JP5034290B2 - Low yield ratio high strength thick steel plate and method for producing the same - Google Patents

Description

  The present invention relates to a thick steel plate that is used by welding in the field of construction, civil engineering, and the like, and more particularly, to a high-strength thick steel plate excellent in weldability having a yield stress YS of 650 MPa or more and a yield ratio YR of 80% or less. Is.

  In recent years, with the increase in the size and the span of steel structures in the fields of construction and civil engineering, there is an increasing demand for thickening and increasing the strength of steel materials used. On the other hand, from the viewpoint of ensuring the safety of a steel structure, it is required to have a high allowable stress and to reduce the yield ratio, which is the ratio between the yield stress and the tensile strength. By reducing the yield ratio, even if an external stress higher than the yield stress is applied, the stress can be absorbed by plastic deformation, and since the allowable stress leading to fracture is large, the plastic deformability is excellent. This is because it becomes a steel material.

  However, in a high-tensile steel sheet having a yield stress exceeding 650 MPa, a large amount of alloy elements is generally added to ensure strength. For this reason, the yield ratio increases and the toughness and weldability tend to decrease. Therefore, it is desired to develop a thick steel plate having a low yield ratio and excellent weldability even with high strength.

For example, Patent Documents 1 to 4 propose a method of manufacturing a low yield ratio high strength thick steel plate having a yield stress exceeding 650 MPa. The techniques described in Patent Documents 1 and 2 quench the hot-rolled steel sheet, and then heat and quench again to the two-phase region of ferrite + austenite to achieve high strength and a low yield ratio. Yes. The technique described in Patent Document 3 is a direct quenching method in which quenching is performed immediately after rolling, and the microstructure after quenching is changed to a bainite phase or a martensite phase and then heated again to a two-phase region of ferrite and austenite. Normalizing, achieving high strength and low yield ratio. Further, the technique described in Patent Document 4 is a direct quenching method that delays the start of quenching after rolling, and after ferrite is precipitated, it is rapidly cooled to form a two-phase structure of ferrite phase + martensite phase. High strength and low yield ratio are realized.
JP 2001-288512 A Japanese Patent Laid-Open No. 06-248337 Japanese Patent Laid-Open No. 05-230531 Japanese Patent Application Laid-Open No. 07-097626

  However, since the techniques described in Patent Documents 1 and 2 require a complicated heat treatment process, there is a problem that productivity is low and manufacturing cost is high. Moreover, the technique described in Patent Document 3 is to prevent degradation of retained austenite, recovery of martensite, recovery of strength, toughness, and low yield ratio due to recrystallization by normalizing after direct quenching. In addition, it is necessary to add a total amount of Mn, Ni, Cu, Co more than a predetermined amount, and there is a problem that the manufacturing cost becomes high. Furthermore, the technique described in Patent Document 4 varies the volume fraction of the ferrite and martensite phases depending on the manufacturing conditions and the position in the steel plate, so that a high strength and a low yield ratio can be stably achieved. The situation is not reached.

  Accordingly, an object of the present invention is to produce a high-strength thick steel plate having high strength, a low yield ratio, and excellent weldability without adding a large amount of alloy elements and without performing complicated heat treatment, and its production. To propose a method. A specific development target of the present invention is a high strength thick steel plate excellent in weldability with a yield stress YS of 650 MPa or more and a yield ratio YR of 80% or less.

In order to achieve the above-described problems, the inventors have conducted intensive research on various factors affecting strength, yield ratio, and weldability. As a result, in order to stably realize a yield stress of 650 MPa or more and a low yield ratio of 80% or less, and to ensure excellent weldability, in addition to strict component adjustment, a carbon equivalent C _eq is further set. _{0.35～0.50Mass%,} it is important to control the _{P cm} below 0.28Mass%, further, as a steel sheet microstructure, it is necessary to ensure more than 60% of martensite phase at an area fraction I found out. In addition, in order to stably obtain a thick steel plate having a yield stress of 650 MPa or more and a low yield ratio of 80% or less, the steel material adjusted as described above is hot-rolled, and then the cooling rate and cooling stop. It has been found that it is necessary to perform an accelerated cooling process in which the temperature is optimized, and further a reheating process in which the heating rate after the cooling is stopped, the reheating temperature, and the holding time are optimized.
The present invention has been completed based on the above findings and further studies.

