JP5768603B2 - High-strength welded steel pipe with high uniform elongation characteristics and excellent low-temperature toughness at welds, and method for producing the same - Google Patents

Description

  The present invention relates to API standard X65 to X70 (tensile strength exceeding 550 MPa) class high-strength line pipe, and relates to a high-strength welded steel pipe having excellent weld toughness in a low temperature range up to -20 ° C. and a method for producing the same. .

  In recent years, line pipes used for the transportation of natural gas and crude oil have been strengthened year by year in order to improve transportation efficiency by increasing pressure and to improve local welding construction efficiency by reducing wall thickness. As a result of ground deformation in Japan, there has been a demand for high deformability that hardly causes buckling even if large deformation occurs in the line pipe.

  The lower the yield ratio, the greater the deformability of the steel material. Therefore, a low yield ratio steel has been developed in which the microstructure of the steel material is a two-phase structure in which a soft ferrite phase and a hard phase such as hard bainite and martensite are appropriately dispersed. Has been.

  For example, Patent Document 1 relates to a method of manufacturing a low yield ratio, low carbon, low alloy, high strength steel, which describes a steel having a structure in which a hard phase is appropriately dispersed in a soft phase, and as a manufacturing method thereof, quenching (Q) and tempering ( In the middle of T), a heat treatment method is disclosed in which quenching (Q ′) from a two-phase region of ferrite and austenite is performed.

  Patent Document 2 relates to a method of manufacturing a high-strength low yield ratio steel pipe for construction, and based on the same concept, in the manufacturing process of a welded steel pipe, it is heated in a two-phase region after performing cold bending and welding at the seam. A method of manufacturing a low yield ratio steel pipe that is post-cooled is disclosed. Patent Document 3 discloses a steel for high-strength line pipes having a low yield ratio, and it is disclosed that a low yield ratio is achieved by a structure in which a processed ferrite that is a soft phase and a hard phase of bainite or martensite are mixed. Yes. Patent Document 4 relates to a method for producing a high-strength and high-toughness steel sheet, and discloses that a low yield ratio is achieved when hard island martensite is dispersed in bainite.

  When the pipe pipe is further deformed after the line pipe undergoes large deformation and buckling occurs, local strain concentration occurs in the pipe, and when the ductile fracture occurrence limit strain is reached, ductile fracture occurs. Since the critical strain at which ductile fracture occurs is considered to correlate with the uniform elongation of the steel material, steels having a high uniform elongation with a low yield ratio have been developed.

  Patent Document 5 relates to a low-yield-ratio high-strength and high-toughness steel sheet and a method for producing the same, and the metal structure is a three-phase structure of ferrite, bainite, and island martensite, and the volume ratio of 3-15% island martensite and volume. A steel sheet containing a retained austenite with a fraction of 2% or more and a uniform elongation in the longitudinal direction of the steel sheet of 12% or more and a method for producing the same are disclosed. Patent Document 6 describes a low yield ratio, high strength, high toughness steel pipe using a low yield ratio, high strength, high toughness steel pipe according to Patent Document 5, and a method for producing the same.

JP-A-55-97425 Japanese Patent Laid-Open No. 07-150247 Japanese Patent Laid-Open No. 08-209291 JP 2006-265577 A JP 2008-248328 A JP 2008-248330 A

  Currently, the practical use of high strength line pipes of API standard X65-X70 class with a tensile strength exceeding 550 MPa has progressed, and laying in a cold earthquake zone of −20 ° C. has been studied. No. 6 does not describe a butt weld when using a steel plate as a steel pipe, and does not describe a steel pipe suitable for the above environment. In addition, Patent Documents 1 to 4 do not describe the uniform elongation.

  Therefore, the present invention is highly uniform for suppressing the occurrence of buckling when subjected to bending deformation due to ground deformation such as an earthquake, and for preventing the occurrence of ductile fracture from the buckled portion even if the pipe buckles. An object is to provide a steel pipe using API standard X65-X70 grade high strength steel having elongation and excellent low temperature toughness in a welded portion.

When the buried steel pipe is subjected to bending deformation due to ground fluctuation, the present inventors have aimed to suppress the occurrence of buckling inside the bend until the amount of compressive strain at the position becomes 1%. The following findings were obtained through extensive studies on characteristics and microstructure. In the present invention, the low temperature toughness of the weld zone refers to the low temperature toughness of the weld metal.
1 The buckling can be suppressed as the hardening gradient before and after 1% strain of the stress-strain curve increases. In the actual pipe bending test, the 1.5% proof stress value relative to the 0.5% proof stress value in the stress-strain curve of the steel pipe used. No buckling occurs when the value is 1.15 or more.
2 Uniform elongation of steel sheet is greatly influenced by the form of island martensite (may be called MA (Martensite-Austenite constituents)) and the dispersion state in the first phase. By controlling the heat treatment during forming into a steel pipe shape, the optimum form and dispersion state of MA can be obtained without altering the microstructure of the weld metal necessary for obtaining low temperature toughness.

