KR20050082417A - High-strength steel plate and method for manufacturing the same - Google Patents

Abstract

Provided is a high strength steel sheet having a tensile strength of 750 MPa or more, having excellent low temperature toughness even in a cryogenic environment of -46 ° C, and excellent in low temperature toughness of a welded part, and a method of manufacturing the same.

High strength steel sheet of the present invention is C: 0.01 to 0.10%, Si: 0.30% or less, Mn: 1.20 to 2.50%, P: 0.010% or less, S: 0.002% or less, Ni: 0.2 to 1.5%, Mo: 0.1 to 0.8 %, Nb: 0.005 to 0.06%, Ti: 0.004 to 0.025%, sol.Al: 0.05% or less, N: 0.0050% or less and O (oxygen): 0.003% or less, or further Cr, Cu, V, B , Ca, Mg, Zr, and REM contain a predetermined amount of one or more, the remainder is Fe and impurities, and the following formula (1) (the element symbol in the formula means the content of each element contained in steel) The A value represented by is made of steel of 0.5% or less, and the half width of the X-ray diffraction intensity from the (110) plane is 0.18 degrees or more, or further has a predetermined metal structure, and the tensile strength is 750 MPa. That's it.

A = 12P + 45S + 67 (N + O) ... (1)

Description

High-strength steel plate and method for manufacturing the same

The present invention is excellent in cryogenic toughness, has a tensile strength of 750 MPa or more, and relates to a preferred high strength steel sheet used in a line pipe or various pressure vessels for transporting natural gas or crude oil, and a manufacturing method thereof.

In pipelines that transport natural gas or crude oil over long distances, there is an increasing demand for restricting the increase in wall thickness by increasing the strength of the pipe material itself in order to reduce laying costs and transportation costs. Currently, in the American Petroleum Institute (API), X80 grade (tensile strength of 620 MPa or more) is standardized and practically used, and X100 (tensile strength of 750 MPa or more) and higher than X100 (for example, tensile strength of more than 100) are used. The application of the high strength grade steel of 900 Mpa or more of tensile strength is also examined.

On the other hand, in a line pipe, it is important to have both strength characteristics and base material low temperature toughness among the required characteristics to be provided as a structural material. In particular, when laying in extreme cold, the low temperature toughness of a base material is extremely important, and there exists a possibility that a pipeline may be destroyed if this low temperature toughness is not enough. In general, however, toughness deteriorates when increasing the strength characteristics, whereas strength is insufficient when trying to increase the toughness. Therefore, it is difficult to satisfy these two characteristics, and it is necessary for steel materials to have fine crystal grains.

In order to meet such a request for high strength and excellent low temperature toughness, for example, Japanese Patent Application Laid-Open No. 8-199292 and Japanese Patent Application Laid-Open No. 2000-199036 include low temperature toughness of X100 grade with a higher Mn content. This outstanding high strength steel and high strength line pipe and its manufacturing method are proposed.

Further, Japanese Patent Laid-Open No. 2002-220634 discloses a high-strength steel having a tensile strength of 600 MPa or more excellent in deformation resistance characteristics and a desired low temperature toughness and a method of manufacturing the same. Based on the evaluation of the fracture characteristics in the real pipe by the DWTT test specified in the API, in particular, in the recognition that a high strength line pipe of grade X100 or higher is required to be evaluated by a fracture test using a test piece of a steel pipe full thickness. A high strength steel having excellent unstable fracture resistance is disclosed.

However, in the techniques described in Japanese Patent Application Laid-Open No. 8-199292, Japanese Patent Application Laid-Open No. 2000-199036, and Japanese Patent Application Laid-Open No. 2002-220634, low-temperature toughness is only evaluated in the Charpy impact test. In addition, the DWTT test described in Japanese Patent Laid-Open No. 2003-3233 is only performed at -30 ° C, and the toughness in cryogenic environments such as -40 ° C to -50 ° C expected in extreme cold is examined. It is not.

The present invention has been made in view of the above circumstances, and its object is to have a tensile strength of 750 MPa or more and to have excellent low temperature toughness even in a cryogenic environment at -46 ° C (-50F), and also to absorb energy of a welded joint. The present invention provides a high strength steel sheet excellent in welded low-temperature toughness and a method for producing the same, which is 80 J or more under the same environment.

Specifically, an object of the present invention is to provide a high strength steel sheet having all of the following performances and a method of manufacturing the same.

Base material strength: Tensile strength (TS)

Base metal toughness: impact absorption energy _(v E _{-46 ℃)} ≥200J

Base material toughness: Soft surface fracture rate (SA _{-46 ° C} ) ≥ 75% by DWTT test

Weld Seam Toughness: Shock Absorption Energy ( _v E _{-46 ℃} ) ≥80J

MEANS TO SOLVE THE PROBLEM This inventor discovered the following as a result of repeating experimental examination in order to achieve the said subject.

Generally, in order to achieve high strength and high toughness, it is well known that the structure of the steel is made of bainite, martensite, or a mixed structure thereof. Is not enough. However, by miniaturizing the developed dislocation undercarriage formed during hot working and inheriting them to bainite and martensite structures, it is possible to suppress the occurrence of breakage at low temperatures and to stop breakage propagation (these performances are In particular, it has been found that the "breakdown suppression characteristics" and "breakdown propagation stop characteristics" are particularly improved.

