demonstrated.

It is very important that the steel materials of the present invention are produced by strictly managing the order and time of addition of elements to be added to molten steel in which the dissolved oxygen amount of molten steel is adjusted to 0.010% or less, and furthermore, the time until the start of casting. Steel materials satisfying the requirements of (A) and (B) can be produced.

First, molten steel whose quantity of elements except Ti, REM, Zr, and Ca was adjusted suitably was prepared, and molten steel whose dissolved oxygen amount of molten steel was adjusted to 0.010% or less is prepared. Subsequently, at least 1 type of element chosen from the group which consists of Ti, REM, and Zr is added, and Ca is added after that. In this invention, it is important to add Ca within 40 minutes after addition of REM, and to start casting within 80 minutes after addition of Ca. By adding the predetermined alloy element in this order to the molten steel having the dissolved oxygen amount adjusted, generation of coarse oxide is suppressed, and a desired complex oxide serving as a nucleus for intragranular ferrite is produced to satisfy the above requirement (A). Can be. In addition, by appropriately controlling both the time from the addition of REM to the addition of Ca and the time from the addition of Ca to the start of casting, the composition of the three-component inclusions specified in the above requirement (B) is appropriately controlled. It can adjust and it can prevent the blockage of the nozzle at the time of casting, and melting loss. Hereinafter, the manufacturing method of the steel material of this invention is demonstrated in detail.

[About dissolved oxygen amount of molten steel]

First, in this invention, at least 1 type of element chosen from the group which consists of Ti, REM, and Zr is added to the molten steel which adjusted the amount of dissolved oxygen to 0.010% or less. When any one of the above elements is added to molten steel having a dissolved oxygen amount of more than 0.010%, coarse oxides are formed, so that the HAZ toughness deteriorates rather. Therefore, the dissolved oxygen amount before adding the said element shall be 0.010% or less. Preferably it is 0.009% or less, More preferably, you may be 0.008% or less. In addition, dissolved oxygen means oxygen in the free state which does not form oxide and exists in molten steel.

In addition, since the amount of dissolved oxygen in the molten steel primary-refined by the converter and the electric furnace is normally exceeding 0.0100%, in this invention, it is necessary to adjust the amount of dissolved oxygen in molten steel to the said range, for example by the following method.

As a method of adjusting the amount of dissolved oxygen in molten steel, the method of vacuum C deoxidation using a RH type degassing | purification apparatus, the method of adding deoxidative elements, such as Si, Mn, Ti, Al, etc. are mentioned, for example. These methods may be appropriately combined to adjust the amount of dissolved oxygen. Instead of the RH degassing refiner, the dissolved oxygen amount may be adjusted using a ladle heating refiner, a simple molten steel treatment plant, or the like. In this case, since the dissolved oxygen amount cannot be adjusted by vacuum C deoxidation, a method of adding a deoxidizing element such as Si may be employed to adjust the dissolved oxygen amount. When employ | adopting the method of adding deoxidizing element, such as Si, you may add a deoxidizing element when going out to a ladle from a converter.

[About time after REM addition]

Ca is added within 40 minutes after the addition of REM, and casting is started within 80 minutes after the addition of Ca.

If Ca is added before REM is added, Ca oxide is formed in a large amount, and thus CaO reacts with Al ₂ O ₃ constituting the nozzle to form an oxide having a low melting point composition, thereby causing nozzle loss. .

In addition, even when Ca is added after REM is added, when Ca is added for more than 40 minutes after REM is added, oxides of REM are separated and reduced, and a large amount of CaO is added in subsequent Ca addition. Since CaO reacts with Al ₂ O ₃ constituting the nozzle to form an oxide having a low melting point composition, melting of the nozzle occurs. Therefore, the time from adding REM to adding Ca is within 40 minutes. Preferably it is within 36 minutes, More preferably, it is within 32 minutes.

In addition, when casting is started for more than 80 minutes after adding Ca, Ca reduces the oxides formed in the molten steel (especially, oxides of REM), so that a large amount of CaO is formed, and thus CaO forms Al ₂ O ₃ constituting the nozzle. And the oxide of low melting | fusing point composition are formed, and the melt of a nozzle generate | occur | produces. Therefore, the time from the addition of Ca to the start of casting is within 80 minutes. Preferably it is within 70 minutes, More preferably, it is within 60 minutes.

Moreover, according to the examination result of the present inventors, in order to exhibit a desired characteristic effectively, time management of the said process is very important, and it turned out that a desired characteristic is not acquired if it is outside the above-mentioned range.