  In the present invention, “high uniform elongation” means that the ratio of 1.5% proof stress to 0.5% proof stress of the base metal part (1.5% proof stress / 0.5% proof stress value) is 1.15 or more. In addition, it means that the product of tensile strength and uniform elongation has an excellent deformation performance of 7500 MPa ·% or more.

The present invention has been made by further investigation based on the obtained knowledge. The composition of the base material is mass%,
C: more than 0.03% to 0.06%,
Si: 0.1% or less,
Mn: 1.0-1.7%,
Al: 0.003 to 0.08%,
Nb: 0.01-0.04%,
Ti: 0.005 to 0.025%,
Further Cu: 0.1-0.5%,
Ni: 0.1 to 0.5%,
Mo: 0.1 to 0.5%,
Cr: 0.1 to 0.5%,
V: 0.003-0.04%,
1 type or 2 types or more, and the balance Fe and unavoidable impurities,
The component composition of the weld metal is mass%,
C: 0.06 to 0.08%,
Si: 0.2 to 0.5%
Mn: 1.3-1.8%
Al: 0.03% or less,
B: 0.001 to 0.003%,
Nb: 0.005 to 0.025%,
Ti: 0.015-0.040%,
Cu: 0.1% or less,
V: 0.03% or less,
O: 0.015-0.04%,
N: 0.01% or less,
In addition, Ni: 0.1 to 0.4%,
Mo: 0.05-0.2%
Cr: 0.1 to 0.2%
Containing one or more of
The balance Fe and inevitable impurities,
The base material portion is an island-shaped martensite having an average aspect ratio of 2.0 or less in which the first phase is ferrite and the second phase is dispersed in an area ratio of 5 to 20% in the first phase. 90% or more of martensite has a microstructure in the ferrite grain boundaries,
The weld metal part has a highly uniform elongation characterized by having a microstructure in which the area ratio of acicular ferrite is 80% or more and the area ratio of island martensite is 5% or less, and the weld part High strength welded steel pipe with excellent low temperature toughness.
2. The component composition of the base material part is further mass%,
Ca: 0.0005 to 0.01%,
REM: 0.0005 to 0.02%,
Zr: 0.0005 to 0.01%,
Mg: 0.0005 to 0.01%,
A high-strength welded steel pipe having high uniform elongation as described in 1 and excellent in low temperature toughness at the welded portion.
3. % By mass
C: more than 0.03 to 0.06%,
Si: 0.1% or less,
Mn: 1.0-1.7%,
Al: 0.003 to 0.08%,
Nb: 0.01-0.04%,
Ti: 0.005 to 0.025%,
Further Cu: 0.1-0.5%,
Ni: 0.1 to 0.5%,
Mo: 0.1 to 0.5%,
Cr: 0.1 to 0.5%,
V: 0.003-0.04%,
A steel slab comprising one or more of the balance Fe and unavoidable impurities,
After reheating to Ac ₃ or higher, hot rolling at a rolling end temperature Ar ₃ or higher, and then forming a steel plate obtained by air cooling into a cylindrical shape by cold forming, followed by rapid heating to Ac ₁ or higher and Ac ₃ or lower Then, after cooling to room temperature by air cooling or water cooling, the end is welded, and finally the pipe is expanded, and a high strength welded steel pipe with high uniform elongation and excellent low temperature toughness at the weld is manufactured. Method.
4). The component composition of the billet is further mass%,
Ca: 0.0005 to 0.01%,
REM: 0.0005 to 0.02%,
Zr: 0.0005 to 0.01%,
Mg: 0.0005 to 0.01%,
A method for producing a high-strength welded steel pipe having high uniform elongation as described in 3 and excellent in low-temperature toughness of the welded portion, characterized by containing one or more of the following.

  According to the present invention, there is provided an API standard X65-X70 class high-strength steel pipe which is less prone to buckling of the steel pipe and subsequent ductile fracture due to ground fluctuation such as an earthquake and has a low temperature toughness of a welded portion up to −20 ° C. This is extremely useful in industry.

In the present invention, the component composition and the microstructure of the base metal part and the weld metal part are respectively defined.
[Base Material Component Composition] In the following description,% is mass%.
C: More than 0.03% and 0.06% or less C needs to be added in excess of 0.03% in order to secure a sufficient MA area ratio. On the other hand, if added over 0.06%, in addition to the ferrite phase and second phase MA in the base material microstructure, it leads to the formation of pearlite phase and leads to a decrease in ductility, so the upper limit is made 0.06% .

Si: 0.1% or less Since Si promotes the formation of MA in the weld heat affected zone and causes a reduction in weld toughness, the upper limit is made 0.1% in order to suppress the formation of MA in the weld.

Mn: 1.0 to 1.7%
Mn acts as a hardenability improving element. Furthermore, the addition of a large amount has the effect of reducing the amount of C that can be dissolved in the ferrite phase and increases the C concentration in the untransformed austenite region, thereby increasing the amount of MA produced.