That is, the present invention is C: 0.03-0.2 mass%, Si: 0.05-0.5 mass%, Mn: 0.8-3 mass%, P: 0.02 mass% or less, S: 0.005 mass % Or less, Al: 0.1 mass% or less, N: 0.007 mass% or less, with the balance being Fe and inevitable impurities, the following formula (l):
Ceq = C + Si / 24 + Mn / 6 (1)
Here, C, Si, Mn: content of each element (mass%)
The Ceq defined by the formula is 0.35 to 0.5 mass%, and the following formula (2):
P _cm = C + Si / 30 + Mn / 20 (2)
Here, C, Si, Mn: content of each element (mass%)
In being defined _{P cm} is less 0.28Mass%, and have your 90% or more areas of ItaAtsudan surface, made balance being bainite phase at an area fraction of martensite phase is 60% or more, yield stress It is a low yield ratio high strength thick steel plate with YS of 650 MPa or more, tensile strength TS of 826 MPa or more, and yield ratio YR of 80% or less.

In addition to the above component composition, the thick steel plate of the present invention further includes Cu: 0.1 to 1 mass%, Ni: 0.1 to 1 mass%, Cr: 1 mass% or less, Mo: 1 mass% or less, Nb: 0.1 mass. % Or less, V: 0.2 mass% or less, Ti: 0.03 mass% or less, B: 0.005 mass% or less, Ca: 0.005 mass% or less, REM: 0.02 mass% or less, and Mg: 0.005 mass% or less 1 type or 2 types or more selected from among the following (3) formula;
C _eq = C + Si / 24 + Mn / 6 + Ni / 40 + Cr / 5 + Mo / 4 + V / 14 (3)
Here, C, Si, Mn, Cr, Ni, Mo, V, content of each element (mass%)
C _eq defined by the following formula is 0.35 to 0.50 mass%, and the following formula (4):
P _cm defined by is 0.28 mass% or less.
P _cm = C + Si / 30 + (Mn + Cu + Cr) / 20 + Ni / 60 + Mo / 15 + V / 10 + 5 × B (4)
Here, C, Si, Mn, Cu, Cr, Ni, Mo, V, B: Content of each element (mass%)

In the present invention, C: 0.03 to 0.2 mass%, Si: 0.05 to 0.5 mass%, Mn: 0.8 to 3 mass%, P: 0.02 mass% or less, S: 0.005 mass % Or less, Al: 0.1 mass% or less, N: 0.007 mass% or less, with the balance consisting of Fe and inevitable impurities, the following formula (1):
C _eq = C + Si / 24 + Mn / 6 (1)
Here, C, Si, Mn: content of each element (mass%)
C _eq defined by the following formula is 0.35 to 0.5 mass%, and the following formula (2):
P _cm = C + Si / 30 + Mn / 20 (2)
Here, C, Si, Mn: content of each element (mass%)
A steel slab having a P _cm defined by ≦ 0.28 mass% is heated to 1000 to 1250 ° C. and then hot-rolled to a rolling end temperature of 800 ° C. or higher, and a cooling rate from a temperature range of Ar ₃ transformation point or higher. Accelerated cooling to a temperature range of 350 ° C. or lower at 5 to 60 ° C./s is temporarily interrupted, and then reheated to a temperature of 350 to 550 ° C. at a rate of temperature rise of 2 ° C./s or higher for 15 minutes. A method for producing a high yield strength steel sheet having a low yield ratio , having a yield stress YS of 650 MPa or more, a tensile strength TS of 826 MPa or more, and a yield ratio YR of 80% or less, characterized by cooling after being held below.

In addition to the above component composition, the production method of the present invention further includes Cu: 0.1 to 1 mass%, Ni: 0.1 to 1 mass%, Cr: 1 mass% or less, Mo: 1 mass% or less, Nb: 0.1 mass. % Or less, V: 0.2 mass% or less, Ti: 0.03 mass% or less, B: 0.005 mass% or less, Ca: 0.005 mass% or less, REM: 0.02 mass% or less, and Mg: 0.005 mass% or less 1 type or 2 types or more selected from among the following (3) formula;
C _eq = C + Si / 24 + Mn / 6 + Ni / 40 + Cr / 5 + Mo / 4 + V / 14 (3)
Here, C, Si, Mn, Cr, Ni, Mo, V: Content of each element (mass%)
C _eq defined by the formula 0.35 to 0.50 mass%, and the following formula (4):
P _cm = C + Si / 30 + (Mn + Cu + Cr) / 20 + Ni / 60 + Mo / 15 + V / 10 + 5 × B (4)
Here, C, Si, Mn, Cu, Cr, Ni, Mo, V, B: Content of each element (mass%)
P _cm defined by is 0.28 mass% or less.

