JP2001342538A - High tensile steel with low yield ratio, excellent in weldability and low temperature toughness, and production of the same - Google Patents

Abstract

PROBLEM TO BE SOLVED: To provide a high tensile steel with a low yield ratio, excellent in weldability and low temperature toughness for buildings or tanks holding various kinds of liquified gases wherein earthquake-proof properties are required, and provide a production method of the same. SOLUTION: The steel structure at the position of 1/4 thickness in a cross section of the sheet thickness direction, contains martensite or martensite- austenite mixture phase with the area ratio of observed section of 1-10%, wherein 90% or above of each size of this phase has the equivalent circular radius of 3 μm or below and the yield point does not appear in the tension test. For this purpose, the composition is controlled (arranged) to be C: 0.03-0.15%, Si: 0.40% or below, Mn: 1.0-2.0%, P: 0.02% or below, S: 0.01% or below, Nb: 0.005-0.05%, Ti: 0.005-0.025%, Al: 0.06% or below, N: 0.001-0.005%, and PCM: 0.25% or below by mass %..

Description

DETAILED DESCRIPTION OF THE INVENTION

[0001]

BACKGROUND OF THE INVENTION The present invention relates to a construction steel which is required to have high toughness and a low yield ratio from the viewpoint of seismic resistance, and a steel for various tanks. The present invention relates to a high-strength steel requiring low-temperature toughness and a low yield ratio at the same time as the corresponding composite properties, and a method for producing the same.

[0002]

2. Description of the Related Art With the shift from elastic design (allowable stress design) to ultimate strength design based on a new seismic design standard implemented in June 1981, low yield ratios are required for building steel materials. I have. In order to achieve a low yield ratio, generally, a dual phase (dual phase) of the steel structure is formed, that is, a soft phase (usually ferrite) that controls yield and a hard phase (pearlite, bainite) for securing tensile strength. , Martensite, etc.) are widely used. Specifically, the steel after hot rolling or quenching, including controlled rolling, is reheated to the two-phase temperature of ferrite and austenite to form austenite in which ferrite and C are concentrated, and then air-cooled. Japanese Patent Laid-Open No. 2-266378 discloses a method of cooling at the above-described cooling speed (and further tempering thereafter).
No., for example. At this time,
The higher the C content, the easier the two-phase organization becomes,
The hard phase is more hardened, and the yield ratio can be easily reduced. However, there is a problem that increasing the C content is disadvantageous for weldability and low-temperature toughness. On the other hand, in order to improve low-temperature toughness, low C and controlled rolling are effective, but since the yield ratio increases in both cases, improvement in low-temperature toughness and low yield ratio are incompatible with each other. It was extremely difficult. Conventionally, in building applications, the required level of toughness is low, and high C, which is advantageous for lowering the yield ratio
Although there was no particular problem with steel, the demands for seismic performance in recent years following the Great Hanshin Earthquake have been increasing.
There was a problem that it was not always possible to respond sufficiently.

[0003] Further, in the steel material used for the tank for the liquefied gas storage tank, the liquefaction temperature of the gas is generally low at normal pressure (-48 in the case of LPG, though it depends on the type of liquefied gas).
° C), excellent low-temperature toughness is required not only in the base material but also in the welded joint. In contrast, Japanese Patent Application Laid-Open
Japanese Patent Application Laid-Open No. 290246/1990 discloses a method of adding 6.5 to 12.0% Ni, and Japanese Patent Application Laid-Open No. 58-153730 discloses a method of quenching and tempering a steel having a specific composition to provide tempered martensite and bainite. A method utilizing toughness is disclosed. On the other hand, liquid ammonia is known to cause stress corrosion cracking (SCC) of steel, and IGC C
ODE 17.13 (International C
ode for the construction
and Equipment of Ships Ca
rrying LiquidifiedGames in
Bulk) regulates operating conditions during storage, such as oxygen partial pressure and temperature, and restricts the Ni content of steel to 5% or less and the actual yield strength to 440 N / mm ² or less. Stipulates. For this reason, Japanese Unexamined Patent Publication No.
No. 7613 discloses a steel sheet in which only the surface layer is softened, and Japanese Unexamined Patent Publication No. 57-139493 discloses a tank manufacturing method using mild steel clad steel and a soft welding final layer.