The form of REM, Ca, Zr, Ti to be added to molten steel is not particularly limited. For example, as REM, pure La, pure Ce, pure Y, or pure Ca, pure Zr, pure Ti, Fe-Si-La alloy, Fe-Si-Ce alloy, Fe-Si-Ca alloy, Fe-Si-La-Ce alloy, Fe-Ca alloy, Ni-Ca alloy, etc. may be added. In addition, you may add a micrometal to molten steel. The micrometal is a mixture of rare earth elements, and specifically contains about 40 to 50% of Ce and about 20 to 40% of La. However, since the micrometal often contains Ca as an impurity, when the micrometal contains Ca, it is necessary to satisfy the range specified by the present invention.

The molten steel obtained by component adjustment may be continuously cast in accordance with a conventional method to form a slab, and then hot rolled in accordance with a conventional method.

The steel according to the present invention can be used, for example, as a material for structures such as bridges, high-rise buildings, ships, and the like. In addition to quenching to medium-heating welding, welding heat influences also in high-input heat welding having a heat input amount of 50 kJ / mm or more. Negative toughness can be prevented.

The steel material of this invention targets steel materials, such as a thick steel plate, whose plate | board thickness is about 3.0 mm or more. The excellent HAZ toughness improvement effect which concerns on this invention is exhibited effectively when it is set as the thick steel plate whose plate | board thickness is 50 mm or more, especially 80 mm or more, and heat input welding with a heat input amount of 50 kJ / mm or more is performed effectively.

[Example]

Hereinafter, although an Example demonstrates this invention still in detail, the following example is not a property which limits this invention, It is also possible to change suitably and to implement it in the range suitable for the meaning mentioned above and later, It is included in the technical scope of the invention.

After the molten iron was first refined in a 240-ton converter, the ladle was pulled out from the converter, and subjected to secondary refining while adjusting the components and adjusting the temperature.

In the ladle, Ti was added to molten steel deoxidized using Si and Mn, and adjusted to the dissolved oxygen amounts shown in Tables 1 and 2, followed by REM and Zr, followed by Ca. At this time, the time from adding REM to adding Ca and the time from adding Ca to starting casting were varied in various ways as shown in Tables 1 and 2 below. Table 1 and Table 2 also show the addition order of REM and Ca. Moreover, about No.33-35 of following Table 1, time from adding Ca to adding REM was shown.

The dissolved oxygen amount means the amount of oxygen contained in the molten steel as the dissolved atom, and was measured using an oxygen sensor using a solid electrolyte. REM is in the form of a micrometal containing about 50% La and about 25% Ce, Zr is a Zr member, Ti is a Fe-Ti alloy, and Ca is a Ni-Ca alloy or a Ca-Si alloy. Or in the form of Fe-Ca green compacts, respectively.

In addition, a ladle heating refining apparatus LF, a reflux type degassing refining apparatus RH, etc. were used for secondary refining.

In following Table 3-Table 6, the component composition (remaining part is iron and an unavoidable impurity) of the steel material after component adjustment is shown.

Molten steel after component adjustment was cast from the ladle to the continuous casting machine, and cast into slab. As a nozzle (ladle nozzle) used when transferring molten steel in a ladle to a continuous casting machine, the nozzle made of alumina graphite generally used in steel industry was used.

After casting, the ladle nozzle is visually observed to see if no deposits are found on the inner wall of the nozzle, `` no nozzle blockage (pass, ○) '', and the deposits are confirmed on the inner wall of the nozzle. Yes (no, x) ". The evaluation results are shown in Tables 11 and 12 below.

In addition, when the ladle nozzle is visually observed and no melt is found in the nozzle, the nozzle is checked for "no nozzle loss (passed, ○)" and the nozzle is checked for "nozzle loss (rejected, x)". Evaluated. The evaluation results are shown in Tables 11 and 12 below.

The slab obtained by casting was hot-rolled and the steel plate of thickness 30mm was obtained. The sample was cut out from the cross section in the t / 4 position (t is the thickness of a hot rolled sheet steel) position of the obtained hot rolled sheet steel. The cut-out sample surface was observed 10,000 times using EPMA "JXA-8500F (device name) made from Nippon Denshi, and the component composition was quantitatively analyzed about the inclusion of 0.2 micrometer or more in maximum diameter. Observation conditions make acceleration voltage 20 mA, sample current 0.01 mA, observation field area 1-5 cm <2>, and the number of analyzes as 100 randomly selected, and quantitates the composition of components in the center part by wavelength dispersion spectroscopy of characteristic X-rays. Analyzed. The element to be analyzed is Al, Mn, Si, Ti, Zr, Ca, La, Ce, O, S. Using a known substance, the relationship between the X-ray intensity of each element and the element concentration is calculated in advance as a calibration curve. In addition, the X-ray intensity obtained from the center part of the inclusion to be analyzed and the concentration of elements contained in the inclusion to be analyzed were quantified from the calibration curve.