  According to the present invention, it is possible to stably manufacture a thick steel plate having excellent weldability and having a yield stress of 650 MPa or more and a low yield ratio of 80% or less without performing complicated heat treatment. Therefore, it can greatly contribute to the enlargement of steel structures, the improvement of earthquake resistance, and the improvement of construction efficiency.

First, the steel structure in the thick steel plate of the present invention will be described.
Conventionally, a multistage heat treatment including reheating and quenching to a ferrite + austenite two-phase region is generally used as a manufacturing process of a low yield ratio high strength thick steel plate. The structure of the thick steel plate obtained by such a process is mainly composed of a ferrite phase and dispersed bainite or martensite as a hard second phase. Depending on the volume fraction of the ferrite phase, the yield stress is 650 MPa or more. There is a problem that the high strength of can not be achieved stably.

On the other hand, the conventional manufacturing process of high-strength thick steel sheets with yield stress of 650 MPa or higher, which does not consider the yield ratio, is quenched from the temperature above the Ac ₃ transformation point to a relatively low temperature range immediately after rolling or after reheating. Then, it is common to perform a long-time tempering treatment using a heat treatment furnace in a temperature range below the Ac ₁ transformation point. In this case, the steel structure is mainly composed of a tempered martensite phase, and 80% There is a problem that the following yield ratio cannot be achieved.

  Therefore, the present invention provides a steel sheet structure for stably achieving a high strength with a yield stress of 650 MPa or more and a low yield ratio of 80% or less, and a martensite phase containing a large amount of movable dislocations in an area fraction of 60% or more. Is an essential requirement. This is because the martensite structure quenched immediately after rolling has a very high dislocation density and a very hard phase, and thus has a high tensile strength. This is because it is possible to achieve both high strength and a low yield ratio in order to suppress excessive increase.

  However, as-quenched martensite structure reduces the ductility and toughness of the base metal, and thus has not been actively used as a structure of a low yield ratio high-strength thick steel sheet. Therefore, conventionally, in order to improve the ductility and toughness of the as-quenched martensitic steel, it is common to perform a tempering treatment for a long time using a heat treatment furnace to obtain a tempered martensite phase. However, in this case, the movable dislocation disappears and the yield stress is significantly increased, so that there is a problem that a low yield ratio of 80% or less cannot be achieved.

  Therefore, in the present invention, while strict component adjustment is performed and accelerated cooling after hot rolling and reheating treatment conditions after stopping cooling are strictly defined, while improving ductility and toughness, high strength is achieved. A suitable microstructure for achieving both a low yield ratio and a low yield ratio is defined as follows.

First, the microstructure included in the steel plate of the present invention, at 90% or more of the regions of the plate thickness cross section, it is necessary that martensite is in an area fraction of 60% or more. The phase excluding the martensite phase is substantially a bainite phase. If the area fraction of martensite is less than 60%, it is impossible to achieve both high strength with a yield stress of 650 MPa or more and low yield ratio of 80% or less . Such a microstructure may be satisfied in an area of 90% or more of the plate thickness cross section.

  When a structure such as ferrite, pearlite, and cementite is mixed as a phase other than the martensite phase, the strength is lowered, so that the area fraction is preferably small. Further, when island martensite coexists, the toughness is lowered, so it is preferable that this area fraction is also small. However, when the structure mixed in addition to the martensite phase and the bainite phase is 10% or less in area fraction, the influence can be ignored.

Next, the reason which limits the component composition of the thick steel plate of this invention is demonstrated.
C: 0.03-0.2 mass%,
C has a large effect of increasing the strength of steel and is a component necessary for ensuring the strength required for structural steel. In order to acquire the said effect, it is necessary to contain C 0.03 mass% or more. On the other hand, the addition exceeding 0.2 mass% reduces the weld heat affected zone (HAZ) toughness and weld crack resistance, as well as the toughness of the base material. Therefore, in the present invention, C is in the range of 0.03 to 0.2 mass%. Preferably it is the range of 0.05-0.15 mass%.

Si: 0.05-0.5 mass%
When Si is added as a deoxidizing material, it is necessary to add at least 0.05 mass%. However, if added over 0.5%, the toughness of the base material deteriorates, and the weldability and the HAZ toughness significantly decrease. Therefore, Si is set to a range of 0.05 to 0.5 mass%. Preferably it is the range of 0.05-0.35 mass%.