However, the tank in which the LPG and the liquid ammonia are mixed must naturally satisfy the specifications required for both. On the other hand, large-capacity tanks and high-tension tanks of this type, which are often mounted on ships, are required to have high tensile strength, and are subject to superior low-temperature toughness from LPG and the upper limit of yield strength from liquid ammonia. At the same time, achieving a low yield ratio at the same time has been a major issue.

[0005] Furthermore, martensite or a martensite-austenite mixed phase (MA consitite)
is harmful to low-temperature toughness because it is hard and brittle, and it is generally accepted that steel components and production conditions are limited so as not to be formed as much as possible, or when formed, they are decomposed by heat treatment such as tempering. And aggressively martensite or a martensite-austenite mixed phase (M
-A constituents) were not used. The martensite or martensite-austenite mixed phase (M-Ac) defined in the present invention.
The term “instruments” is also referred to as island-like martensite or M *, and the appearance method (etching method) for identifying its phase (structure) will be described later.

[0006]

DISCLOSURE OF THE INVENTION The present invention aims at achieving excellent weldability and low-temperature toughness as well as high strength and a low yield ratio.
Martensite or martensite-austenite mixed phase (MA constituent) in steel structure
s) The present invention provides a low-yield-ratio high-strength steel excellent in weldability and low-temperature toughness, which limits the form of existence such as the structure fraction and size and prevents a yield point from appearing in a tensile test, and a method for producing the same. Make it an issue.

[0007]

Means for Solving the Problems The present inventors have proposed a martensite or martensite-austenite mixed phase (MA composition) which has been regarded as detrimental to toughness.
nts), it is found that the yield ratio can be reduced by defining the existence form such as the fraction and size and preventing the yield point from appearing during the tensile test.
b, a steel having a specific composition, controlled rolling-accelerated cooling to refine the structure by securing the strength and toughness, and stopping the accelerated cooling at a relatively low temperature to obtain martensite or martensite- The invention of a low-yield-ratio high-strength steel excellent in weldability and low-temperature toughness has been completed based on fine generation of austenite mixed phase (MA-constituents).

According to the present invention, it is possible to supply a large amount and inexpensively of steel for construction having excellent seismic resistance and steel having both low temperature toughness and a low yield ratio for a mixed tank of liquid ammonia and LPG. Since high strength can be achieved, the tank can be easily mounted on a ship.

The gist of the present invention is as follows.

(1) The steel structure at the 1/4 thickness position in the cross section in the thickness direction contains 1 to 10% of martensite or a martensite-austenite mixed phase (MA-constituents) in an area fraction of an observed cross section, A low yield ratio high tensile strength steel excellent in weldability and low temperature toughness characterized in that 90% or more of the individual sizes of the phase have an equivalent circle diameter of 3 μm or less and no yield point is obtained in a tensile test.

(2) Steel component in mass%, C: 0.03
0.15%, Si: 0.4% or less, Mn: 1.0-
2.0%, P: 0.02% or less, S: 0.01% or less,
Nb: 0.005 to 0.05%, Ti: 0.005 to
0.025%, Al: 0.06% or less, N: 0.001
0.005%, and the following (1) is not more than 0.25% P _CM weldability index as defined in formula, the balance being composed of iron and unavoidable impurities (1) above, wherein Low yield ratio high tensile strength steel with excellent weldability and low temperature toughness. _{P CM = C + Si / 30} + Mn / 20 + Cu / 20 + Ni / 60 + Cr / 20 + Mo / 15 + V / 10 + 5B · · · (1)

(3) Cu: 0.05-0.
5%, Ni: 0.05 to 1.0%, Cr: 0.05 to
0.5%, Mo: 0.05 to 0.5%, V: 0.01 to
0.05%, B: 0.0002 to 0.003%, Mg:
The low-yield-ratio high-strength steel excellent in weldability and low-temperature toughness according to the above item (2), further comprising one or more kinds in the range of 0.0002 to 0.005%.