In addition, it is extremely effective to limit the total amount of P, S, N, and O (oxygen) in the base material for miniaturization of dislocation understructure, and it is developed finely by a combination of appropriate hot rolling and post-rolling treatment (cooling conditions, etc.). In order to obtain bainite, martensite, or a mixed structure having one dislocation substructure, and to achieve high strength and low temperature toughness, X from the (110) plane in the steel of the chemical composition of the high strength steel sheet of the present invention described later It has been found that this is made possible by controlling the half width of the line diffraction intensity. Moreover, it was confirmed that the restriction | limiting of the total amount of P, S, N, and O is effective also in refinement | miniaturization of the weld heat influence part of this high strength steel.

The term "potential substructure" as used herein refers to a tissue by dislocations or the like introduced into the tissue by hot working or the like, and "finely developed dislocation substructure" is a fine subgrain or a cell-like structure in which the angle of neighboring subgrains is 0.5. The above-mentioned tissue is called. In other words, a large amount of dislocation is introduced into the austenite by hot working, but a large amount of dislocation introduced by the appropriate base material component and the processing after hot working and rolling forms fine subgrains and the like, and the subgrain and the like are cooled. It remains in the tissue after metamorphosis by, and contributes to the improvement of toughness of steel.

Such finely developed dislocation substructures that contribute to the improvement of the toughness of high strength steel cannot be obtained only by producing conventional materials by conventional methods. In order to obtain this structure, it is necessary to satisfy the following conditions (a), (b) and (c) simultaneously.

(a) The total ratio of martensite phase and bainite phase in the metal structure of the surface layer portion and the wall thickness center is 95 vol% or more and 80 vol% or more, respectively.

(b) Limit the total amount of P, S, N and O in the base material. In other words, the A value of the following formula (1) is limited to 0.5% or less. In addition, the element symbol in (1) formula means content (mass%) of each element contained in steel in all.

A = 12P + 45S + 67 (N + O) ... (1)

(c) The half width of the X-ray diffraction intensity from the (110) plane is 0.18 degrees or more, preferably 0.22 degrees or more, more preferably 0.25 degrees or more.

By satisfy | filling these conditions, in a base material, the high intensity | strength of 750 Mpa or more, the outstanding Charpy impact characteristic and DWTT characteristic in -46 degreeC can be made compatible.

This invention was made based on the said knowledge, The summary is the manufacturing method of the high strength steel plate of (1) and (2), the high strength welded steel pipe of (3), and (4).

(1) In mass%, C: 0.01 to 0.10%, Si: 0.30% or less, Mn: 1.20 to 2.50%, P: 0.01% or less, S: 0.002% or less, Ni: 0.2 to 1.5%, Mo: 0.1 to 0.8%, Nb: 0.005 to 0.06%, Ti: 0.004 to 0.025%, sol.Al: 0.05% or less, N: 0.0050% or less, and O (oxygen): 0003% or less, or, further Contains components of the group or / and the second group,

One or more of the components of the first group: Cr: 1.0% or less, Cu: 0.1 to 1.5%, V: 0.1% or less, and B: 0.0030% or less

Component of the second group.Ca: 0.01% or less, Mg: 0.01% or less, Zr: 0.01% or less and REM: 0.05% or less

Remainder is Fe and an impurity, A value represented by following formula (1) consists of steel of 0.5% or less, The half width of the X-ray-diffraction intensity from (110) plane is 0.18 degree or more, and tensile strength High strength steel sheet having a 750 MPa or more.

A = 12P + 45S + 67 (N + O) ... (1)

Here, the element symbol in (1) formula means content (mass%) of each element contained in steel.

(2) The high strength steel sheet according to the above (1), wherein the total ratio of the martensite phase and the bainite phase in the metal structure of the surface layer portion and the wall thickness center portion is 95 vol% or more and 80 vol% or more, respectively.

(3) A high strength welded steel pipe obtained by processing the high strength steel sheet according to the above (1) or (2).

(4) In mass%, C: 0.01 to 0.10%, Si: 0.30% or less, Mn: 1.20 to 2.50%, P: 0.01% or less, S: 0.002% or less, Ni: 0.2 to 1.5%, Mo: 0.1 to 0.8%, Nb: 0.005 to 0.06%, Ti: 0.004 to 0.025%, sol.Al: 0.05% or less, N: 0.0050% or less and O (oxygen): 0.003% or less, or in addition to the above components, In addition, it contains a component of the following first group and / or second group,

1% or more of components: mass% of a 1st group in Cr: 1.0% or less, Cu: 0.1-1.5%, V: 0.1% or less, and B: 0.0030% or less

Component of the second group.Ca: 0.01% or less, Mg: 0.01% or less, Zr: 0.01% or less and REM: 0.05% or less

The remainder is Fe and impurities, and after heating the steel having an A value of 0.5% or less represented by the following formula (1) to 950 to 1200 ° C, hot rolling is performed to finish rolling at a finishing temperature of 900 to 600 ° C, and 600 ° C. The method of producing high strength steel, characterized in that the cooling is terminated after the accelerated cooling is performed at a cooling rate of 4 ° C / sec or more from a temperature range not lower than 550 ° C to a temperature of 4 ° C / sec or more, so that the recuperation temperature width is 70 ° C or less.