Mn: 0.8-3 mass%
Mn has an effect of increasing the strength of steel, and in the present invention, it is necessary to contain 0.8 mass% or more in order to ensure a yield stress of 650 MPa or more. On the other hand, when it contains exceeding 3 mass%, the toughness of a base material and HAZ toughness will fall remarkably. Therefore, Mn is set to a range of 0.8 to 3 mass%. Preferably it is 1.0-2.5 mass%.

P: 0.02 mass% or less P is an element that is mixed as an inevitable impurity in the steel, increases the strength of the steel, and degrades the toughness. In particular, it greatly reduces the toughness of the welded portion, so it is reduced as much as possible. It is desirable. When P exceeds 0.02 mass%, this tendency becomes remarkable, so this value is set as the upper limit. In addition, since excessive reduction of P leads to an increase in refining cost, it is desirable that the lower limit of P is about 0.005 mass%.

S: 0.005 mass% or less S is an element that is mixed as an inevitable impurity in steel and deteriorates the toughness of the base metal and the welded portion, and is desirably reduced as much as possible. In particular, when S exceeds 0.005 mass%, this tendency becomes remarkable. Therefore, S is set to 0.005 mass% or less.

Al: 0.1 mass% or less Al is a component added as a deoxidizer, and is most commonly used in molten steel deoxidation of high-tensile steel. In addition, N in the steel is fixed as AlN, which contributes to improving the toughness of the base material. Such an effect is recognized by addition of Al: 0.005 mass% or more. On the other hand, addition exceeding 0.1 mass% leads to a decrease in the toughness of the base material, and is mixed into the weld metal part during welding to decrease the toughness. For this reason, content of Al shall be 0.1 mass% or less. Preferably, it is 0.01-0.07 mass%.

N: 0.007 mass% or less N is an impurity component inevitably contained in the steel. When N exceeds 0.007 mass%, the base material and weld zone toughness are significantly reduced. For this reason, content of N shall be 0.007 mass% or less.

C _eq : 0.35 to 0.50 mass%
In the present invention, it is necessary to adjust the content of each component so that the carbon equivalent C _eq defined by the following formula (1) is 0.35 to 0.50 mass% within the above-described component composition range. .
C _eq = C + Si / 24 + Mn / 6 (1)
Here, C, Si, Mn: content of each element (mass%)
When C _eq is less than 0.35 mass%, the hardenability in accelerated cooling after rolling becomes insufficient, and a desired yield stress of 650 MPa or more cannot be secured. On the other hand, if C _eq exceeds 0.50 mass%, the base material toughness and the uniform elongation decrease. Therefore, C _eq needs to be in the range of 0.35 to 0.50 mass%.

In the present invention, it is further necessary to adjust the content of each component so that P _cm defined by the following formula (2) is 0.28 mass% or less within the above component composition range.
P _cm = C + Si / 30 + Mn / 20 (2)
Here, C, Si, Mn: content of each element (mass%)
P _cm is an index of the cold cracking property of the weld, and is desirably as low as possible. When P _cm exceeds 0.28 mass%, the weldability is remarkably lowered. Therefore, P _cm needs to be adjusted to 0.28 mass% or less.

In addition to the above essential components, the thick steel plate of the present invention is optionally selected from one or two selected from Cu, Ni, Cr, Mo, Nb, V, Ti, B, Ca, REM and Mg. The above can be contained in the following ranges.
One or two kinds selected from Cu: 0.1 to 1 mass% and Ni: 0.1 to 1 mass% Cu and Ni have an effect of increasing strength while maintaining high toughness, and have a small adverse effect on HAZ toughness. Therefore, it is an element useful for increasing the strength, and can be contained as necessary.
Cu is preferably contained in an amount of 0.1% or more. However, if the content exceeds 1 mass%, hot brittleness is caused to deteriorate the surface properties of the steel sheet. Therefore, Cu is preferably added in the range of 0.1 to 1 mass%. More preferably, it is the range of 0.2-0.7 mass%.
Ni is preferably contained in an amount of 0.1 mass% or more, but even if contained in excess of 1 mass%, the effect is saturated, an effect commensurate with the content cannot be obtained, and only an increase in cost is caused. Therefore, Ni is preferably in the range of 0.1 to 1 mass%. More preferably, it is 0.2-0.8 mass%.