(4) Ca: 0.0005 to 5% by mass
Excellent in weldability and low-temperature toughness according to the above item (2) or (3), further containing any one of 0.004% and REM: 0.0005 to 0.004%. Low yield ratio high tensile steel.

(5) A slab or a slab made of the steel composition according to any one of the above (2) to (4) is
After heating to a temperature of 0 to 1250 ° C. and setting the cumulative rolling reduction in the austenite non-recrystallization temperature range to 30% or more and finishing hot rolling at a temperature of 720 points or more, accelerated cooling is started from a temperature of 680 ° C. or more (1) characterized in that the accelerated cooling is stopped at a temperature of 150 to 350 ° C., and then the mixture is allowed to cool.
A method for producing a low-yield-ratio high-strength steel excellent in weldability and low-temperature toughness described in the paragraph.

[0015]

BEST MODE FOR CARRYING OUT THE INVENTION Hereinafter, the present invention will be described in detail.

The reason why the present invention has limited the steel structure, the steel composition and the manufacturing method as set forth in the claims will be described.

[0017] The steel structure is characterized in that it contains martensite or a martensite-austenite mixed phase (MA-constituents) in an area fraction of 1 to 10% at an area fraction of the observed cross section at a 1/4 thickness position in the cross section in the thickness direction. One component. This martensite or a martensite-austenite mixed phase (MA-constiti)
ents) has a high dislocation density and is a very hard phase enriched with C. Due to the presence of this phase, dislocations start to move at a low stress during a tensile test, and there is no yield point on the stress-strain curve. Draw a round curve. Martensite or martensite-austenite mixed phase (M-Ac)
Even when the structural fraction of the components is within the above-mentioned limited range, a yield point may appear depending on the structure of the matrix (for example, a ferrite structure). One. This is, specifically, in the tensile test, the load-
It means that the elongation curve draws a round curve, and it is essential that a yield point does not appear in order to achieve both high tension and low yield ratio. In a round load-elongation curve with no yield point, a yield strength of 0.2% proof stress is generally adopted, and the yield strength is lower when compared with steel of the same tensile strength that yields a yield point. And, as a result, the yield ratio also decreases.

Defining the structure of the matrix as a condition for not producing a yield point in a tensile test also depends on the hardness and constituent fraction of martensite or a martensite-austenite mixed phase (MA-constituents). Not only can't say in general,
For reasons such as ambiguous descriptions of those organizations (it is impossible to accurately describe a wide variety of organizations)
It was determined that it was inappropriate as a component of the invention.

Martensite or a martensite-austenite mixed phase (MA constituent)
The lower limit 1% of the constituent fraction (area fraction of the observed cross section) of s) is
The minimum amount required for the dislocation to start moving with low stress during the tensile test, and the upper limit of 10% is a limit amount that does not deteriorate the toughness more than necessary. However, from the viewpoint of low-temperature toughness, it is not sufficient to limit the constituent fraction (area fraction of the observed cross section) of martensite or a martensite-austenite mixed phase (M-A constituents) as described above.

In the case where a large unit (size) exists in the form of a block, it acts as a fracture starting point and toughness is deteriorated. 90% or more of the individual sizes of the austenitic mixed phases (MA-constituents) were limited to 3 μm or less in circle equivalent diameter. These numerical values are based on the experimental facts of the inventors.

