JP2003321729A - High strength steel sheet having excellent weld heat affected zone toughness and production method thereof - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide a high strength steel sheet which has excellent weld heat affected zone toughness and can be produced at a low cost without adding large quantities of alloy elements, and to provide a production method thereof. <P>SOLUTION: The high strength steel sheet having excellent weld heat affected zone toughness has a composition containing, by mass, 0.02 to <0.07% C, 0.01 to 0.5% Si, 0.5 to 2.0% Mn, 0.05 to 1.0% W, 0.005 to 0.04% Ti, 0.01 to 0.08% Al, and the balance substantially Fe. The steel sheet has a metallic structure substantially consisting of ferrite and bainite. The steel sheet preferably contains one or two kinds of metals selected from 0.005 to 0.07% Nb and 0.005 to 0.10% V as well. <P>COPYRIGHT: (C)2004,JPO

Description

Detailed Description of the Invention

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a high-strength steel sheet having excellent weld heat-affected zone toughness, which is used in the fields of construction, marine structures, shipbuilding, civil engineering, construction machinery, etc., and a method for producing the same. .

[0002]

2. Description of the Related Art From the viewpoint of increasing the size of welded steel structures and reducing costs, demand for steel sheets having higher strength and higher toughness is increasing. Generally, high strength and high toughness steel sheet uses so-called TMC which uses quenching and tempering treatment, controlled rolling and controlled cooling.
Although it is manufactured by the P method, the quenching and tempering process requires time and labor, and the manufacturing cost is high. Further, when strengthening the strength of a steel material by using the TMCP method, it is necessary to add a large amount of alloying elements to the steel material, which causes problems such as cost increase due to addition of the alloying elements and deterioration of toughness in the weld heat affected zone. .

In order to make up for the drawbacks of quenching and tempering treatment, Japanese Patent Publication Nos. 53-6616 and 58-3011 disclose direct quenching techniques in which quenching is carried out directly after rolling. Since it is performed in a line separate from the rolling / cooling line, there is no big difference from the conventional type, and it does not lead to improvement in production efficiency and production cost.

On the other hand, Japanese Patent No. 3015923 and Japanese Patent No. 3
Japanese Patent No. 015924 discloses a technique in which rolling to quenching and tempering are performed on the same line, and tempering is performed by rapid heating without holding time. Since all steps are performed on the same line, the manufacturing time is shortened,
Manufacturing efficiency and manufacturing cost are greatly improved. Further, the steel material produced by this technique is rapidly cooled to a bainite or martensite structure, and then rapidly heated and tempered, whereby supersaturated solid solution carbon is precipitated as fine cementite, and further tempered without holding time. Cementite does not become coarse by the treatment, so it has excellent strength and toughness.

[0005]

However, Japanese Patent No. 3015
The techniques described in Japanese Patent No. 923 and Japanese Patent No. 3015924 can significantly improve manufacturing efficiency and manufacturing cost, but in order to obtain high-strength steel, the carbon content of the steel material is changed as shown in the examples. Since it is necessary to increase or increase the addition amount of other alloying elements, not only the cost of the material is increased, but also the deterioration of the toughness of the weld heat affected zone becomes a problem. As described above, according to the conventional technique, it is difficult to manufacture a high-strength steel sheet having excellent weld heat-affected zone toughness without adding a large amount of alloying elements.

Therefore, an object of the present invention is to solve the problems of the prior art and to manufacture at a low cost without adding a large amount of alloying elements, and a high-strength steel sheet having excellent weld heat-affected zone toughness and its It is to provide a manufacturing method.

[0007]

The features of the present invention for solving the above problems are as follows.

(1)% by mass, C: 0.02 or more,
Less than 0.07%, Si: 0.01 to 0.5%, Mn:
0.5-2.0%, W: 0.05-1.0%, Ti:
0.005-0.04%, Al: 0.01-0.08%
With the balance consisting essentially of Fe and C in atomic%
C / (W + Ti), which is the ratio of the total amount of W and Ti, is 0.5 to 3.0, and the metal structure is substantially a two-phase structure of ferrite and bainite. W
A high-strength steel sheet having excellent weld heat-affected zone toughness, characterized in that a carbide containing Ti and Ti is dispersed and precipitated.