A = 12P + 45S + 67 (N + O) ... (1)

Here, the element symbol in (1) formula means content (mass%) of each element contained in steel.

The "half width of X-ray diffraction intensity" refers to the width of the distribution where the diffraction intensity is 1/2 of the highest intensity value in the X-ray diffraction intensity data ("diffraction intensity-angle" data). It is shown. In addition, "half width" is explained later.

In addition, "REM" is a rare earth element and refers to scandium (Sc), yttrium (Y), and lanthanide (15 elements). Content of REM is content of the sum total of the rare earth elements contained.

(The best form to carry out invention)

EMBODIMENT OF THE INVENTION Hereinafter, the reason which prescribed | regulated the high tensile strength steel plate of this invention, its manufacturing method, and a welded steel pipe as mentioned above is demonstrated in detail. In addition, below, "%" of an alloying element means "mass%."

First, the chemical composition of steel is demonstrated.

C: 0.01% to 0.10%

Although C is included for the purpose of securing strength, at a content of less than 0.01%, hardenability is insufficient, making it difficult to secure tensile strength of 750 MPa or more, and insufficient toughness. Conversely, when it contains exceeding 0.10%, the toughness of steel (base material) and a weld part, especially weld heat influence part (HAZ) falls. Moreover, the weldability at the time of welding construction also falls. For this reason, C content was made into 0.01 to 0.10%. The range is preferably 0.02% to 0.08%, and more preferably 0.03% to 0.08%.

Si: 0.30% or less

Si is usually added as a deoxidizer, but when its content exceeds 0.30%, the toughness of the steel and its welded portion decreases. For this reason, Si content was made into 0.30 or less. The upper limit is preferably 0.20% and more preferably 0.15%. On the other hand, although a minimum in particular is not prescribed | regulated, in order to acquire sufficient deoxidation effect, it is preferable to make Si content into 0.01% or more.

Mn: 1.20 to 2.50%

Although Mn is contained in order to improve hardenability and raise strength, it is difficult to ensure tensile strength of 750 MPa or more at a content of less than 1.20%. On the contrary, when it contains exceeding 2.50%, the toughness of steel and its weld part will fall. For this reason, Mn content was made into 1.20 to 2.50%. Preferable range is 1.2 to 2.2%, and more preferable range is 1.2 to 1.7%.

P: 0.010% or less

P is an impurity element, and not only lowers the low-temperature toughness of the steel and its welded portion, especially the weld heat affected portion, but also lowers the weldability. Therefore, the lower the P content is, the more preferable it is. However, unavoidable mixing is inevitable, and excessive reduction leads to an increase in cost. Therefore, the upper limit is set to 0.010% as long as no substantial harm is caused. The upper limit is preferably 0.008%, and more preferably 0.005%. On the other hand, P content needs to satisfy | fill Formula (1) mentioned later.

S: 0.002% or less

S is an impurity element similar to the above P, and not only lowers the low-temperature toughness of the steel and its welded portion, especially the weld heat affected portion, but also lowers the weldability. In this invention, reduction of the content is an essential element. In other words, in order to secure sufficient cryogenic toughness in high strength steel sheets with a tensile strength of 750 MPa or more, it is desirable to keep the S content as low as possible, but unavoidable mixing is unavoidable, and excessive reduction leads to an increase in cost, thereby causing substantial harm. As long as it does not generate | occur | produce, it was 0.002% or less. The upper limit is preferably 0.0008% and more preferably 0.0005%. In addition, S content needs to satisfy | fill Formula (1) mentioned later.

Ni: 0.2-1.5%

Ni has the effect of improving weldability in addition to improving the low temperature toughness and brittle crack propagation stopping performance of steel. These effects are obtained even at the impurity level, but become remarkable at a content of 0.2% or more. However, even if it contains more than 1.5%, not only the margin of improvement of the said effect becomes small compared with a cost increase, but excessive residual austenite is produced by quenching-tempering treatment, and yield strength may fall. For this reason, it is good to make Ni content into 0.2 to 1.5% at the time of positively adding and containing.

Mo: 0.1-0.8%

Mo improves the hardenability and improves the strength and toughness of the steel by strengthening the solid solution. In addition, the composite addition with Nb promotes the refinement of the structure, and also has the effect of dispersing suitable residual austenite in steel to improve the base metal and the welded part toughness. These effects become remarkable at a content of 0.1% or more. However, when it contains exceeding 0.8%, intensity | strength will be excessively increased and the toughness of a base material and its weld part will be impaired. For this reason, Mo content was made into 0.1 to 0.8%.

Nb: 0.005 to 0.06%

Nb is an element which refines the structure of the steel and greatly improves the toughness of the high strength steel, but the content is not obtained at a content of less than 0.005%. On the other hand, when it contains exceeding 0.06%, weldability will be impaired. For this reason, Nb content was made into 0.005 to 0.06%. The range is preferably 0.005% to 0.03%, and more preferably 0.005% to 0.02%.