Incidentally, martensite or a martensite-austenite mixed phase (M-Aconstite) is used.
nts) is an etching method developed by LePera (Journal o).
f Metals, March, 1980, p. 38)
Is most suitable, and this etching causes the martensite or martensite-austenite mixed phase (M-Aconstituents) to appear white.

Next, in order to obtain the limited martensite or martensite-austenite mixed phase (MA-constituents) as in the present invention, and to prevent the yield point from appearing in the tensile test, the optimum steel component is used. Will be described.

C is the most remarkable effect on the properties of steel.
The lower limit of 0.03% is a minimum amount for ensuring strength and preventing the heat-affected zone such as welding from softening more than necessary. However, if the C content is too large, the hardenability increases more than necessary, and the steel material has an adverse effect on the inherent strength, toughness balance, weldability, etc., so the upper limit was made 0.15%.

Si is an element contained in the deoxidized steel,
If a large amount is added, the weldability and the HAZ toughness deteriorate, so the upper limit is limited to 0.4%. Deoxidation of steel is sufficiently possible only with Ti and Al, and the lower the better, from the viewpoint of HAZ toughness, hardenability and the like, the more preferable, and it is not always necessary to add.

Mn is an element indispensable for securing strength and toughness, and its lower limit is 1.0%. However, Mn
If the amount is too large, the hardenability increases and not only deteriorates the weldability and HAZ toughness, but also promotes the center segregation of the continuous cast slab, so the upper limit was made 2.0%.

P is an impurity in the steel of the present invention.
Since a reduction in the amount tends to reduce grain boundary fracture in the HAZ, a smaller amount is preferable. If the content is high, the base material,
The upper limit is set to 0.02% in order to deteriorate the low-temperature toughness of the weld.

S, like P, is an impurity in the steel of the present invention, and is preferably as small as possible from the viewpoint of the low-temperature toughness of the base material. If the content is large, the low-temperature toughness of the base material and the welded portion is deteriorated, so the upper limit was made 0.01%.

Nb is an essential element for increasing the unrecrystallization temperature of austenite and maximizing the effect of the controlled rolling during hot rolling, and at least 0.005% of Nb is required. It also contributes to the refinement of heated austenite during quenching. Further, it has an effect of improving strength as precipitation hardening. However, excessive addition causes toughness degradation of the welded portion, so the upper limit was made 0.05%.

[0029] Ti is essential for improving the base material and HAZ toughness. Because, when the amount of Al is small (for example, 0.003% or less), Ti combines with O to form a precipitate containing Ti ₂ O ₃ as a main component, becomes a nucleus for the formation of intragranular transformed ferrite, and improves the HAZ toughness. Let it. Further, Ti is combined with N and finely precipitated as TiN in the slab, and γ during heating is obtained.
This is because it suppresses coarsening of the grains and is effective in reducing the grain size of the rolled structure, and the fine TiN present in the steel sheet refines the HAZ structure during welding. To get these effects,
Ti must be at least 0.005%. However, if too much, TiC is formed and the low-temperature toughness and weldability are deteriorated.
The upper limit is 0.025%.

Al is an element generally contained in the deoxidized upper steel, but the deoxidation is sufficient with only Si or Ti, and the lower limit is not limited in the steel of the present invention. But A
When the amount of l increases, not only does the cleanliness of the steel deteriorate, but also the toughness of the weld metal deteriorates, so the upper limit was made 0.06%.

N is contained in steel as an unavoidable impurity, but combines with Nb to form a carbonitride to increase the strength, and forms TiN to form a steel as described above. Enhance the nature. Therefore, the amount of N is at least 0.001.
%is necessary. However, an increase in the amount of N is extremely harmful to HAZ toughness and weldability, and the upper limit of the steel of the present invention is 0.005%.

Next, C which can be optionally contained
The reason for adding u, Ni, Cr, Mo, V, B, and Mg will be described.

The main purpose of adding these elements to the basic components is to improve properties such as strength and toughness without impairing the excellent characteristics of the steel of the present invention. Therefore, the amount added is of a nature that should be naturally restricted.