(2) Further, in mass%, Nb: 0.0
05-0.07% and / or V: 0.005-0.
Containing 10%, C content in atomic% and W, Ti, Nb, V
C / (W + Ti + Nb + V), which is the ratio of the total amount of C.
5 to 3.0, W, Ti and N in the ferrite phase
A high-strength steel sheet having excellent weld heat-affected zone toughness according to (1), characterized in that carbides containing b and / or V are dispersed and precipitated.

(3) The HIC resistance according to (1) or (2), which further contains 0.05 to 1.0% of Mo in a total amount with W in mass%. High strength steel plate with excellent properties.

(4) Further, in mass%, Cu: 0.5
1% or 2 selected from 0% or less, Ni: 0.50% or less, Cr: 0.50% or less, B: 0.005% or less
(1) to (3) characterized by containing at least one species
A high-strength steel sheet excellent in weld heat-affected zone toughness according to any one of 1.

(5) After heating the steel having the chemical composition according to any one of (1) to (4) to a temperature of 1000 to 1300 ° C. and hot rolling at a rolling end temperature of 750 ° C. or higher. Welding characterized by performing accelerated cooling to 300 to 600 ° C. at a cooling rate of 5 ° C./s or more, and then immediately reheating to 550 to 700 ° C. at a heating rate of 0.5 ° C./s or more. Heat-affected zone A method for manufacturing a high-strength steel sheet having excellent toughness.

[0013]

BEST MODE FOR CARRYING OUT THE INVENTION The present inventors diligently studied a method for producing a steel sheet for the purpose of improving the toughness of a heat-affected zone of a high-strength steel sheet, and in a production process of accelerated cooling after controlled rolling and subsequent reheating. In addition to strengthening by bainite transformation during accelerated cooling by performing reheating during bainite transformation, precipitation strengthening by fine precipitates that precipitate during ferrite transformation from untransformed austenite during reheating reduces alloying elements and reduces We have obtained the knowledge that it is possible to increase the strength of steel of the component type. Then, by using a steel containing W and Ti, extremely fine composite precipitation of W and Ti is dispersed and precipitated, and even when Nb and V are added in combination, Ti, W and Nb and It was found that the strength of the ferrite phase can be increased by dispersing and precipitating the precipitate containing V or V.

The present invention has a two-phase structure of the above-described bainite phase produced by accelerated cooling after rolling and a ferrite phase in which precipitates containing Ti and W as a basic matter generated by reheating thereafter are dispersed and precipitated. The present invention relates to a high-strength steel sheet and a manufacturing method thereof, in which precipitation strengthening is utilized in addition to transformation strengthening, so that it is not necessary to add a large amount of alloying elements, and high strength can be achieved without impairing the toughness of the weld heat affected zone. Can be achieved.

The high strength steel sheet of the present invention will be described in detail below. First, the structure of the high strength steel sheet of the present invention will be described.

The metal structure of the steel sheet of the present invention is substantially a two-phase structure of ferrite and bainite. In the present invention, a large amount of alloying elements is added by utilizing transformation strengthening by bainite transformation during accelerated cooling and precipitation strengthening by fine precipitates that are reheated after accelerated cooling and precipitate in ferrite. It is possible to increase the strength. The ferrite phase is rich in ductility and generally soft, but in the present invention, high strength can be achieved by the fine precipitates described below. On the other hand, when the alloying element is not added in a large amount, the strength is insufficient only by the bainite single layer structure obtained by accelerated cooling, but the two phase structure with the precipitation strengthened ferrite phase has sufficient strength. Will be things. When one or more different metal structures such as martensite and pearlite are mixed in the two-phase structure of ferrite and bainite, the strength will decrease. good. However, if the volume fraction of the structure other than the ferrite phase and the bainite phase is low, the effect can be ignored, so that another metal structure having a total volume fraction of 5% or less, that is, one kind of martensite, pearlite, or the like is used. You may contain 2 or more types. Further, from the viewpoint of securing strength, it is desirable that the ferrite fraction be 5% or more, and from the viewpoint of securing the toughness of the base material, the bainite fraction be 10% or more.