Ti: 0.004-0.025%

Ti is an element that refines the structure of the steel and the weld heat affected zone and improves the low temperature toughness of the base material and the weld heat affected zone, but the above effect cannot be obtained at a content of less than 0.004%. On the other hand, when it contains exceeding 0.025%, not only the low-temperature toughness of steel and its weld part, especially the welding heat influence part, but a weldability also fall. For this reason, Ti content was made into 0.004 to 0.025%. The range is preferably 0.004% to 0.015%, and more preferably 0.004% to 0.010%.

sol.Al: 0.05% or less

Al is an element usually added as a deoxidizer, and has a function of fixing N contained as an impurity in steel as AlN, but when the content exceeds 0.05% by sol.Al content, not only the weld property deteriorates but also weldability. At the same time, the MA ratio (the ratio of island-like martensite structure) increases, and the toughness deteriorates. For this reason, content of Al was made into 0.05% or less by sol.Al content. The upper limit is preferably 0.035%, and more preferably 0.025%. On the other hand, the lower limit does not need to be particularly defined, but in order to sufficiently obtain the above effects, the sol.Al content is preferably made 0.0005% or more.

N: 0.0050% or less

N is an impurity element, which is a harmful element that lowers the toughness of steel, and when the content thereof exceeds 0.0050%, the desired low temperature toughness cannot be secured. For this reason, N content was made into 0.0050% or less. Although a preferable upper limit is 0.0025% and a more preferable upper limit is 0.0020%, the lower the N content, the better. In addition, N content needs to satisfy | fill Formula (1) mentioned later.

O (oxygen): 0.003% or less

O is an impurity element similar to the above N and is an extremely harmful element that lowers the toughness of steel. When the content exceeds 0.003%, the desired low temperature toughness cannot be secured. For this reason, O content was made into 0.003% or less. The upper limit is preferably 0.0018% and more preferably 0.0012%, but the lower the O content, the better. In addition, O content needs to satisfy | fill Formula (1) demonstrated next.

A value: 0.5% or less

Each element of P, S, N and O is suppressed to the content within the above-mentioned range, respectively, and is represented by the following formula (1) (The element symbol in a formula means content (%) of each element contained in steel) It is necessary that the A value to be 0.5% or less.

A = 12P + 45S + 67 (N + O) ... (1)

That is, in a steel material having an A value of more than 0.5%, even after performing appropriate hot rolling and post-rolling treatment (accelerated cooling described later), the fine dislocation understructure is not sufficiently introduced into the steel structure, and the welded portion is not sufficiently refined. The target high strength and high toughness cannot be obtained. For this reason, A value was made into 0.5% or less. The upper limit with preferable A value is 0.4%.

The high-strength steel sheet of the present invention is sufficient to consist of the above-described components, the balance Fe and impurities with respect to the chemical composition of the steel, but if necessary, any one or more of Cr, Cu, V, B, Ca, Mg, Zr, and REM may be used. You may positively add and contain. In this case, high strength can be obtained without damaging the low-temperature toughness and weldability of steel and its weld part, especially the welding heat influence part, and a steel plate, steel pipe, etc. of higher strength can be obtained.

Cu: 0.1-1.5%

Cu improves hardenability and has the effect of toughening steel (base material) without harming weldability so much, and the effect becomes remarkable by content of 0.1% or more. However, when it contains exceeding 1.5%, not only the toughness of a base material and its weld part may be impaired, but hot ductility may fall significantly. For this reason, Cu content in the case of adding is good to be 0.1 to 1.5%.

Cr: 1.0% or less

V: 0.1% or less

B: 0.0030% or less

All of these elements have an effect of improving hardenability and toughening steel. However, when Cr, V, and B are contained in excess of 1.0%, 0.1%, and 0.0030%, respectively, the strength increases excessively, and the toughness of the steel and the weld portion thereof may be damaged. For this reason, content of Cr, V, and B was 1.0% or less, 0.1% or less, and 0.0030% or less, respectively. The said effect is acquired also at an impurity amount level with respect to any element. Therefore, although the lower limit is not specifically defined, a remarkable effect is seen in the content of 0.01% or more in Cr, 0.005% or more in V, and 0.0003% or more in B. Therefore, the contents of Cr, V and B in the case of actively adding and containing are respectively, It is preferable to set it as 0.01 to 1.0%, 0.005 to 0.1%, and 0.0003 to 0.0030%.

Ca: 0.01% or less

Mg: 0.01% or less

Zr: 0.01% or less

REM (rare earth element): 0.05% or less

All of these elements have an action of stabilizing elements (N, C, O) harmful to low temperature toughness, in addition to controlling the form of inclusions in the steel and improving the toughness and corrosion resistance of the steel and its welded portions. However, when Ca, Mg, and Zr are all contained in an amount exceeding 0.01% and in an amount exceeding 0.05% in REM, the cleanliness of the steel decreases and the toughness of the steel and its welded portion decreases. For this reason, content of Ca, Mg, and Zr was 0.01% or less in all, and content of REM was 0.05% or less.