  As will be described later, in order to make the area ratio of MA 5% or more in the microstructure, it is necessary to add 1.0% or more. On the other hand, even if added over 1.7%, the effect is saturated, so the upper limit is made 1.7% from the viewpoint of economy.

Al: 0.003 to 0.08%
Al acts as a deoxidizing element. In order to obtain a sufficient deoxidation effect by simultaneous addition with Si, a content of 0.003% or more is necessary. On the other hand, if added over 0.08%, the cleanliness of the steel is lowered and the uniform elongation is reduced, so the upper limit is made 0.08%.

Nb: 0.01-0.04%
Nb expands the austenite non-recrystallized region during hot rolling, and also acts as an element for improving the hardenability of steel. Further, since the C concentration in the untransformed austenite region is increased similarly to Mn, the amount of MA produced is increased. As will be described later, in order to make the area ratio of MA 5% or more in the microstructure, it is necessary to add 0.01% or more. On the other hand, if added over 0.04%, the toughness of the weld is reduced, so the upper limit is made 0.04%.

Ti: 0.005-0.025%
Ti forms nitrides and has an adverse effect on toughness. It is effective in reducing the amount of dissolved N in steel. In addition, the precipitated TiN suppresses the coarsening of austenite grains due to the pinning effect, and the microstructure is coarse. Control. In order to obtain such an effect, 0.005% or more is contained. On the other hand, if added over 0.025%, TiC is formed, and the yield ratio tends to increase due to precipitation hardening, so the upper limit is made 0.025%.

  Furthermore, in the present invention, API standard X65 to X70 strength is secured as the strength of the base material portion, and one or more of Cu, Ni, Mo, Cr, and V are used for the purpose of increasing the strength of the weld heat affected zone. Containing.

Cu: 0.1 to 0.5%
When Cu is contained in an amount of 0.1% or more, it acts as a hardenability improving element and can replace a large amount of Mn addition. However, the addition of up to 0.5% can satisfy the strength of APIX70, and the effect is saturated even if it is contained in excess of 0.5%. .

Ni: 0.1 to 0.5%
Ni acts as a hardenability improving element and does not cause deterioration in toughness even when added. In order to obtain this effect, it is preferable to contain 0.1% or more, but the addition of 0.5% can satisfy the strength of APIX70, and even if it exceeds 0.5%, the effect is effective. In order to saturate, when it is contained, the upper limit is made 0.5%.

Mo: 0.1 to 0.5%
Mo can be contained in order to improve the strength of the base material or the weld heat affected zone. By containing 0.1% or more, it acts as a hardenability improving element and can be used as a substitute for adding a large amount of Mn. However, it is an expensive element, and the addition of up to 0.5% can satisfy the strength of APIX70, and even if contained over 0.5%, the effect is saturated. Is 0.5%.

Cr: 0.1 to 0.5%
Cr can be contained in order to improve the strength of the base material or the weld heat affected zone. By containing 0.1% or more, it acts as a hardenability improving element and can be used as a substitute for adding a large amount of Mn. However, it is an expensive element, and the addition of up to 0.5% can satisfy the strength of APIX70, and even if contained over 0.5%, the effect is saturated. Is 0.5%.

V: 0.003-0.04%
V can be added to improve the strength of the base material or the weld heat affected zone. By containing 0.003% or more, carbide can be formed in the steel and the strength of the steel can be increased by precipitation strengthening. On the other hand, if the content exceeds 0.04%, the toughness of the weld heat-affected zone is adversely affected.

  The above is the basic component composition of the base material part, but when further improving the uniform elongation characteristic, one or more of Ca, REM, Zr, and Mg can be contained. Ca, REM, Zr, and Mg form MnS, which is a non-metallic inclusion in the steel, or form an oxide or nitride, thereby improving the cleanliness of the steel and improving the uniform elongation.

Ca: 0.0005 to 0.01%
Ca is an element effective for controlling the form of sulfide in steel, and when contained in an amount of 0.0005% or more, the production of MnS harmful to ductility is suppressed. On the other hand, when the content exceeds 0.01%, a CaO-CaS cluster is formed, and ductility is deteriorated. Therefore, when it is contained, the upper limit is preferably made 0.01%.

REM: 0.0005 to 0.02%
REM is an effective element for controlling the form of sulfide in steel, and when it is contained in an amount of 0.0005% or more, it suppresses the generation of MnS harmful to ductility. On the other hand, since it is an expensive element and the effect is saturated even if it contains more than 0.02%, when it is contained, the upper limit is preferably made 0.02%.

Zr: 0.0005 to 0.01%
Zr forms carbonitrides in steel and brings about a pinning effect that suppresses coarsening of austenite grains. In order to obtain a sufficient pinning effect, the content is preferably 0.0005% or more. However, if the content exceeds 0.01%, the cleanliness of the steel is remarkably lowered and the ductility is lowered. In such a case, the upper limit is preferably set to 0.01%.