Next, the precipitates dispersed and precipitated in the ferrite phase will be described. The steel sheet of the present invention utilizes the precipitation strengthening by the fine composite carbide containing W and Ti in the ferrite phase as a basis. W and Ti are elements that form carbides in steel, and it has been conventionally performed to strengthen steel by precipitation of WC and TiC. However, in the present invention, W and Ti are added together to form W and Ti. By finely precipitating a composite carbide containing, as a basic matter, in steel, a greater strength improving effect can be obtained as compared with the case of precipitation strengthening WC or TiC. This unprecedented strength-enhancing effect is due to the fact that the composite carbide containing W and Ti as the base is stable and has a slow growth rate, so that an extremely fine precipitate having a grain size of less than 10 nm can be obtained. .

The composite carbide containing W and Ti as a basic component is composed of W, Ti and C only, and W and Ti
Is combined with C at an atomic ratio of about 1: 1 and is extremely effective in increasing strength. In the present invention,
It has been found that by adding Nb and / or V in combination, the precipitate becomes a composite carbide containing W, Ti and Nb and / or V, and similar precipitation strengthening can be obtained.

It has also been found that similar precipitation strengthening can be obtained when the composite carbide containing W and Ti as a base contains Mo. When Mo is contained, it is preferable to contain 0.05 to 1.0% of Mo in the total amount with W in mass%. The composite carbide in the case of containing Mo is W, Ti, a composite carbide containing Mo, or W, T
It is a composite carbide containing i, Mo, Nb and / or V.

In the present invention, the composite carbide mainly composed of W and Ti, which is a precipitate that is dispersed and precipitated in the steel sheet, is obtained by producing a steel sheet using the production method of the present invention for steel having the components described below. , And can be obtained by dispersing in a ferrite phase.

Next, the chemical composition of the high strength steel sheet of the present invention will be described. In the following description, all units shown by% are% by mass.

C: 0.02% or more and less than 0.07%.
C is an element that contributes to precipitation strengthening as a carbide,
If less than 0.02%, sufficient strength cannot be secured, and 0.07%
In the above case, since the toughness is deteriorated, the C content is specified to be 0.02 or more and less than 0.07%.

Si: 0.01 to 0.5% Si is added for deoxidation, but if it is less than 0.01%, the deoxidizing effect is not sufficient, and if it exceeds 0.5%, toughness and weldability are deteriorated, so the Si content is 0.01-0.0. Specify 5%.

Mn: 0.5 to 2.0% Mn is added for strength and toughness, but if it is less than 0.5%, its effect is not sufficient, and if it exceeds 2.0%, the weldability deteriorates, so the Mn content is 0.5-2.0%. Prescribed in.

Al: 0.01 to 0.08%. Al is added as a deoxidizer, but if it is less than 0.01%, it has no effect, and if it exceeds 0.08%, the cleanliness of the steel decreases and the toughness deteriorates, so the Al content is 0.01-. Specify to 0.08%.

W: 0.05 to 1.0% W is an important element in the present invention, and when it is contained in an amount of 0.05% or more, it forms fine composite carbide with Ti while suppressing pearlite transformation during cooling after hot rolling, and greatly contributes to the increase in strength. To do. However, if it exceeds 1.0%, the toughness of the weld heat affected zone is deteriorated, so the W content is 0.05 to 1.
Specify 0%.

Ti: 0.005 to 0.04%. Ti
Is an important element in the present invention like W. 0.0
Addition of at least 05% forms fine composite carbides with W and greatly contributes to the strength increase. However, 0.04%
Over T causes deterioration of the toughness of the HAZ,
The i content is specified to be 0.005 to 0.04%.