In the inclusions, those having an oxygen content of 5% or more were used as oxides. In addition, when 5% or more of oxygen and a plurality of elements were detected from one inclusion, the average composition of the oxide was calculated from the ratio of X-ray intensities based on each element to a single oxide of each element. In addition, when S was detected in an inclusion, the average composition of the oxides of Ca, REM, and Mn was computed on the assumption that sulfides were formed preferentially rather than oxide. That is, when S is detected in inclusions, it is assumed that CaS, REM sulfide, and MnS are produced in the order of Ca, REM, Mn, and the element concentration consumed as sulfide from the element concentration determined according to the detected S concentration. The remaining elemental concentration except for was considered to be produced as an oxide, and the average composition of the oxide was calculated. The composition of the inclusions included in the hot rolled steel sheet is shown in Tables 7 to 10 below.

Note that, in Table 7 to Table 10, "Other" is means an amount of inclusions such as MgO or Cr ₂ O _3.

The oxides of REM existed in the form of M ₂ O ₃ , M ₃ O ₅ , and MO _{2 in} the steel material when the metal element is represented by M. However, all oxides of REM were converted into M ₂ O ₃ to calculate an average composition. Further, oxides of Ti, the Ti ₂ O ₃ in the steel and Ti ₃ O _5, TiO ₂ present in the form of, but in terms of an oxide of any Ti as TiO _2, was calculated average composition.

As a result of observing the sample surface by EPMA, most of the observed inclusions were composite inclusions containing REM and Zr, but also inclusions of REM and inclusions of Zr were produced as single inclusions.

In the composition of the inclusions shown in Tables 7 to 10, the average composition of each oxide when the total of Al ₂ O ₃ , CaO, and REM oxides was reconverted as 100% is shown in Tables 11 and 12 below.

Based on the average composition of each oxide shown in Table 11 and Table 12, the Z value computed by following [Equation 2 '] is shown together with following Table 11 and Table 12.

[Equation 2 ']

Next, in order to evaluate the toughness of HAZ subjected to heat influence at the time of welding, a welding reproducing test shown below was conducted by simulating high heat input welding. The welding reproduction test was performed by heating the sample cut out from the hot rolled steel sheet to 1400 ° C., holding it at this temperature for 60 seconds, and then cooling the sample. Cooling was adjusted so that cooling time from 800 degreeC to 500 degreeC might be 300 second. The impact characteristic of the sample after cooling was evaluated by performing the V notch Charpy test and measuring the absorption energy (vE- ₄₀ ) in _-40 degreeC.

The samples were sampled three by three according to JIS Z2242 "Charpy impact test method of metal materials" from the same steel grade. The average value of vE- ₄₀ measured for each sample is shown in Tables 11 and 12 below. The average value of vE- ₄₀ is 100 J or more as a pass (good HAZ toughness).

From Tables 1 to 12, it can be considered as follows. Nos. 1 to 32 are examples satisfying the requirements specified in the present invention, and since the oxide composition in the steel can be appropriately controlled, the steel is produced without causing clogging of the nozzle or melting during casting. HAZ toughness at the time of welding is favorable. On the other hand, Nos. 33 to 75 are examples that deviate from any of the requirements defined in the present invention.

Particularly in Nos. 33 to 35, since Ca is added to molten steel in which dissolved oxygen amount [O] is adjusted before adding REM, CaO is generated more than that of REM, and the amount of oxide and CaO of REM is increased. The relationship in Equation 2 is not satisfied. Therefore, CaO reacts with Al ₂ O ₃ constituting the nozzle to form an oxide having a low melting point composition, thereby causing the melt of the nozzle.

Since No. 36 adds Ca excessively, CaO is produced | generated too much more than oxide of REM, and the amount of oxide and CaO of REM does not satisfy | fill the relationship of said Formula (2). Therefore, CaO reacts with Al ₂ O ₃ constituting the nozzle to form an oxide having a low melting point composition, thereby causing the melt of the nozzle.

In Nos. 37, 38, 46, and 74, Ca was added in excess of 40 minutes after adding REM. Thus, more CaO was produced than the oxide of REM, and the amount of oxide and CaO of REM was expressed in the above formula. 2] is not satisfied. Therefore, CaO reacts with Al ₂ O ₃ constituting the nozzle to form an oxide having a low melting point composition, thereby causing the melt of the nozzle.