Mg: 0.0005 to 0.01%
Mg has the effect of refining oxides in the steelmaking process and is effective in suppressing coarse oxides that cause ductility reduction. In order to sufficiently obtain an oxide refinement effect, it is preferably contained in an amount of 0.0005% or more, but even if contained over 0.01%, the effect is saturated. Is preferably 0.01%.

  Components other than the above are Fe and inevitable impurities. In the present invention, P and S are unavoidable impurities, and excessive P content segregates during casting to lower the ductility of the steel, and excessive S content promotes the generation of MnS harmful to ductility. In any case, it is preferable to reduce as much as possible in consideration of economic efficiency, and the P amount is preferably 0.01% or less, and the S amount is preferably 0.003% or less.

[Welding metal component composition] In the following description, "%" means "mass%".
C: 0.06% to 0.08%
In the weld metal, C is required to be 0.06% or more in order to prevent hot cracking of the weld metal. On the other hand, if it exceeds 0.08%, a large amount of MA harmful to weld metal toughness is generated in the weld metal microstructure, so the upper limit is made 0.08%.

Si: 0.2 to 0.5%
Si acts as a deoxidizing element in the weld metal and is an element necessary for controlling the amount of oxygen in the weld metal. If the Si content in the weld metal is less than 0.2%, deoxidation is insufficient and the amount of oxygen in the weld metal increases, resulting in a decrease in toughness. On the other hand, if it exceeds 0.5%, the production of MA harmful to weld metal toughness becomes remarkable, so the upper limit is made 0.5%.

Mn: 1.3-1.8%
Mn also acts as a hardenability improving element in the weld metal. In order to make the weld metal an acicular ferrite having higher strength than polygonal ferrite, it is necessary to contain 1.3% or more. On the other hand, even if added over 1.8%, the effect is saturated, so the upper limit is made 1.8%.

Al: 0.03% or less Al is present in the weld metal as an unavoidable impurity due to dilution from the base metal part. However, if it exceeds 0.03%, the formation of TiO described later is inhibited, and the acicular ferrite of the weld metal Since the miniaturization is suppressed and excellent low temperature toughness cannot be obtained, the upper limit is made 0.03%.

B: 0.001 to 0.003%
B is an element necessary for suppressing the formation of polygonal ferrite from the austenite grain boundary of the weld metal and forming an acicular ferrite main structure. In order to completely suppress the formation of polygonal ferrite from the grain boundary, it is necessary to contain 0.001% or more, but even if it exceeds 0.003%, the effect is saturated, so the upper limit is 0.003%. And

Nb: 0.005 to 0.025%
Nb forms B as a solid solution B at the austenite grain boundary by forming a nitride before the solid solution N in the weld metal and B. In order to acquire such an effect, it is necessary to contain 0.005% or more. On the other hand, if it exceeds 0.025%, carbides are formed, the weld metal is precipitated and hardened, and the toughness is reduced, so the upper limit is made 0.025%.

Ti: 0.015-0.040%
Ti reacts with oxygen in the weld metal to form TiO that functions as an acicular ferrite transformation nucleus from within the weld metal austenite grains. In order to obtain a fine acicular ferrite structure, it is necessary to generate a large number of TiO, and Ti must be contained in an amount of 0.015% or more. On the other hand, if it exceeds 0.040%, TiO in the weld metal is aggregated and coarsened to reduce the Charpy impact value, so the upper limit is made 0.040%.

Cu: 0.1% or less Cu may be contained as an impurity in the weld metal due to dilution from the base material, but if it exceeds 0.1%, it segregates at the columnar crystal interface during the solidification process of the weld metal. In addition, since the melting point is lower than that of the base iron, it causes liquefaction cracking, so the upper limit is made 0.1%.

V: 0.03% or less V may be mainly contained as an impurity in the weld metal due to dilution from the base metal, but if it exceeds 0.03%, carbide is formed and precipitation hardening occurs. In order to reduce the toughness of the metal, the upper limit is made 0.03%.

O: 0.015-0.04%
O reacts with the above-mentioned Ti to form TiO that functions as an acicular ferrite transformation nucleus from within the weld metal austenite grains. In order to generate a large number of TiO necessary for obtaining a fine acicular ferrite structure, it is necessary to contain 0.015% or more. On the other hand, if it exceeds 0.04%, TiO in the weld metal is aggregated and coarsened to reduce the Charpy impact value, so the upper limit is made 0.04%.

N: 0.01% or less N in the weld metal exists as an unavoidable impurity. However, if it exceeds 0.01%, it dissolves and significantly deteriorates the weld metal toughness, so the upper limit is 0.01%. And

  Furthermore, in the present invention, for the purpose of increasing the strength of the weld metal, one or more of Ni, Mo, and Cr are contained.

Ni: 0.1 to 0.4%
When Ni is contained in an amount of 0.1% or more, it acts as a hardenability improving element, and even if contained in a large amount, Ni does not cause toughness deterioration. However, the addition of up to 0.4% can satisfy the strength of APIX70, and the effect is saturated even if the content exceeds 0.4%. .