The high-strength steel sheet of the present invention can obtain fine precipitates of a composite carbide containing Ti and W by using the steels having the above-mentioned components. It is desirable to limit the proportion of the content of the elements forming the as follows. That is, C / (W + Ti), which is the ratio of the amount of C in atomic% to the total amount of W and Ti, is 0.1.
5-3.0 is preferable. Strengthening according to the present invention is Ti,
This is due to the fine composite carbide containing W. In order to effectively utilize the precipitation strengthening by this fine composite carbide, the relationship between the amount of C and the carbide forming elements W and Ti is important, and by adding these elements in an appropriate balance. A thermally stable and very fine composite carbide can be obtained. At this time, when the value of C / (W + Ti) represented by the content of each element in atomic% is less than 0.5 or exceeds 3.0, the amount of any element is excessive and the welding heat affected zone is affected. Since a hardened structure such as island martensite is formed and the toughness of the weld heat affected zone is deteriorated, C / (W
The value of (+ Ti) is preferably 0.5 to 3.0. However, each element symbol is the content of each element in atomic%. When using the content of mass%, (C / 12.01) / (W / 18
3.84 + Ti / 47.9).

Since Nb and / or V form fine composite carbide with Ti and W, the steel sheet of the present invention may contain Nb and / or V.

Nb: 0.005 to 0.07% Nb
Improves the toughness by making the structure finer, but forms a composite carbide together with Ti and W, and contributes to the strength increase. However, if it is less than 0.005%, there is no effect, and if it exceeds 0.07%, the toughness of the weld heat affected zone deteriorates, so the Nb content is specified to be 0.005 to 0.07%.

V: 0.005 to 0.10%. V is also N
Similar to b, it forms a composite carbide with Ti and W and contributes to the increase in strength. However, if it is less than 0.005%, it has no effect, and if it exceeds 0.10%, the toughness of the weld heat affected zone deteriorates, so the V content is specified to be 0.005 to 0.10%.

When Nb and / or V is contained, C / (W + Ti + Nb + V), which is the ratio of the amount of C in atomic% to the total amount of W, Ti, Nb, and V, is 0.5 to 3.0. It is preferable that Strengthening by the present invention is Ti, W
However, when Nb and / or V is contained, it becomes a composite carbide containing them. At this time, C / (W +
If the value of (Ti + Nb + V) is less than 0.5 or exceeds 3.0, the amount of either element is excessive, and a hardened structure such as island martensite is formed in the weld heat affected zone, resulting in deterioration of the weld heat affected zone toughness. C / (W + Ti + Nb + V)
The value of is preferably 0.5 to 3.0. However, each element symbol is the content of each element in atomic%. In addition, mass%
When using the content of (C / 12.01) / (W / 183.84 + Ti / 47.
9 + Nb / 92.91 + V / 50.94).

In the present invention, Mo may be contained.

The total amount of Mo: W is 0.05 to 1.0%
And Mo can replace W in a fine composite carbide containing W and Ti, so the total amount of W and Mo is specified to be 0.05 to 1.0%. When Mo is contained, the value of C / (W + Mo + Ti + Nb + V) is set to 0.5 to 3.0. When using the content of mass%, (C / 12.01) / (W / 18
3.9 + Mo / 95.9 + Nb / 92.91 + V / 50.94 + Ti / 47.9) value from 0.5 to 3.
Set to 0.

In the present invention, one or more of Cu, Ni, Cr and B shown below may be contained for the purpose of further improving the strength and toughness of the steel sheet.

Cu: 0.50% or less. Cu is an element effective in improving toughness and increasing strength, but if added in large amounts, the weldability deteriorates, so if added, 0.50%
Is the upper limit.

Ni: 0.50% or less. Ni is an element effective for improving the toughness and increasing the strength, but if added in a large amount, it becomes costly disadvantageous and the toughness of the weld heat affected zone deteriorates. Therefore, if added, the upper limit is 0.50%. To do.

Cr: 0.50% or less. Cr is Mn
Like C., it is an element effective for obtaining sufficient strength even with low C, but if added in a large amount, the weldability deteriorates, so if it is added, the upper limit is 0.50%.

B: 0.005% or less. B is an element that contributes to strength increase and HAZ toughness improvement, but 0.00
If added in excess of 5%, the weldability will deteriorate, so if added, the content is limited to 0.005% or less.

The balance other than the above consists essentially of Fe.
The fact that the balance consists essentially of Fe means that those containing other trace elements including unavoidable impurities can be included in the scope of the present invention unless the effects of the present invention are lost.

Next, a method of manufacturing the high strength steel sheet of the present invention will be described.