Cu exhibits almost the same effects and phenomena as Ni. The upper limit of 0.5% is not only deteriorated in weldability, but excessive addition is restricted because Cu-cracks are generated during hot rolling and production becomes difficult. You. The lower limit should be 0.05%, which should be the minimum for a substantial effect to be obtained. This is C
The same applies to r and Mo.

If Ni is not added excessively, weldability, H
Improves the strength and toughness of the base material without adversely affecting AZ toughness. In order to exert these effects, it is essential to add at least 0.05% or more. On the other hand, excessive addition is not only expensive but also unfavorable for weldability. In addition, it has been pointed out that adding a large amount of Ni may induce stress corrosion cracking (SCC) in liquid ammonia. According to the experiments of the inventors, the addition of up to 1% does not significantly deteriorate the weldability and SCC in liquid ammonia, and has a greater effect of improving the strength and toughness. Therefore, the upper limit is set to 1.0%.

Cr and Mo are added in an amount of 0.05% or more to improve both the strength and toughness of the base material. However, if the addition amount is too large, the toughness and weldability of the base metal and the welded portion are deteriorated, and the control of the structure described later becomes difficult, which is not preferable.

V has almost the same effect as Nb, but its effect is smaller than that of Nb. Further, V also affects the hardenability, and is added from the viewpoint of controlling the structure as in the case of the above-mentioned elements. The effect similar to Nb is 0.
If it is less than 01%, the effect is small, and the upper limit can be tolerated up to 0.05%.

B segregates at austenite grain boundaries and suppresses the formation of ferrite, thereby improving hardenability and contributing to strength improvement. To enjoy this effect, at least 0.0002% is required. However, too much addition not only saturates the effect of improving hardenability but also may form B precipitates that are harmful to toughness, so the upper limit was made 0.003%. In addition, in cases where stress corrosion cracking is a concern as steel for tanks, reduction of the hardness of the base metal and the weld heat affected zone is often the point (for example, to prevent sulfide stress corrosion cracking (SCC)). HR for
C ≦ 22 (HV ≦ 248) is essential. In such a case, the addition of B which increases the hardenability is not preferable.

Mg has the effect of suppressing the growth of austenite grains in the heat affected zone and reducing the size of the austenitic grains, thereby toughening the welded portion. In order to enjoy such effects, Mg needs to be 0.0002% or more. On the other hand, as the addition amount increases, the effect cost on the addition amount decreases,
The upper limit is set to 0.005% because it is not advantageous in terms of cost.

Furthermore, Ca and REM control the morphology of MnS, improve the low-temperature toughness of the base material, and also cause hydrogen-induced cracking (HIC, SSC, SOC) in a wet hydrogen sulfide environment.
HIC) reduces susceptibility. In order to exhibit these effects, at least 0.0005% is required. But,
Too much addition will increase the cleanliness of the steel, adversely affect base metal toughness and hydrogen-induced cracking (HIC, SSC,
(SOHIC) In order to increase the sensitivity, the upper limit of the amount added is 0.
004%. Since Ca and REM have almost the same effect, one of them may be added in the above range.

Even if the individual components of the steel are limited, excellent properties cannot be obtained unless the entire component system is appropriate. Thus, limiting the value of P _CM shown in the following equation (1) below 0.25%. _{P CM = C + Si / 30} + Mn / 20 + Cu / 20 + Ni / 60 + Cr / 20 + Mo / 15 + V / 10 + 5B · · · (1) P CM is an indicator representing the weldability, the lower the weldability is good. In the present invention steel, as long as P _CM is 0.25% or less, it is possible to ensure excellent weldability.

While ensuring excellent weldability and low-temperature toughness, in the tensile test as described above, the load-elongation curve draws a round curve and does not produce a yield point. It is extremely effective to do so.
Hereinafter, the reason will be described.