The said effect is acquired also at an impurity amount level with respect to any element. Therefore, although the lower limit is not specifically defined, since a remarkable effect is seen in content of 0.0005% or more in all, content of Ca, Mg, and Zr in the case of actively adding and containing is 0.0005 to 0.01%, and content of REM is 0.0005 to It is preferable to set it as 0.05%.

On the other hand, it is preferable in consideration of weldability and cleanliness of Steel, that the carbon equivalent C _eq and V _s shown below into, respectively from 0.40 to 0.58 and a range of 0.28~0.42%.

C _eq (%) = C + (Mn / 6) + {(Cu + Ni) / 15} + {(Cr + Mo + V) / 5}

V _s (%) = C + (Mn / 5) + 5P- (Ni / 10)-(Mo / 15) + (Cu / 10)

Herein, the element symbol means content (%) of the element.

The reason why C _eq is preferably 0.40 to 0.58% is that the mixed structure of bainite and martensite is used not only in the base metal but also in the heat affected zone of welding, so that the desired structure can be obtained under a wide range of manufacturing conditions without accompanying deterioration of toughness. Because it is possible to get a river. When the carbon equivalent is less than the lower limit, it is difficult to maintain the tensile strength of the base metal at 750 MPa or more due to the lack of hardenability. When the carbon equivalent exceeds the upper limit, the toughness at the weld heat affected zone and the toughness at the surface of the steel sheet are deteriorated due to excessive increase in hardenability.

It is a V _s with 0.28~0.42% in order to reduce the center segregation of continuous casting the cast. When the V _s value exceeds 0.42%, central segregation occurs strongly, and when the tensile strength is high strength steel of 750 MPa or more, deterioration of toughness at the center portion occurs. On the other hand, if less than 0.28%, center segregation does not occur but tensile strength of 750 MPa or more cannot be secured.

The high strength steel sheet described in the above (1) is made of steel having the chemical composition described above, and is a steel sheet whose half width of the X-ray diffraction intensity from the (110) plane is 0.18 degrees or more. The half width of the X-ray diffraction intensity is 0.18 degrees or more for the following reasons.

FIG. 1: is a figure which shows the data of X-ray diffraction intensity on the (110) plane of steel typically, and is for demonstrating the half width of X-ray diffraction intensity. (A) of FIG. 1 shows one peak, and (b) shows a case where the peak is divided into two. As shown in Fig. 1, the half width indicates the width of the distribution in degrees at the intensity value at which the diffraction intensity is 1/2 of the highest intensity value (peak value) at the peak of the diffraction intensity. As shown in Fig. 1 (b), when the peak is divided into two, a value that is 1/2 of the higher peak intensity value is taken.

The half width of the X-ray diffraction intensity is one of the evaluation parameters of the lattice defect density in the metal structure and the like, but in the high strength steel sheet of the present invention, the index for achieving high toughness in the low temperature region is obtained by using the half width. The lattice defect density becomes limited. In other words, when the half width of the X-ray diffraction intensity on the (110) plane of the bainite or martensite phase is satisfied to be 0.18 degrees or more, the lattice defect density associated with the formation of fine subgrains is large and excellent in the low temperature region. Toughness is exerted. On the other hand, the half width of the X-ray diffraction intensity is preferably 0.22 degrees or more, more preferably 0.25 degrees or more.

The crystal plane on which X-ray diffraction is made the (110) plane is because this crystal plane is most commonly used in X-ray diffraction. In the high-strength steel sheet of the present invention, in order to obtain good low-temperature toughness, the "half width of the X-ray diffraction intensity on the (110) plane is defined to be 0.18 degrees or more", but in the case of the steel sheet having a strength of 750 MPa or more in tensile strength From the viewpoint of the balance of strength and the like, it is preferable that the half width is 0.20 to 0.30 degrees.

The half-width is taken as a half intensity value of the peak of Kα1 when the peaks of Kα1 and Kα2 are revealed independently in a diffraction pattern, and at the half intensity value of the peaks of Kα1 and Kα2. If the values appear to overlap, measure the width of the sum. In addition, the said half width measurement shall be performed in the surface parallel to a rolling surface in the site | part which entered 1 mm inside from the steel plate surface in the thickness direction.

The high strength steel plate of (1) base material is a steel plate which prescribed | regulated the chemical composition (the condition that A value is 0.5 or less) and the half width of X-ray-diffraction intensity as mentioned above. The half width can be set to 0.18 degrees or more by appropriately performing the hot rolling and the post-rolling treatment as described later, whereby bainite, martensite, or a mixed structure having finely developed dislocation substructures can be obtained. Lose. The steel plate which quantitatively prescribed this metal structure is a steel plate of description of (2) demonstrated next.

In the high strength steel sheet of the above-mentioned (2), in the high strength steel sheet of (1), the total ratio of martensite phase and bainite phase in which the metal structure occupies in the metal structure of the surface layer portion is 95% by volume or more, It is a steel plate whose total ratio of a martensite phase and a bainite phase occupies in a metal structure is 80 volume% or more.

In this steel sheet, the conditions (a) to (c) are clearly satisfied, and bainite, martensite, or a mixed structure thereof having a sufficiently fine and developed dislocation substructure is obtained. Therefore, the breakage generation suppression characteristics and breakage propagation stop characteristics at low temperatures are remarkably excellent, and thus the unstable fracture resistance characteristics are further improved, and both the high strength of 750 MPa and higher, the Charpy impact characteristic and the DWTT characteristic at -46 ° C are compatible. You can.