According to the present invention, a large amount of alloying elements is added by utilizing transformation strengthening by bainite transformation during accelerated cooling and precipitation strengthening by fine carbides precipitated in ferrite during reheating after accelerated cooling. This is a technology that can increase the strength without doing so. In the present invention, by supercooling to the bainite transformation region by accelerated cooling, it is possible to complete the ferrite transformation without maintaining the temperature during the subsequent reheating.

The high-strength steel sheet of the present invention is a steel having the above-mentioned composition, and is hot-rolled at a heating temperature of 1000 to 1300 ° C. and a rolling end temperature of 750 ° C. or higher, and then at 5 ° C.
Accelerated cooling to 300 to 600 ° C at a cooling rate of / s or more, and immediately after that, 550 to 550 at a heating rate of 0.5 ° C / s or more.
By reheating to a temperature of 700 ° C., the metal structure has a two-phase structure of ferrite and bainite, and fine composite carbide mainly containing W and Ti can be dispersed and precipitated in the ferrite phase. Here, the temperature is the average temperature of the steel sheet. Hereinafter, each manufacturing condition will be described in detail.

Heating temperature: 1000 to 1300 ° C.
If the heating temperature is lower than 1000 ° C, the solid solution of carbide is insufficient to obtain the required strength, and if it exceeds 1300 ° C, the toughness deteriorates.

Rolling end temperature: 750 ° C. or higher. If the rolling end temperature is low, the subsequent ferrite transformation rate will decrease, and therefore, sufficient precipitation of fine precipitates cannot be obtained during ferrite transformation by reheating, and the strength will decrease, so the rolling end temperature is set to 750 ° C or higher. To do.

Immediately after completion of rolling, cooling is performed at a cooling rate of 5 ° C./s or more. If the cooling rate is less than 5 ° C / s, ferrite is generated during cooling, so that not only reinforcement by bainite cannot be obtained, but also precipitates generated during ferrite transformation in the high temperature range of 700 ° C or higher easily become coarse. , Cannot obtain sufficient strength. Therefore, the cooling rate after rolling is 5 ℃
Specify at least / s. As a cooling method at this time, any cooling equipment can be used depending on the manufacturing process.

Cooling stop temperature: 300 to 600 ° C.
After completion of rolling, it is in the bainite transformation range of 300 to accelerating cooling.
By quenching to 600 ° C., a bainite phase is generated, and cooling is stopped during bainite transformation, whereby untransformed austenite can be transformed into ferrite during subsequent reheating. further,
Since the driving force is increased by the supercooling, the ferrite transformation in the reheating process is promoted, and the ferrite transformation can be completed by the reheating in a short time. If the cooling stop temperature is lower than 300 ° C., the bainite transformation is almost completed, so that not only a sufficient amount of ferrite cannot be obtained by subsequent reheating, but also island martensite (MA) is generated, so that the reheating is not performed. Precipitation of fine carbide becomes insufficient,
If the temperature exceeds 600 ° C, the driving force for ferrite transformation is not sufficient, ferrite transformation is not completed during reheating, and pearlite precipitates, so precipitation of fine carbide is insufficient and sufficient strength cannot be obtained. Stop temperature 300 ~
Specified at 600 ° C.

Immediately after accelerated cooling, reheating is performed to a temperature of 550 to 700 ° C. at a temperature rising rate of 0.5 ° C./s or more. This process is an important manufacturing condition in the present invention. The fine precipitates that contribute to the strengthening of the ferrite phase precipitate simultaneously with the ferrite transformation during reheating. In order to obtain such fine precipitates, it is necessary to reheat to a temperature range of 550 to 700 ° C. immediately after accelerated cooling. Temperature rising rate is 0.5 ℃ / s
If the amount is less than the above, it takes a long time to reach the target reheating temperature, so that the production efficiency is deteriorated, and pearlite transformation occurs. Therefore, dispersed precipitation of fine precipitates cannot be obtained and sufficient strength cannot be obtained. If the reheating temperature is less than 550 ° C, ferrite transformation does not proceed and bainite transformation occurs, so that sufficient precipitation strengthening cannot be achieved, and if it exceeds 700 ° C, precipitates become coarse and sufficient strength cannot be obtained. The temperature range of heating is specified to 550 to 700 ° C. It is not necessary to set the temperature holding time at the reheating temperature. When the production method of the present invention is used, even if the material is cooled immediately after being reheated, ferrite transformation sufficiently progresses, so that high strength due to fine precipitation can be obtained. However, in order to surely complete the ferrite transformation, the temperature can be maintained within 30 minutes. If the temperature is maintained for more than 30 minutes, the precipitate may become coarse and the strength may be reduced. Further, since the ferrite transformation progresses even in the cooling process after reheating, the cooling rate after reheating is basically air cooling. However, it is also possible to perform cooling at a high cooling rate that does not inhibit ferrite transformation.