The heating temperature prior to rolling is 1000 to 125
The reason for limiting the temperature to 0 ° C. is to keep the austenite grains small during heating and to make the rolling structure finer. 125
0 ° C. is an upper limit temperature at which austenite during heating does not become extremely coarse. If the heating temperature exceeds this temperature, austenite grains are coarsely mixed and the structure after transformation is also coarse, so that the toughness of steel is significantly deteriorated. On the other hand, if the heating temperature is too low, it is difficult not only to secure a rolling end temperature (Ar ₃ point or more) described later, but also to raise the austenite non-recrystallization temperature, thereby reducing the effect of controlled rolling during hot rolling. The lower limit was set to 1000 ° C. from the viewpoint of solutionizing Nb to maximize its effect and to develop precipitation hardening.

The slab or slab heated under the above conditions is subjected to a cumulative rolling reduction of 30% or more in the austenite non-recrystallization temperature range, and after completion of hot rolling at 720 ° C. or more, 680 ° C. or more. Accelerated cooling from the temperature of

By performing rolling in the austenite non-recrystallization temperature range, austenite grains are remarkably refined, so that at least a 30% or more cumulative rolling reduction is required. If the rolling end temperature is lower than 720 ° C., the ferrite transforms and precipitates, and the ferrite may be processed (rolled), which is not preferable in terms of lowering the yield ratio and ensuring low-temperature toughness. For this reason, the rolling end temperature is limited to 720 ° C. or higher.

After the completion of hot rolling at 720 ° C. or higher, 6
The reason why the accelerated cooling is started from a temperature of 80 ° C. or higher is to make the structure finer by increasing the cooling speed in the transformation region and simultaneously improve the strength and toughness. Further, the refinement of the structure is indispensable for finely forming the martensite-austenite mixed phase (MA-constituents) as the C-enriched phase as in the present invention. The organization is 68
When the temperature is lower than 0 ° C., coarse ferrite starts to precipitate, and the strength is reduced and the toughness is deteriorated. This accelerated cooling must stop at a temperature of 150-350 ° C. At a temperature higher than 350 ° C., the cooling after stopping the accelerated cooling is substantially tempering, and the strength is reduced, and the martensite-austenite mixed phase (MA-constituents) is decomposed, so that the yield point is obtained. And a low yield ratio cannot be achieved. On the other hand, when the accelerated cooling stop temperature is lower than 150 ° C., in addition to a high possibility that a martensite-austenite mixed phase (MA-constituents) is generated more than necessary, softening due to heat influences such as welding and gas cutting occurs. It is not preferable in use performance because it becomes remarkable. For this reason, the lower limit temperature of the accelerated cooling stop temperature was set to 150 ° C.

The cooling rate during accelerated cooling cannot be unconditionally determined because it varies depending on the steel composition, the intended yield ratio, and the low-temperature toughness level. It is desirable that the average cooling rate is up to at least 3 ° C./sec.

[0048]

EXAMPLES Examples of the present invention will be described together with comparative examples.

In the converter-continuous casting-thick plate process, steel plates of various steel components (thickness 15 to 80 mm) are manufactured, and their strength, yield ratio (YR), toughness and weldability (oblique y-shaped weld cracking test) )investigated.

Table 1 shows the steel composition of the steel of the present invention together with the comparative steel, and Table 2 shows the manufacturing conditions and various characteristics of the steel sheet.

[0051]

[Table 1]

[0052]

[Table 2]

The steel sheets manufactured according to the method of the present invention (steel of the present invention) all have good properties. On the other hand, the comparative steel not according to the present invention is inferior in any of the properties.