In the steel sheet having a half width of less than 0.18 degrees, the development of the dislocation underlayer is not sufficient and fine. Therefore, even if the metal structure satisfies the above conditions, sufficient Charpy impact characteristics and DWTT characteristics cannot be obtained.

On the contrary, when the chemical composition of the steel is out of the range defined by the present invention or the structure of the steel is not the structure defined by the present invention, even if the half width of the (110) plane peak is 0.18 degrees or more, the minute dislocation underlayer is fine. The steel sheet which combines both high strength and high toughness is not obtained.

Next, the manufacturing method of the high strength steel (method of said (4)) of this invention mentioned above is demonstrated.

The high strength steel sheet of the present invention is a method of reheat quenching and tempering after ordinary hot rolling as long as the chemical composition of the steel satisfies the conditions specified in the present invention, or similarly, a method of directly quenching and tempering after normal hot rolling, and also similarly ordinary It is also possible to manufacture by a method of accelerated cooling treatment after hot rolling. However, in order to reliably and stably manufacture, it is preferable to manufacture by the method of accelerated-cooling after performing hot rolling according to the following conditions.

Heating temperature: 950-1200 degrees Celsius

If heating temperature is less than 950 degreeC, the tensile strength of 750 Mpa or more may not be ensured. Moreover, when heating temperature exceeds 1200 degreeC, after the subsequent hot rolling, stabilization of the element (N, C, O) which is harmful to generation | occurrence | production of brittle fracture and low-temperature toughness will become inadequate, and desired low-temperature toughness may not be secured. have. For this reason, it is preferable to make heating temperature into 950-1200 degreeC.

Finishing temperature of hot rolling: 900 to 600 ° C

When the finishing temperature of hot rolling is less than 600 degreeC, the tensile strength of 750 Mpa or more may not be ensured. In addition, when the finish temperature of hot rolling exceeds 900 degreeC, the refinement | miniaturization of the structure by rolling and subsequent accelerated cooling is not enough, and the stabilization of the element (N, C) which is harmful to occurrence of brittle fracture and low-temperature toughness becomes inadequate. In some cases, the desired low temperature toughness cannot be secured. For this reason, the finishing temperature of hot rolling shall be 900-600 degreeC.

On the other hand, in order to make the X-ray half width of the (110) plane 0.18 degrees or more, after sufficiently reducing the low-temperature austenite region, the lower bainite is nucleated from the austenite particles, and further growth of the lower bainite is prevented. It is necessary to restrain. For this reason, a high-density dislocation is required, and therefore, it is preferable to perform 50% or more of rolling in the austenite microrecrystallization temperature range (975 ° C or lower A _r3 transformation point or more). On the other hand, when the reduction ratio in the unrecrystallized temperature range of austenite exceeds 90%, the anisotropy of the mechanical properties becomes remarkable, so the reduction ratio in the unrecrystallized temperature range is preferably 90% or less.

Water cooling start temperature: More than 600 degrees Celsius

When the water cooling start temperature at the time of accelerated cooling is less than 600 degreeC, the tensile strength of 750 Mpa or more may not be ensured. For this reason, the water cooling start temperature at the time of accelerated cooling should be 600 degreeC or more.

Cooling rate: More than 4 degrees Celsius / second

If the cooling rate at the time of accelerated cooling is less than 4 degrees-C / sec, coarse and large bainite will mix in a structure, and favorable low-temperature toughness cannot be ensured. Moreover, the dislocation undercarriage developed by the rolling process may not remain in the structure after transformation, and may not be introduced into the final product. For this reason, the cooling rate at the time of accelerated cooling should be 4 degrees C / sec or more. In addition, the upper limit of a cooling rate is not specifically prescribed.

Water cooling stop temperature: 550 degrees Celsius or less

When the water cooling stop temperature at the time of accelerated cooling exceeds 550 ° C, the tensile strength of 750 MPa or more cannot be ensured, the structure is not sufficiently refined, and the developed dislocation understructure introduced by rolling processing is the final after transformation. It may not be introduced into a product, and the desired unstable breakdown resistance property may not be secured. For this reason, it is good to make the water cooling stop temperature at the time of accelerated cooling to 550 degreeC or less.

On the other hand, it is preferable to stop cooling at 500-300 degreeC, without cooling to room temperature from a viewpoint of the toughness improvement by the tempering effect, and the prevention of a hydrogen defect, and to cool slowly after that. The water cooling stop temperature is the limit of the temperature range of 500 to 300 ℃, water cooling stop at a higher temperature than that directly leads to lack of quenching. In order to further enhance the tempering effect, tempering is performed below the A _c1 transformation point.

Reheat temperature width: 70 degrees Celsius or less

Cooling is complete | finished so that regeneration temperature width may be 70 degrees C or less. Here, the "reheating temperature width" means the difference between the temperature attained when the cooling is stopped and the temperature of the steel sheet when the surface temperature rises and stabilizes with heat inside the steel sheet after cooling stop. Specifically, it is the difference between the steel plate temperature measured immediately after exiting the water cooling device and the steel plate temperature measured when 20 to 50 seconds (different depending on the plate thickness) elapsed.