FIG. 1 shows a steel sheet of the present invention (0.05C-0.25Si-1.2Mn-) manufactured by the above manufacturing method.
0.2W-0.01Ti) transmission electron microscope (TEM)
The photograph observed at is shown. According to FIG. 1, it can be confirmed that very fine precipitates are precipitated in rows, but this is due to transformation precipitation that occurs at the austenite / ferrite interface during ferrite transformation. An extremely high precipitation strengthening is obtained. The precipitate is a carbide containing W and Ti, and this was confirmed by analysis using energy dispersive X-ray spectroscopy (EDX) or the like.

As equipment for reheating after accelerated cooling, a heating device can be installed on the downstream side of the cooling equipment for accelerated cooling. As the heating device, it is preferable to use a gas combustion furnace or an induction heating device capable of rapidly heating the steel sheet. The induction heating device is particularly preferable because it is easier to control the temperature than the soaking furnace and the cost is relatively low, and the steel sheet after cooling can be heated quickly. Further, by arranging a plurality of induction heating devices in series continuously, even when the line speed and the type and size of the steel sheet are different, it is only necessary to arbitrarily set the number of induction heating devices to be energized. It is possible to freely control the reheating temperature.

An example of equipment for carrying out the manufacturing method of the present invention is shown in FIG. As shown in FIG. 2, a hot rolling mill 3, an accelerated cooling device 4, an in-line induction heating device 5, and a hot leveler 6 are arranged in the rolling line 1 from the upstream side to the downstream side. In-line type induction heating device 5
Alternatively, another heat treatment apparatus may be used as the hot rolling mill 3 which is a rolling equipment and the accelerated cooling device 4 which is a subsequent cooling equipment.
By installing on the same line as above, since reheating treatment can be performed quickly after the completion of rolling and cooling, heating can be performed without excessively lowering the temperature of the steel sheet after rolling and cooling.

[0052]

EXAMPLE Steels having the chemical composition shown in Table 1 (steel types A to R) were made into slabs by the continuous casting method, and the slabs were made to have plate thicknesses of 18 and 2.
6 mm thick steel plates (No. 1-32) were manufactured.

[0053]

[Table 1]

After the heated slab is rolled by hot rolling, it is immediately cooled using a water cooling type accelerated cooling equipment,
Reheating was performed using an induction heating furnace or a gas combustion furnace.
The induction heating furnace was installed on the same line as the accelerated cooling equipment.
Table 2 shows the manufacturing conditions of each steel plate (No. 1 to 32).

The microstructure of the steel sheet produced as described above was observed with an optical microscope and a transmission electron microscope (TEM). The components of the precipitate were analyzed by energy dispersive X-ray spectroscopy (EDX). In addition, the tensile properties and weld heat affected zone (HAZ) toughness of each steel sheet were measured. Table 2 shows the measurement results
Are also shown. As for the tensile properties, a tensile test was performed using a full-thickness test piece in the vertical direction of rolling as a tensile test piece, and the tensile strength was measured. Tensile strength of 580 MPa or more was defined as the strength required for the present invention. Regarding the weld heat affected zone (HAZ) toughness, a Charpy test was performed using a test piece to which a heat history corresponding to a heat input of 40 kJ / cm was added by a reproduction heat cycle device. And Charpy absorbed energy at -10 ℃ is 100J
The above items were regarded as good.