The comparative steel 11 has a low C content, and has Nb, T
In addition to the fact that i is not added, the accumulated rolling reduction in the γ non-recrystallization temperature range is small, so that the weldability is good but the strength is low and the toughness is poor. Although the comparative steel 12 is within the scope of the present invention in terms of composition, since the water cooling stop temperature is high, martensite or a martensite-austenite mixed phase (MA-constituents) is not generated, and as a result, a yield point appears. And the yield strength is high, and the yield ratio is high. Comparative Steel 13, although the addition amount of each element is within the scope of the present invention, inferior in weldability due to high P _CM. In addition, coarse martensite or a martensite-austenite mixed phase (M-Aconstiti)
ents) is high and inferior in toughness. The comparative steel 14 has a high Ti content, a low rolling temperature under manufacturing conditions, and a low water-cooling start temperature, so that a yield point appears, both the yield strength and the yield ratio are high, and the low-temperature toughness is poor. In addition, the comparative steel 1 with a high Ti content
In No. 4, HAZ toughness was also confirmed to be inferior, which is not preferable in terms of use performance. Comparative Steel 15 has a high C content, P _CM
Is high, the weldability is inferior, and the accelerated cooling stop temperature is low, so that coarse martensite or a martensite-austenite mixed phase (MA-constite)
The nts) fraction is high, and the ratio of coarse ones is high, so that the toughness is poor. Further, it has been confirmed that the comparative steel 15 having a low accelerated cooling stop temperature has remarkable HAZ softening during welding, which is not preferable in terms of use performance.

[0055]

According to the present invention, it has become possible to produce a low-yield-ratio high-tensile steel excellent in weldability and low-temperature toughness. as a result,
For building with excellent seismic performance, or liquid ammonia and L
It has become possible to supply inexpensively a large amount of steel having excellent weldability for use in a tank mixed with PG or the like. In particular, since the strength can be increased, the tank can be easily mounted on a ship.

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Claims (5)

[Claims] 1. A steel structure at a 1/4 thickness position in a cross section in the thickness direction,
The martensite or martensite-austenite mixed phase (MA constituents) contains 1 to 10% by area fraction of the observed cross section, and 90% or more of the individual sizes of the phase have a circle equivalent diameter of 3 µm or less; Low yield ratio high tensile strength steel with excellent weldability and low temperature toughness characterized by no yield point in tensile test. 2. The steel component in mass%, C: 0.03-0.
15%, Si: 0.4% or less, Mn: 1.0 to 2.0
%, P: 0.02% or less, S: 0.01% or less, Nb:
0.005 to 0.05%, Ti: 0.005 to 0.02
5%, Al: 0.06% or less, N: 0.001 to 0.0
05% and the weldability index P defined by the following equation (1)
_The low yield ratio high tensile strength steel having excellent weldability and low temperature toughness according to claim 1, characterized in that _CM is 0.25% or less and the balance consists of iron and unavoidable impurities. _{P CM = C + Si / 30} + Mn / 20 + Cu / 20 + Ni / 60 + Cr / 20 + Mo / 15 + V / 10 + 5B · · · (1) 3. Cu: 0.05 to 0.5% by mass%;
Ni: 0.05 to 1.0%, Cr: 0.05 to 0.5
%, Mo: 0.05 to 0.5%, V: 0.01 to 0.0
5%, B: 0.0002 to 0.003%, Mg: 0.0
The low-yield-ratio high-tensile steel having excellent weldability and low-temperature toughness according to claim 2, further comprising one or more kinds in the range of 002 to 0.005%. 4. Ca: 0.0005 to 0.0% by mass
The low-yield-ratio high-tensile steel having excellent weldability and low-temperature toughness according to claim 2 or 3, further comprising any one of 0.4% and REM: 0.0005 to 0.004%. 5. A slab or a slab made of the steel composition according to any one of claims 2 to 4, which is subjected to a temperature of 1000 to 1250 ° C.
After the hot rolling is completed at a temperature of 720 points or more with the cumulative reduction in the austenite non-recrystallization temperature range being 30% or more, accelerated cooling is started from a temperature of 680 ° C. or more. The method according to claim 1, wherein the accelerated cooling is stopped at a temperature of 350 ° C, and then the steel is allowed to cool.