After the accelerated cooling stop, when the recuperation temperature width until the end of cooling exceeds 70 ° C., the dislocation undercarriage introduced by the rolling process is not introduced into the final product after transformation, and the breakage propagation stop characteristic is deteriorated. do. In order to reduce the reheating temperature width, it is preferable to reduce the temperature difference between the steel sheet surface layer and the central portion during cooling, and to terminate at least the phase transformation of the surface layer portion at the end of cooling.

According to the method demonstrated above, the high strength steel plate of the said (1) or (2) base material which combines the cryogenic toughness excellent in high strength can be reliably and stably manufactured.

Moreover, the high strength welded steel pipe (welded steel pipe of said (3)) of this invention is demonstrated.

The high strength welded steel pipe of the present invention is a welded steel pipe obtained by processing the high strength steel sheet of the present invention described above. The welded steel pipe may be obtained by processing by a known pipe-making method by any known welding as long as the high strength steel sheet of the present invention is used as the base material.

For example, a steel pipe is produced, quenched, and tempered as needed by a method of processing a high strength steel sheet into a U shape, followed by an O shape, welding and expanding the pipe by a conventional method (UO press method). Can be applied. The said UO press, welding, and expansion can be performed by using the apparatus provided in the normal steel mill. The welding may be performed by a submerged arc welding method using a commercially available welding material.

(Example)

The steel having the chemical composition shown in Table 1 was vacuum-dissolved in a laboratory to a slab having a thickness of 100 to 160 mm, hot rolled under various conditions, and then cooled under various conditions to have a thickness of 14 to 35 mm. It was a steel sheet. Hot rolling conditions and cooling conditions are shown in Table 2.

Table 1

Table 2

About the obtained steel plate, the structure of steel, the half width of X-ray-diffraction intensity, tensile property, and toughness were investigated with the following method. Moreover, the toughness was also investigated in the weld seam part.

In the investigation of the structure of the steel, martensite and bainite were observed by optical microscopic observation on the surface of the sample taken from a portion corresponding to 1/4 of the thickness of the plate and etched with a 2% nital corrosion solution. The total area ratio (total ratio) of was measured. Ten fields were measured about one sample, and the average of ten measured values was made into the total ratio of this steel plate.

The measurement of the half width of the X-ray diffraction intensity was carried out by taking a test piece of 25 square mm including a surface parallel to the rolled surface of the portion that entered 1 mm from the steel plate surface in the thickness direction, and electropolishing the surface thereof. The range of 20 mm diameter was used as the measuring surface. In addition, the cobalt source was used for the measurement using RU-200 by Rika Denki Corporation. The output was 30 KV, 100 Hz.

About the tensile property, the 14A tensile test piece prescribed | regulated to JISZ2201 was extract | collected in parallel in the rolling direction at the center of plate | board thickness, and was used for the tensile test, and yield strength YS (MPa) and tensile strength TS (MPa) were calculated | required.

For toughness, the Charpy impact test piece of No. 4 specified in JIS Z 2202 was taken vertically from the sheet thickness center in the rolling direction and subjected to the Charpy impact test, and the shock absorption energy _v E _{-46 ° C} (J) and the ductile-brittle wavefront transition. The temperature vTs (° C) was obtained. In addition, the DWTT test piece specified in API 5L was taken vertically in the rolling direction, and used for DWTT test, and the ductile fracture rate SA _{-46 占 폚} (area%) _{at -46 占 폚} and 75% ductile-brittle wavefront transition temperature. SATT _75% (° C.) was measured.

In addition, a weld seam is produced by submerged arc welding (heat input 3.2 to 7.6 kJ / mm) for each front and back surface, and the Charpy test piece is positioned at the weld FL portion (the boundary between the weld metal and the base metal). to, perpendicular to the weld line, performing the Charpy impact test were taken from the portion enters the interior 1㎜ from the surface was measured in the impact absorption energy _v E _{-46 ℃} (J) of the same region.

The structure of the steel (total ratio of martensite and bainite) and the half width of the X-ray diffraction intensity are shown together in Table 2 above. In Table 3, the tensile properties (YS, TS) of the base material, the toughness of the base material ( _v E _{-46 ° C} , _v T _s and SA _{-46 ° C} , SATT _75% ) and the toughness of the weld FL part ( _v E _{-46 ° C} ).

Table 3

As is apparent from Table 3, in the example of the present invention, the tensile strength (TS) of the base material is 750 MPa or more, the Charpy absorbed energy ( _v E _{-46 ° C.} ) and the DWTT ductile wavefront ratio of 75% or more _{at −46 ° C.} or more. (SA _{-46 ° C} ), and high Charpy absorption energy ( _v E _{-46 ° C} ) exceeding 80J was also shown in the joint Charpy test. In other words, it can be seen that the steel sheet has achieved all of the target performances indicated in the column of the above-mentioned "Technical Problems to be Invented", combines excellent cryogenic toughness with high strength and is excellent in unstable fracture resistance characteristics.