Cr: 1 mass% or less, Mo: 1 mass% or less, Nb: 0.1 mass% or less, V: 0.2 mass% or less, Ti: 0.03 mass% or less, and B: 0.005 mass% or less Alternatively, two or more of Cr, Mo, Nb, V, Ti, and B are elements that contribute to improving the strength of steel, and can be added as necessary.
Cr is preferably contained in an amount of 0.05 mass% or more. However, if it exceeds 1 mass%, the HAZ toughness is deteriorated.
Mo is preferably contained in an amount of 0.05 mass% or more, but if it exceeds 1 mass%, it adversely affects the base material toughness and the HAZ toughness. Therefore, it is desirable to add 1 mass% or less of Mo.
Nb is preferably contained in an amount of 0.005 mass% or more. However, if it exceeds 0.1 mass%, the base material toughness and the HAZ toughness are deteriorated. Therefore, the Nb content is preferably 0.1 mass% or less.
V is preferably contained in an amount of 0.01 mass% or more, but if it exceeds 0.2 mass%, the HAZ toughness decreases, so 0.2 mass% or less is desirable.
Ti contributes to the improvement of strength by containing 0.005 mass% or more. Further, it has a strong affinity with N, and precipitates as TiN during solidification, thereby suppressing the austenite grain coarsening in the HAZ and contributing to high toughness of the HAZ. On the other hand, when it contains exceeding 0.03 mass%, base material toughness will deteriorate. Therefore, Ti is preferably added in an amount of 0.03 mass% or less.
B has the effect of increasing the strength of the steel through improving hardenability. However, if the content of B exceeds 0.005 mass%, the hardenability is remarkably increased, and the toughness and ductility of the base material are deteriorated. Therefore, B is preferably added in an amount of 0.005 mass% or less. More preferably, it is the range of 0.0003-0.002 mass%.

One or more selected from Ca: 0.005 mass% or less, REM: 0.02 mass% or less, and Mg: 0.005 mass% or less Ca, REM, and Mg are all components that contribute to improved toughness. Yes, it can be added as needed.
Ca is a useful component that improves toughness through refinement of crystal grains, and is preferably contained in an amount of 0.001 mass% or more. However, even if it contains exceeding 0.005 mass%, since the said effect is saturated, it is preferable to make 0.005 mass% into an upper limit.
Although it is preferable to contain REM 0.002 mass% or more, since an effect will be saturated even if it contains exceeding 0.02 mass%, it is preferable to make 0.02 mass% into an upper limit.
Mg is a component having an effect of improving toughness through refinement of crystal grains, and is preferably added in an amount of 0.001 mass% or more. However, even if added over 0.005 mass%, the effect is saturated, so it is preferable to set the upper limit to 0.005 mass%.

In the case of adding the above selection element steel plate of the present invention, within the chemical composition range of the above, and 0.35～0.5Mass% carbon equivalent _{C eq,} defined by the following equation (3) Therefore, it is necessary to adjust the content of each component.
C _eq = C + Si / 24 + Mn / 6 + Ni / 40 + Cr / 5 + Mo / 4 + V / 14 (3)
Here, C, Si, Mn, Ni, Cr, Mo, V: Content of each element (mass%)
When C _eq is less than 0.35 mass%, the hardenability in accelerated cooling after rolling becomes insufficient, and a desired yield stress of 650 MPa or more cannot be secured. On the other hand, if C _eq exceeds 0.50 mass%, the base material toughness and the uniform elongation decrease. Therefore, C _eq needs to be in the range of 0.35 to 0.50 mass%.

Further, when the above-mentioned selective element is added to the thick steel plate of the present invention, each P _cm defined by the following formula (4) is 0.28 mass% or less within the above component composition range. It is necessary to adjust the content of the components.
P _cm = C + Si / 30 + (Mn + Cu + Cr) / 20 + Ni / 60 + Mo / 15 + V / 10 + 5 × B (4)
Here, C, Si, Mn, Cu, Cr, Ni, Mo, V, B: Content of each element (mass%)
P _cm is an index of the cold cracking property of the weld, and is desirably as low as possible. When P _cm exceeds 0.28 mass%, the weldability is remarkably lowered. Therefore, P _cm needs to be adjusted to 0.28 mass% or less.

  In the thick steel plate of the present invention, the components other than the above are preferably composed of Fe and inevitable impurities. However, as long as the effects of the present invention are not impaired, the inclusion of components other than those described above is not rejected.