Mo: 0.05-0.2%
By containing 0.05% or more of Mo, it acts as a hardenability improving element and can be used as an alternative to the addition of Mn. However, since it is an expensive element and the addition of up to 0.2% can satisfy the strength of APIX70, the effect is saturated even if it is contained over 0.2%. Is 0.2%.

Cr: 0.1 to 0.2%
When Cr is also contained in an amount of 0.1% or more, it acts as a hardenability improving element and can be used as an alternative to Mn addition. However, it is an expensive element, and the addition of up to 0.2% can satisfy the strength of APIX70, and even if contained over 0.2%, the effect is saturated. 0.2%.

Components other than the above in the weld metal are Fe and inevitable impurities. In the present invention, P and S are unavoidable impurities, and excessive P content segregates at the grain boundaries of the weld metal part to lower ductility and toughness. Excessive S content is a harmful component of MnS. In order to promote the generation, it is preferable to reduce the amount as much as possible in consideration of economic efficiency. The P amount is preferably 0.01% or less, and the S amount is preferably 0.003% or less.
[Base material microstructure]
In the present invention, the microstructure of the steel pipe base material portion has a first phase (parent phase) mainly composed of ferrite and a second phase dispersed and present in the first phase (parent phase). The two phases are island martensite (may be referred to as MA) having an average aspect ratio of 2.0 or less. The area ratio of the island-like martensite in the second phase is 5 to 20%, and more than 90% of the island-like martensite is defined in the structure existing in the ferrite grain boundary.

  In order to increase the ratio of 1.5% proof stress to 0.5% proof stress (hereinafter also referred to as proof stress ratio) in order to improve the bending buckling limit strain of the steel pipe, MA is defined as the second phase in the base metal part. Disperse at a rate of 5-20%.

  If the area ratio is less than 5%, a sufficient yield strength ratio for improving the bending buckling limit strain of the steel pipe cannot be obtained. On the other hand, if the area ratio exceeds 20%, the aspect ratio of MA described later satisfies the specification. However, since the uniform elongation drop is remarkable, the upper limit is made 20%.

  Note that the MA area ratio is about 1000 to 3000 magnifications and four or more cross-sectional SEM (scanning electron microscope) photographs of the steel are taken, and the individual areas of the MA grains visible in each photograph are measured and integrated. And dividing by the measurement visual field area.

  The aspect ratio of MA is 2.0 or less. As the shape of the MA grain becomes narrower, microscopic breakage is likely to occur from the interface between the MA and the ferrite phase as the first phase, and as a result, the uniform elongation decreases. To do.

  As for the aspect ratio of MA, the cross-sectional SEM photograph of steel is taken at a magnification of about 1000 to 3000 times and four or more fields of view are taken, and for each field of view, the major axis and the minor axis are measured by image analysis to measure the aspect ratio ( = Major axis / minor axis), and then the average value is calculated, and further the average value over the entire field of view.

  Furthermore, when MA having an aspect ratio of 2.0 or less is present in the ferrite grains, although a high yield strength ratio can be obtained, the decrease in uniform elongation when the strength is increased is significant. It is important to exist at the grain interface, and the MA present on the ferrite grain boundary needs to be 90% or more of the total MA.

  The fraction of MA present on the ferrite grain boundary is determined by confirming the positional relationship with the grain boundary in the SEM photograph for all MA particles measured by the above-described area ratio measurement, and calculating the number of particles present on the grain boundary. Count and calculate by dividing by the total number of MA particles.

  In addition, since the ferrite grain boundary can appear by, for example, nital corrosion, it is possible to confirm whether or not the observed MA is on these grain boundaries.

  In the present invention, the area ratio of the microstructure other than the ferrite that is the main component of the matrix and the island-like martensite (MA) that is the second phase is preferably as small as possible.

  However, when the area ratio of the microstructure other than ferrite or bainite and island martensite (also referred to as MA) is small, the influence is small, and therefore other metal structures of 5% or less in total area ratio, In addition, one or more of pearlite and cementite may be contained.

  When retained austenite is present as a microstructure other than ferrite or bainite and island martensite (MA), it can be expected to have an effect of improving elongation due to work-induced transformation, but it is hard martensite after plastic working once. Rather, the area ratio is preferably less than 2%, and more preferably less than 1%.

[Welding metal microstructure]
In the present invention, the microstructure of the steel pipe weld metal is defined as an acicular ferrite structure having an area ratio of 80% or more and a structure in which the area ratio of island martensite is 5% or less.

  In order to achieve both high strength and excellent toughness in the weld metal, it is necessary to make a fine acicular ferrite structure with a large number of TiO as the core, which is partly austenitic by heat treatment etc. and then retransformed. As the fraction of martensite, pearlite, cementite, and the like produced increases, the toughness significantly decreases.

  For this reason, the acicular ferrite area ratio in the weld metal is required to be 80% or more, and preferably 90% or more. Further, in the weld metal, hard MA significantly deteriorates toughness even in a small amount, so the area ratio is set to 5% or less, preferably 2% or less.