On the other hand, especially in the comparative example where the chemical composition of a steel plate is out of the range prescribed | regulated by this invention, or a half width | variety or a metal structure deviates from the specification of this invention, even if it satisfy | fills a prescribed chemical composition, especially DWTT ductile fracture rate is the target It was significantly less than 75%, and the high strength of 750 MPa, the Charpy impact characteristic and DWTT characteristic at -46 degreeC, and the weld FL part Charpy characteristic could not be satisfied simultaneously.

The high strength steel plate of this invention and the welded steel pipe obtained by processing this steel plate are high strength, and also comprise a welding part, and are excellent also in toughness at cryogenic temperature. Since the unstable fracture resistance characteristic based on evaluation by DWTT test is excellent, the effect of the remarkably improving the safety when using the steel pipe of this invention as a line pipe in cryogenic environment, for example is acquired. This steel sheet can be manufactured reliably and stably by the method of the present invention.

1 is a diagram schematically showing data (diffraction pattern) of X-ray diffraction intensity of steel, where (a) is one peak and (b) is a case where the peak is divided into two.

Claims (7)

In mass%, C: 0.01 to 0.10%, Si: 0.30% or less, Mn: 1.20 to 2.50%, P: 0.010% or less, S: 0.002% or less, Ni: 0.2 to 1.5%, Mo: 0.1 to 0.8%, Nb: 0.005 to 0.06%, Ti: 0.004 to 0.025%, sol.Al: 0.05% or less, N: 0.0050% or less and O (oxygen): 0.003% or less, the balance being Fe and impurities, A high strength steel sheet having an A value represented by the formula 1) of 0.5% or less, having a half width of the X-ray diffraction intensity from the (110) plane of 0.18 degrees or more, and a tensile strength of 750 MPa or more. A = 12P + 45S + 67 (N + O) ... (1) [Here, the element symbol in (1) formula means content (mass%) of each element contained in steel.] The high strength steel sheet according to claim 1, wherein the total ratio of martensite phase and bainite phase in the metal structure of the surface layer portion and the wall thickness center portion is 95 vol% or more and 80 vol% or more, respectively. In addition to the components described in claim 1, it further contains components of the following first group and / or second group, At this time, the components of the first group are in mass%, at least one of Cr: 1.0% or less, Cu: 0.1 to 1.5%, V: 0.1% or less, and B: 0.0030% or less, The component of the second group is at least one of Ca: 0.01% or less, Mg: 0.01% or less, Zr: 0.01% or less, and REM: 0.05% or less, The remainder is Fe and impurities, the A value represented by the following formula (1) is made of steel of 0.5% or less, the half width of the X-ray diffraction intensity from the (110) plane is 0.18 degrees or more, and the tensile strength is High strength steel sheet of 750 MPa or more. A = 12P + 45S + 67 (N + O) ... (1) [Here, the element symbol in (1) formula means content (mass%) of each element contained in steel.] The high strength steel sheet according to claim 3, wherein the total ratio of martensite phase and bainite phase in the metal structure of the surface layer portion and the wall thickness center portion is 95 vol% or more and 80 vol% or more, respectively. The high strength welded steel pipe obtained by processing the high strength steel plate of any one of Claims 1-4. In mass%, C: 0.01 to 0.10%, Si: 0.30% or less, Mn: 1.20 to 2.50%, P: 0.010% or less, S: 0.002% or less, Ni: 0.2 to 1.5%, Mo: 0.1 to 0.8%, Nb: 0.005 to 0.06%, Ti: 0.004 to 0.025%, sol.Al: 0.05% or less, N: 0.0050% or less and O (oxygen): 0.003% or less, the balance being Fe and impurities, After heating the steel with A value of 0.5% or less to 950-1200 degreeC, it hot-rolls and finishes rolling at the finishing temperature of 900-600 degreeC, and it is 550 degrees C or less from the temperature range which does not exceed 600 degreeC. The method of producing a high strength steel, characterized in that the cooling is terminated after the accelerated cooling at a cooling rate of 4 ° C / sec or higher to a temperature of? A = 12P + 45S + 67 (N + O) ... (1) [Here, the element symbol in (1) formula means content (mass%) of each element contained in steel.] In addition to the components described in claim 6, further comprising the components of the following first group and / or second group, At this time, the components of the first group are in mass%, at least one of Cr: 1.0% or less, Cu: 0.1 to 1.5%, V: 0.1% or less, and B: 0.0030% or less, The component of the second group is at least one of Ca: 0.01% or less, Mg: 0.01% or less, Zr: 0.01% or less, and REM: 0.05% or less, The remainder is Fe and impurities, and after heating the steel having an A value of 0.5% or less represented by the following formula (1) to 950 to 1200 ° C, hot rolling is performed to finish rolling at a finishing temperature of 900 to 600 ° C, and 600 ° C. The method of producing high strength steel, characterized in that the cooling is terminated after the accelerated cooling is performed at a cooling rate of 4 ° C / sec or more from a temperature range not lower than 550 ° C to a temperature of 4 ° C / sec or more, so that the recuperation temperature width is 70 ° C or less. A = 12P + 45S + 67 (N + O) ... (1) [Here, the element symbol in (1) formula means content (mass%) of each element contained in steel.]