Next, the manufacturing method of the thick steel plate concerning this invention is demonstrated. In addition, the temperature demonstrated hereafter means the temperature of plate | board thickness center part (1 / 2t) unless there is particular notice.
The material used for the production of the thick steel plate in the present invention is the melting of molten steel having the above-described composition in a converter, electric furnace, vacuum melting furnace, etc., and then ingot-bundling rolling method or continuous casting method, etc. The steel material (slab) is obtained by a generally known method.
These steel materials are heated to 1000 to 1250 ° C. prior to hot rolling. When the heating temperature is less than 1000 ° C., the deformation resistance in hot rolling is high, and the amount of reduction per pass cannot be increased. Therefore, the number of rolling passes increases, and the rolling efficiency is lowered. Sometimes casting defects cannot be crimped. On the other hand, when the heating temperature exceeds 1250 ° C., surface flaws are likely to occur due to the scale generated during heating, and the maintenance load after rolling increases.

  The heated steel material is rolled to a predetermined plate thickness by hot rolling with a rolling end temperature of 800 ° C. or higher. The hot rolling conditions other than setting the rolling end temperature to 800 ° C. or higher are not particularly limited as long as the predetermined plate thickness and shape can be satisfied. In the case of an extremely thick steel plate having a thickness exceeding 80 mm, it is desirable to secure at least one or more rolling passes with a reduction rate of 15% or more per pass in order to press-fit the zaku soot. Moreover, if rolling end temperature is less than 800 degreeC, a deformation resistance will become high too much, a rolling load will increase and the burden to a rolling mill will become large. Furthermore, in order to lower the rolling temperature of the thick material to less than 800 ° C., it is necessary to wait in the middle of rolling, which greatly hinders productivity. From the above, in the present invention, the rolling end temperature is set to 800 ° C. or higher.

The thick steel plate after rolling is required to be accelerated and cooled to a temperature range of 350 ° C. or lower because the average cooling rate is 5 to 60 ° C./s from the temperature range of the Ar ₃ transformation point or higher. If the cooling rate after rolling is less than 5 ° C / s, the area fraction of the ferrite phase and pearlite phase in the microstructure after accelerated cooling increases, and the desired microrough weave cannot be obtained, resulting in yielding. It becomes impossible to ensure a stress of 650 MPa or more. On the other hand, when the cooling rate exceeds 60 ° C./s, temperature control and uniform cooling become difficult, and the material varies depending on the steel plate position. In addition, when the cooling stop temperature of accelerated cooling is higher than 350 ° C., the area fraction of the bainite phase and the ferrite phase increases, and the area fraction of the target martensite phase cannot be set to 60% or more. As a result, a yield stress of 650 MPa or more cannot be secured. The accelerated cooling stop temperature may be room temperature or higher, but it is preferably 150 ° C. or higher in consideration of the efficiency of the subsequent reheating treatment.

  After the accelerated cooling is finished, the thick steel plate is temporarily cooled, reheated to a temperature range of 350 to 550 ° C. at a heating rate of 2 ° C./s or more, held at that temperature for 15 minutes or less, and then cooled. When the rate of temperature increase is less than 2 ° C./s, the temperature increase time to the target reheating temperature becomes long, so that productivity is lowered. Further, if the reheating temperature is less than 350 ° C., the effect of improving the base material toughness and ductility is not exhibited. On the other hand, if the reheating temperature exceeds 550 ° C., movable dislocations in the martensite phase disappear, resulting in a significant increase in yield strength, and a yield ratio of 80% or less cannot be obtained. The holding time after reheating may be a short time as long as it is heated to the target reheating temperature for the entire thickness of the steel sheet, but the holding time is set to 15 min or less in order not to impede productivity. Here, as means for reheating, there are methods such as an atmosphere heating furnace, a gas flame, induction heating, etc., but in consideration of economy, controllability, etc., induction heating is preferable. The cooling method and conditions after reheating are not particularly limited.

Using a steel material of the chemical composition, hot rolling under the above conditions, by performing accelerated cooling and reheating, at 90% or more of the regions of the plate thickness cross section, the steel plate structure is, the area fraction of martensite Is a low-yield-strength steel sheet with excellent weldability, having a base metal toughness and ductility, and having a yield stress of 650 MPa or more and a yield ratio of 80% or less. Obtainable.