Hereinafter, a suitable manufacturing method of the steel having the above component composition and the above microstructure will be described.
The steel temperature condition defined in the present invention refers to the average temperature in the thickness direction of the steel slab or the steel plate.

Steel slab heating temperature: Ac ₃ or higher In order to build the shape and microstructure by hot rolling, the steel slab is reheated to a temperature of Ac ₃ or higher for the purpose of austenizing the steel slab. If the heating temperature is less than Ac _3, untransformed ferrite remains and adversely affects the subsequent microstructure control. In order to completely austenite, the heating temperature is preferably set to 1000 ° C. or higher. On the other hand, the upper limit of the billet heating temperature is preferably 1200 ° C. or less from the viewpoint of base material toughness. Steel slab heating temperature: Hot rolling is started from Ac ₃ or higher. In the case of direct feed rolling, hot rolling is started at a temperature of Ac ₃ or higher without reheating. Incidentally, Ac ₃ temperature can be obtained simply by substituting the alloy element content of the steel in the following formula (1).
_{Ac 3 = 961.6-311.9C + 49.5Si-36.4Mn} + 12.7Al-51Cu-29Ni-8.7Cr + 13.5Mo + 308.1Nb-140V + 318.9Ti + 611.2B (1)
M (%) in the formula indicates the content (mass%) of the element M, and when the element M is not added, it is calculated as 0%.

Hot rolling end temperature: Ar ₃ or higher When the rolling temperature when forming into a predetermined plate thickness and width by hot rolling is lowered to less than Ar ₃ , the so-called ferrite that has undergone transformation undergoes processing during rolling. A processed ferrite is formed. Since the yield strength increases as the amount of processed ferrite increases, it becomes difficult to achieve the yield ratio necessary for improving the bending buckling strain of the steel pipe. Therefore, the temperature of the final rolling pass is set to Ar ₃ or higher. Preferably, it is set to 800 ° C. or higher. After hot rolling, air cooling is performed to make the microstructure first phase ferrite.
Incidentally, Ar ₃ temperature can be obtained simply by substituting the alloy element addition of the steel in the following formula (2).
Ar ₃ = 910-273C-74Mn-56Ni-16Cr-9Mo-5Cu (2)
M (%) in the formula indicates the content (mass%) of the element M, and when the element M is not added, it is calculated as 0%.

Next, the manufacturing conditions of the steel pipe will be described.
First, the steel plate manufactured by the above-described manufacturing method is formed into a cylindrical shape by a cold working method. There are UOE method, roll bend method and the like as the forming method, and any of them may be used. And after shape | molding in a cylinder shape, a reheating process is implemented.

Reheating temperature: Ac ₁ or more and Ac ₃ or less After making the microstructure the first phase of the microstructure ferrite, a part thereof is reversely transformed into austenite by heating. In this case, the reverse-transformed austenite is transformed from the triple point of the ferrite grain boundary, and is transformed diffusively, so that MA which is further transformed in the subsequent cooling process is suppressed from being produced in the ferrite grain, The MA to be generated can have a shape with a small aspect ratio and little uniform elongation deterioration.

When the reheating temperature is less than Ac ₁ , since it does not reversely transform to austenite, MA as a hard second phase cannot be generated. On the other hand, when the reheating temperature exceeds Ac ₃ , the entire surface is reversely transformed into austenite, and it is extremely difficult to obtain a state in which the hard phase is dispersed at a predetermined area ratio. ₁ or more and Ac ₃ or less. In order to suppress the generation of reverse transformed austenite during heating from within the grains of the ferrite, it is preferable to set the heating rate during heating to 2 ° C./s or more.

The Ac ₁ temperature can be easily obtained by substituting the alloy element addition amount of steel into the following formula (3).
_{Ac 1 = 751-26.6C + 17.6Si-11.6Mn} -169Al-23Cu-23Ni + 24.1Cr + 22.5Mo + 233Nb-39.7V-5.7Ti-895B (3)
M (%) in the formula indicates the content (mass%) of the element M, and when the element M is not added, it is calculated as 0%.

  After reheating, air cooling or water cooling is performed. In order to increase the hardness of MA which is a hard phase and to obtain a higher yield strength ratio stably, it is preferable to water-cool to 200 ° C. or less at a cooling rate of 10 ° C./s or more.

  After heating and cooling, the ends are welded. If the end portion is first welded and then heated and cooled to generate MA, the weld metal retransforms, martensite, pearlite, cementite, or MA is generated, and the acicular ferrite area ratio in the structure is 80 % Cannot be over.

In particular, when the weld metal is heated to a temperature range of Ac ₁ to Ac ₃ , a large amount of MA is generated in the weld metal, and the MA area ratio cannot satisfy the target value of 5% or less. For the above reasons, seam welding for forming a steel pipe is always performed after heating and cooling of the base metal portion so that the microstructure of the weld metal is mainly composed of acicular ferrite.

  Seam welding is generally single layer welding on the inner and outer surfaces by submerged arc welding, but may be one layer welding by laser or laser arc hybrid welding. After seam welding, pipe expansion is performed to improve the roundness of the pipe. As the tube expansion condition, it is preferable that the tube expansion rate is 0.6% or more and 2.0% or less from the viewpoint of securing the shape.