Nos. 39 to 45 are deteriorated in the HAZ toughness because the component composition of the steel is out of the range specified in the present invention.

Nos. 47, 49, 51, and 53 have a large amount of dissolved oxygen in the prepared molten steel, and thus the desired inclusion composition is not obtained. Therefore, the amount of oxide and CaO of REM did not satisfy the above [Equation 2], causing the nozzle melt. HAZ toughness is also deteriorated.

Nos. 48 and 52 show that the dissolved oxygen content of the prepared molten steel is too large, and Ca is added in excess of 40 minutes after the addition of REM. Therefore, the amount of oxide and CaO of REM satisfies Equation 2 above. If not, the nozzle is damaged. HAZ toughness is also deteriorated.

Since No. 50 starts casting more than 80 minutes after adding Ca, the desired inclusion composition is not obtained. Therefore, the amount of oxide and CaO of REM did not satisfy the above [Equation 2], causing a loss of the nozzle.

No. 54 and 56 are examples of adding Ca over 40 minutes after adding REM. In these examples, since the amount of production of Al ₂ O ₃ did not satisfy the above Equation 1, nozzle clogging occurred. HAZ toughness is also deteriorated.

Since No. 60, 61, 75 started casting more than 80 minutes after adding Ca, the desired interference | inclusion composition is not obtained. Therefore, the amount of Al ₂ O ₃ produced did not satisfy the above [Equation 1], causing the loss of the nozzle. In addition, the HAZ toughness is deteriorated.

Nos. 55, 57, 58, and 59 have a large amount of dissolved oxygen in the prepared molten steel, so that the amount of Al ₂ O ₃ produced does not satisfy the above [Equation 1], and clogging of the nozzle occurs. HAZ toughness is also deteriorated.

Nos. 62, 63, 65, 66, 68, 69, 71, and 72 have excessively large amounts of dissolved oxygen in the prepared molten steel, and therefore the composition when converted into a single oxide does not satisfy the above requirement (A). Therefore, the HAZ toughness is deteriorated.

No. 64 and 67 are examples in which casting is started for more than 80 minutes after adding Ca. In these examples, the composition when converted into a single oxide does not satisfy the above requirement (A). Therefore, the HAZ toughness is deteriorated.

No. 70 and 73 are examples of adding Ca over 40 minutes after adding REM. In these examples, the composition when converted into a single oxide does not satisfy the above requirement (A). Therefore, the HAZ toughness is deteriorated.

Claims (2)

C: 0.02 to 0.15% (meaning of "mass%", the same below),
Si: 0.5% or less (not including 0%),
Mn: 2.5% or less (not including 0%),
P: 0.03% or less (not including 0%),
S: 0.02% or less (not including 0%),
Al: 0.050% or less (not including 0%),
N: 0.01% or less (not including 0%),
Ti: 0.005 to 0.10%,
Zr: 0.0003 to 0.050%,
REM: 0.0003 to 0.015%,
Ca: 0.0003 to 0.010%,
Remaining part is steel material which consists of iron and inevitable impurities,
The steel material includes a composite oxide containing REM, Zr, Ti, Al, and Ca,
The steel material excellent in the toughness of the weld heat affected zone characterized by satisfying the following (A) and (B) when the composition of all the inclusions contained in the said steel is measured and converted into the single oxide.
(A) in proportion to the total inclusions,
Oxide of REM (M ₂ O _{3 when} REM is represented by M): 5-50%,
ZrO ₂ : 5.0-50%,
TiO ₂ : 20.0% or less (does not contain 0%),
Al ₂ O ₃ : 20.0% or less (not including 0%), and
CaO: 50.0% or less (including 0%) is satisfied.
(B) The ratio (mass%) with respect to the total amount of oxides (M ₂ O ₃ ), Al ₂ O ₃ , and CaO of REM satisfies the following Equations 1 and 2. However, in following [Equation 1] and [Equation 2], [] shows the ratio (mass%) of each oxide.
[Equation 1]

[Equation 2]

The method according to claim 1, wherein the steel is another element,
Cu: 2% or less (not including 0%),
Ni: 3.5% or less (not including 0%),
Nb: 0.25% or less (not including 0%),
Mo: 1% or less (not including 0%),
V: 0.1% or less (not including 0%),
Cr: 3% or less (not including 0%), and
B: 0.005% or less (not including 0%)
The steel material excellent in the toughness of the weld heat affected part which further contains 1 or more types of elements chosen from the group which consists of these.