[0056]

[Table 2]

In Table 2, No. 1 to No. 1 of the present invention are shown.
No. 18 has a chemical composition and a manufacturing method within the scope of the present invention, and has a high tensile strength of 580 MPa or more,
The weld heat-affected zone toughness is good, and the structure of the steel sheet is substantially a ferrite + bainite two-phase structure, and Ti and W, and for some steel sheets, Nb and / or V and Mo are further added. Precipitates of fine composite carbides having a particle size of less than 10 nm were dispersed and precipitated.

In Nos. 19 to 25, the chemical components are within the scope of the present invention, but the manufacturing method is outside the scope of the present invention, so that the structure does not become a ferrite + bainite two-phase structure or a fine composite structure. In some cases, carbide was not dispersed and precipitated, and the strength was insufficient. Nos. 26 to 32 had chemical components outside the range of the present invention, and thus sufficient strength could not be obtained, or the weld heat affected zone toughness was poor.

[0059]

As described above, according to the present invention, a high-strength steel sheet having excellent toughness in the weld heat-affected zone can be manufactured at low cost without adding a large amount of alloying elements. Therefore, steel plates used for welded structures such as buildings, marine structures, shipbuilding, civil engineering, and construction machines can be inexpensively and stably manufactured in large quantities, and productivity and economic efficiency can be significantly improved.

[Brief description of drawings]

FIG. 1 is a photograph of a steel plate of the present invention observed with a transmission electron microscope (TEM).

FIG. 2 is a schematic view showing an example of a production line for carrying out the production method of the present invention.

[Explanation of symbols]

1: rolling line, 2: Steel plate, 3: hot rolling mill, 4: Accelerated cooling device, 5: In-line induction heating device, 6: Hot leveler

   ─────────────────────────────────────────────────── ─── Continued front page    (72) Inventor Nobuyuki Ishikawa             1-2-1, Marunouchi, Chiyoda-ku, Tokyo             Main Steel Pipe Co., Ltd. F-term (reference) 4K032 AA01 AA02 AA04 AA11 AA14                       AA16 AA20 AA22 AA23 AA31                       AA35 AA36 AA37 BA01 CC03                       CC04 CD02 CF01 CF02

Claims (5)

[Claims] 1. C: 0.02 or more, 0.07 in mass%
%, Si: 0.01 to 0.5%, Mn: 0.5 to
2.0%, W: 0.05 to 1.0%, Ti: 0.005
~ 0.04%, Al: 0.01-0.08%,
The balance consists essentially of Fe, and the C content in atomic% and W, T
C / (W + Ti), which is the ratio of the total amount of i, is 0.5 to 3.
0, the metal structure is substantially a two-phase structure of ferrite and bainite, and carbides containing W and Ti are dispersed and precipitated in the ferrite phase. Excellent high strength steel plate. 2. Further, Nb: 0.005 by mass%.
0.07% and / or V: 0.005-0.10%
And C / (W + Ti + Nb + V), which is the ratio of the amount of C in atomic% and the total amount of W, Ti, Nb, and V, is 0.5 to
It is 3.0, and carbides containing W, Ti, and Nb and / or V are dispersed and precipitated in the ferrite phase, and the toughness of the weld heat affected zone according to claim 1 is excellent. High strength steel plate. 3. Further, in the total amount with W in mass%,
The high-strength steel sheet having excellent HIC resistance according to claim 1 or 2, which contains 0.05 to 1.0% of Mo. 4. Further, in mass%, Cu: 0.50% or less, Ni: 0.50% or less, Cr: 0.50% or less,
B: One or more selected from 0.005% or less is contained, and Claim 1 thru | or 3 characterized by the above-mentioned.
A high-strength steel sheet excellent in weld heat-affected zone toughness according to any one of 1. 5. A steel having the composition of any one of claims 1 to 4 is heated to a temperature of 1000 to 1300 ° C., hot rolled at a rolling end temperature of 750 ° C. or higher, and then 5 Welding heat effect, characterized by performing accelerated cooling to 300 to 600 ° C at a cooling rate of ℃ / s or more, and then immediately reheating to 550 to 700 ° C at a heating rate of 0.5 ° C / s or more A method for manufacturing a high-strength steel sheet having excellent toughness.