Steels having chemical compositions A to J shown in Table 1 were used, and steel slab heating, rolling and cooling shown in Table 2 were performed, and the steel plate No. 1-12 were produced. Although not shown in Table 1, the contents of P and S, which are inevitable impurities, were both P amount: 0.01% or less and S amount: 0.003% or less.

  From these steel plates, in a direction perpendicular to the rolling direction, a flat plate tensile test piece having a parallel part width of 150 mm and a parallel part length of 600 mm was collected, and after applying a tensile strain corresponding to U-O press forming of a UOE steel pipe, Heating and cooling were performed under the heat treatment conditions shown in Table 3.

  Next, using the heat-treated flat plate tensile test specimen, inner and outer surface single-layer submerged arc welding for simulating seam welding of a steel pipe was performed under the welding heat input conditions shown in Table 3. Finally, a tensile strain corresponding to UOE steel pipe expansion forming was applied to the test body including the submerged arc weld. For comparison, after applying tensile strain to the flat plate tensile test piece, submerged arc welding was first performed, and then heating / cooling was performed, and finally a test body that applied tensile strain again was also produced.

  A sample for microstructural observation is collected from the center of the base metal part of the specimen including the submerged arc weld, and the two-stage etching method is used after mirror-polishing the plate thickness section parallel to the rolling longitudinal direction of the original steel sheet. MA appeared. Thereafter, a microstructure photograph of 5 fields of view was randomly taken at a magnification of 2000 using a scanning electron microscope (SEM). The area ratio of MA, the average aspect ratio, and the ratio of MA belonging to the ferrite grain boundary in the photograph. Was measured and calculated by image analysis. Furthermore, after the same sample was mirror-polished again, it was etched with a 3% nitric acid alcohol etchant and observed with an optical microscope at a magnification of 400 times to confirm the type of the first phase of the microstructure.

  Next, a No. 14A tensile test piece was sampled from the center of the base material part of the same specimen in accordance with JIS Z2201, and a tensile test was performed. The tensile test measured yield strength, tensile strength, and uniform elongation according to JIZ Z2241.

  Similarly, a 2 mm V-notch Charpy impact test piece was sampled from the center of the base material part of the test body according to JIS Z2202, and a Charpy impact test was performed. The Charpy test measured ductile-brittle fracture surface transition temperature (vTrs) according to JIS Z2242.

  A chemical composition analysis sample was taken from the weld metal of the submerged arc weld and the chemical composition of the weld metal was measured. Table 4 shows the measurement results.

  A sample for observing the microstructure of the weld metal was collected from the submerged arc weld, and the plate thickness section was mirror-polished, and then MA was revealed using a two-step etching method. After that, using a scanning electron microscope (SEM), microscopic photographs of 5 fields of view were randomly taken at a magnification of 2000 times, and the area ratio of MA in each field of view was measured and calculated by image analysis, and the average of 5 fields of view was calculated. The value was determined. Furthermore, after the same sample was mirror-polished again, it was etched with a 3% nitric acid alcohol etchant and observed with an optical microscope at a magnification of 400 times to confirm the type of microstructure.

  Next, a 2 mmV notch Charpy impact test piece was sampled from the submerged arc weld according to JIS Z2202, and a Charpy impact test of the weld metal was performed. The Charpy test was performed according to JIS Z2242, and the absorbed energy (average value of 3 bars) at a test temperature of −20 ° C. was measured.

  Results of microstructure analysis and machine of the base metal part and weld metal part of the specimen subjected to cold working + simulated heat treatment + inner / outer surface 1 layer submerged arc welding + pipe expansion equivalent cold working to simulate UOE steel pipe manufacturing process Table 5 summarizes the results of the investigation of the physical properties.

No. 1-1 to 6 are invention examples in which the base metal part chemical composition, the weld metal chemical composition, the base metal part microstructure, and the weld metal microstructure are within the scope of the present invention, and any of the strengths of APIX65 to X70 is obtained. The ratio of 1.5% proof stress to 0.5% proof stress is 1.15 or more, the product of tensile strength and uniform elongation exceeds 7500 MPa ·%, and the weld metal Charpy absorbed energy at −20 ° C. Exhibited an excellent low-temperature toughness exceeding 100 J.

  On the other hand, comparative example No. which heated / cooled after submerged arc welding was performed after cold work distortion equivalent to a U-O press was given. In No. 1-2, both the acicular ferrite area ratio and the MA area ratio were outside the scope of the present invention due to the heat effect of heating and cooling in the microstructure of the weld metal, and the weld metal Charpy absorbed energy was significantly reduced.