Steels A to O having various component compositions shown in Table 1 were melted in a converter, adjusted by ladle refining, and made into a steel slab by a continuous casting method. Thereafter, these steel slabs were hot-rolled under the conditions shown in Table 2, acceleratedly cooled, reheated and then cooled to obtain thick steel plates having the thicknesses shown in Table 2. Test materials were sampled from the thick steel plates and subjected to the following martensite area fraction measurement, tensile test, impact test, and weld impact test.
<Measurement of martensite area fraction>
A cross section perpendicular to the rolling direction of the steel sheet (test material) is mirror-polished, dipped in a nital solution, corroded to reveal a martensite structure, and this cross-sectional structure is 1000 times larger using a scanning electron microscope. The area fraction of martensite was obtained by taking a picture at a magnification and analyzing the result.
<Tensile test>
JIS No. 4 tensile test specimens were collected from the thickness 1/2 position of each thick steel plate obtained as described above, and subjected to a tensile test in accordance with the provisions of JIS Z2241, tensile properties (yield stress YS, tensile Strength TS, elongation El) were measured. In this example, the target characteristics were yield stress YS: 650 MPa or more, yield ratio YR: 80% or less, and total elongation: 15% or more.
<Impact test>
A V-notch specimen was taken from the position of half the thickness of each steel plate in accordance with JIS Z2202, the Charpy impact test was conducted in accordance with JIS Z22242, and the absorbed energy at 0 ° C. (vE ₀ ) and the toughness of the base metal was evaluated. In this example, the number of tests was 3 each, and all targets were vE ₀ > 100 J.
<Slant y-shaped weld crack test>
From each thick steel plate, an oblique y-type weld crack test was carried out in accordance with JIS Z3158, and the root crack generation rate at 50 ° C. preheating was measured. In addition, JIS Z3212 equivalent was used for the supply wire.

The results of the above measurements are shown together in Table 2. From Table 2, all the thick steel plates of the inventive examples that meet the conditions of the present invention have a yield stress of 650 MPa or more, a yield ratio of 80% or less, a total elongation of 15% or more, and the absorbed energy vE ₀ at 0 ° C. It has a high strength of> 100 J, a low yield ratio, high ductility and high toughness, and excellent weldability without occurrence of cracks in the root portion even in the oblique y-type weld cracking test. Recognize.
On the other hand, the thick steel plate of the comparative example which deviates from the conditions of the present invention can obtain only one inferior in any one or more of the base material strength, yield ratio, ductility, base material toughness and weld cracking property. I can't.
For example, in the comparative example (No. 3) in which the cooling rate after the end of rolling is lower than the range of the present invention, the martensite phase is not generated, and the yield stress is greatly inferior to the target value. Moreover, the comparative example (No. 4) which does not perform a reheating process remarkably embrittles the martensite phase, and the target toughness cannot be obtained. Further, in the comparative example (No. 10) in which the reheating holding time is long with respect to the range of the present invention, the movable dislocation in the martensite phase disappears, resulting in an increase in yield stress, and as a result, a low yield ratio cannot be obtained. .
In the comparative example (No. 5) in which the reheating temperature is higher than the range of the present invention, the movable dislocation in the martensite phase disappears and the yield stress is high, and as a result, a low yield ratio cannot be obtained. On the other hand, the comparative example (No. 15) whose reheating temperature is lower than the range of the present invention is insufficient in improving the toughness of the martensite phase and inferior in the base material toughness.
In the comparative example (No. 7) in which the cooling stop temperature after the end of rolling is higher than the range of the present invention, the area fraction of martensite is low and the yield stress is lower than the target value. On the other hand, in the comparative example (No. 16) in which the rolling end temperature is lower than the range of the present invention, a ferrite phase is partially generated and the martensite area fraction is low, and the yield stress is also lower than the target value.
In the comparative example (No. 19) in which the C content is higher than the range of the present invention, the martensite phase is severely deteriorated in toughness and ductility, and weldability is also inferior. On the other hand, in the comparative example (No. 22) in which the amount of C is lower than the range of the present invention, since the martensite phase is not generated during the accelerated cooling, the yield stress does not reach the target value. In the comparative example (No. 20) in which C _eq and P _cm are higher than the range of the present invention, the base material toughness, ductility and weldability are inferior to the target characteristics. In the comparative example (No. 23) in which C _eq is lower than the range of the present invention, a martensite phase is not generated during accelerated cooling, and the yield stress is low. Furthermore, since the hardenability at the time of accelerated cooling is low in the comparative example (No. 21) in which the amount of Mn is lower than the range of the present invention, the area fraction of the martensite phase is low and the yield stress is lower than the target value.

  The present invention can be applied to thick steel plates used for welded steel structures such as shipbuilding, bridges, line pipes, pressure vessels, in addition to the fields of architecture and civil engineering.