  In Comparative Example 1-3 in which the reheating temperature after applying cold working strain equivalent to the U-O press was below the lower limit of the present application, austenitization did not occur during reheating, so the area ratio of MA was 5% of the lower limit. As a result, the tensile strength was low, and the ratio of 1.5% proof stress to 0.5% proof strength did not reach the target of the present invention. Conversely, in Comparative Example 1-4 in which the reheating temperature exceeded the upper limit of the present application, MA reversibly transformed into austenite entirely by reheating, then bainite transformed during air cooling, and MA having a large aspect ratio between bainite laths. Generated. As a result, the product of tensile strength and uniform elongation was less than 7500.

  In Comparative Example 7, in which the steel slab heating temperature during hot rolling was lower than the lower limit of the present invention, the steel slab was not completely austenitic, and the remaining ferrite phase remained until the end even after rolling, forming, and heating history. As a result of the influence of MA formation after reheating and the MA fraction on the ferrite grain boundary being below the range of the present invention, the product of tensile strength and uniform elongation was less than 7500. Similarly, in Comparative Example 8 in which the rolling end temperature during hot rolling was lower than the lower limit of the present invention, the MA fraction on the ferrite grain boundary was lower than the range of the present invention. And the uniform elongation were less than 7500.

  Comparative Example No. in which the amount of C in the base material part exceeded the upper limit of the present invention. In No. 9, the area ratio of MA exceeded the upper limit. As a result, the uniform elongation decreased, and the product of the tensile strength and the uniform elongation was less than 7500. Comparative Example No. in which the amount of Si in the base material part exceeded the upper limit of the present invention. No. 10, the amount of Si in the weld metal also exceeded the upper limit, and as a result of the increase in the MA area ratio in the weld metal, the weld metal Charpy absorbed energy decreased.

  Comparative Example No. in which the amount of Mn in the base material part was below the lower limit of the present invention. In No. 11, the area ratio of MA was outside the range of the present invention, so the base material tensile strength was low, and the ratio of 1.5% proof stress to 0.5% proof stress was lowered. Comparative Example No. in which the Nb content of the steel exceeded the upper limit of the present invention. No. 12, the Nb content of the weld metal also exceeded the upper limit of the present invention, and the MA area ratio also deviated from the range of the present invention, so that the weld metal Charpy absorbed energy decreased.

  In Comparative Examples 2-a, 2-b, 2-c, 2-d, 2-e, 2-f, 2-g, and 2-h, the chemical components of the weld metal are outside the scope of the present invention. However, although the base metal part satisfies the target mechanical properties, the weld metal microstructure is outside the scope of the present invention, or as a result of excessive TiO or precipitation hardening of Nb or V, both are weld metal. Charpy absorbed energy decreased.

Claims (3)

The composition of the base material is mass%,
C: more than 0.03% to 0.06%,
Si: 0.1% or less,
Mn: 1.0-1.7%,
Al: 0.003 to 0.08%,
Nb: 0.01-0.04%,
Ti: 0.005 to 0.025%,
Further Cu: 0.1-0.5%,
Ni: 0.1 to 0.5%,
Mo: 0.1 to 0.5%,
Cr: 0.1 to 0.5%,
V: 0.003-0.04%,
1 type or 2 types or more, and the balance Fe and unavoidable impurities,
The component composition of the weld metal is mass%,
C: 0.06 to 0.08%,
Si: 0.2 to 0.5%
Mn: 1.3-1.8%
Al: 0.03% or less,
B: 0.001 to 0.003%,
Nb: 0.005 to 0.025%,
Ti: 0.015-0.040%,
Cu: 0.1% or less,
V: 0.03% or less,
O: 0.015-0.04%,
N: 0.01% or less,
In addition, Ni: 0.1 to 0.4%,
Mo: 0.05-0.2%
Cr: 0.1 to 0.2%
Containing one or more of
The balance Fe and inevitable impurities,
The base material portion is an island-shaped martensite having an average aspect ratio of 2.0 or less in which the first phase is ferrite and the second phase is dispersed in an area ratio of 5 to 20% in the first phase. 90% or more of martensite has a microstructure in the ferrite grain boundaries,
The weld metal part has a microstructure in which the area ratio of acicular ferrite is 80% or more and the area ratio of island martensite is 5% or less,
A high-strength welded steel pipe with high uniform elongation and excellent low temperature toughness at the weld. The component composition of the base material part is further mass%,
Ca: 0.0005 to 0.01%,
REM: 0.0005 to 0.02%,
Zr: 0.0005 to 0.01%,
Mg: 0.0005 to 0.01%,
The high strength welded steel pipe having high uniform elongation according to claim 1 and excellent in low temperature toughness of the welded portion. A method for producing a high-strength welded steel pipe having a high uniform elongation according to claim 1 or 2 and having excellent welded portion low temperature toughness ,
After reheating to Ac ₃ or higher, hot rolling at a rolling end temperature Ar ₃ or higher, and then forming a steel plate obtained by air cooling into a cylindrical shape by cold forming, followed by rapid heating to Ac ₁ or higher and Ac ₃ or lower Then, after cooling to room temperature by air cooling or water cooling, the end is welded, and finally the pipe is expanded, and a high strength welded steel pipe with high uniform elongation and excellent low temperature toughness at the weld is manufactured. Method.