Claims (4)

C: 0.03-0.2 mass%,
Si: 0.05-0.5 mass%,
Mn: 0.8-3 mass%,
P: 0.02 mass% or less,
S: 0.005 mass% or less,
Al: 0.1 mass% or less,
N: 0.007 mass% or less,
The balance consists of Fe and inevitable impurities,
Below (l) _{C eq} is 0.35～0.5Mass% defined by the equation, and the following (2) _{P cm} defined by the equation is not more than 0.28Mass%, ItaAtsudan surface 90% In the above regions, the martensite phase area fraction is 60% or more, the balance is a bainite phase, the yield stress YS is 650 MPa or more, the tensile strength TS is 826 MPa or more, and the yield ratio YR is 80% or less. High strength thick steel plate.
C _eq = C + Si / 24 + Mn / 6 (1)
P _cm = C + Si / 30 + Mn / 20 (2)
Here, C, Si, Mn: content of each element (mass%) In addition to the above component composition, Cu: 0.1 to 1 mass%, Ni: 0.1 to 1 mass%, Cr: 1 mass% or less, Mo: 1 mass% or less, Nb: 0.1 mass% or less, V: 0.00. 1 mass% or less, Ti: 0.03 mass% or less, B: 0.005 mass% or less, Ca: 0.005 mass% or less, REM: 0.02 mass% or less, and Mg: 0.005 mass% or less or comprise two or more, the _{P cm to C eq,} defined by the following equation (3) is defined by 0.35～0.50Mass% and the following equation (4) is not more than 0.28Mass% The low yield ratio high-strength thick steel plate according to claim 1,
C _eq = C + Si / 24 + Mn / 6 + Ni / 40 + Cr / 5 + Mo / 4 + V / 14 (3)
P _cm = C + Si / 30 + (Mn + Cu + Cr) / 20 + Ni / 60 + Mo / 15 + V / 10 + 5 × B (4)
Here, C, Si, Mn, Cu, Cr, Ni, Mo, V, B: Content of each element (mass%) C: 0.03-0.2 mass%,
Si: 0.05-0.5 mass%,
Mn: 0.8-3 mass%,
P: 0.02 mass% or less,
S: 0.005 mass% or less,
Al: 0.1 mass% or less,
N: 0.007 mass% or less, the balance being Fe and inevitable impurities, C _eq defined by the following formula (1) is 0.35 to 0.5 mass%, and the following formula (2) A steel slab having a defined P _cm of 0.28 mass% or less is heated to 1000 to 1250 ° C., then hot-rolled to a rolling end temperature of 800 ° C. or higher, and a cooling rate of 5 from a temperature range of Ar ₃ transformation point or higher. Accelerated cooling to a temperature range of 350 ° C. or lower at ˜60 ° C./s, once cooling is interrupted, and then reheated to a temperature of 350 to 550 ° C. at a temperature rising rate of 2 ° C./s or higher, and the temperature is reduced to 15 minutes or less. A method of manufacturing a low yield ratio high strength thick steel sheet having a yield stress YS of 650 MPa or more, a tensile strength TS of 826 MPa or more, and a yield ratio YR of 80% or less.
C _eq = C + Si / 24 + Mn / 6 (1)
P _cm = C + Si / 30 + Mn / 20 (2)
Here, C, Si, Mn: content of each element (mass%) In addition to the above component composition, Cu: 0.1 to 1 mass%, Ni: 0.1 to 1 mass%, Cr: 1 mass% or less, Mo: 1 mass% or less, Nb: 0.1 mass% or less, V: 0.00. 1 mass% or less, Ti: 0.03 mass% or less, B: 0.005 mass% or less, Ca: 0.005 mass% or less, REM: 0.02 mass% or less, and Mg: 0.005 mass% or less or comprise two or more, the _{P cm to C eq,} defined by the following equation (3) is defined by 0.35～0.50Mass% and the following equation (4) is not more than 0.28Mass% The method for producing a low yield ratio high strength thick steel plate according to claim 3.
C _eq = C + Si / 24 + Mn / 6 + Ni / 40 + Cr / 5 + Mo / 4 + V / 14
... (3)
P _cm = C + Si / 30 + (Mn + Cu + Cr) / 20 + Ni / 60 + Mo / 15 + V / 10 + 5 × B (4)
Here, C, Si, Mn, Cu, Cr, Ni, Mo, V, B: Content of each element (mass%)