LONGITUDINAL SEAM WELDED STEEL PIPE

Abstract

The present invention relates to steel pipe excellent in toughness of the weld metal part at a low temperature obtained by submerged arc welding in the longitudinal direction from both the inside and outside surfaces having strengths of the X60 to X70 class. The steel pipe of the present invention is a pipe having weld zones welded in a longitudinal direction at an inside surface and outside surface, wherein the tensile strength of the base metal is 480 to 620 MPa, the weld metal has a predetermined composition of constituents, when % X expresses a content of an element X in the weld metal, Pcm defined by Pcm=% C+% Si/30+(% Mn+% Cu+% Cr)/20+% Ni/60+% Mo/15+% V/10+5% B is 0.2% or less, Ceq defined by Ceq=% C+% Mn/6+(% Cr+% Mo+% V)/5+(% Ni+% Cu)/15 is 0.35 to 0.45%, defined by =(1.5(% O0.89% Al)+3.4% N% Ti)1000 is 20 to 40, and % Al/% O is 0.3 to 0.8.

Claims

1. A longitudinal seam welded steel pipe having weld zones welded at an inside surface and outside surface in a longitudinal direction, a chemical composition of a base metal of the steel pipe containing, by mass %, C: 0.01 to 0.1%, Si: less than 0.5%, Mn: 0.5 to 2.0%, P: 0.015% or less, S: 0.01% or less, Al: 0.01 to 0.05%, Ti: 0.005 to 0.03%, N: 0.002 to 0.006%, O: 0.005% or less, Mg: 0 to 0.01%, Ca: 0 to 0.03%, Ni: 0 to 0.6%, Cr: 0 to 0.5%, Cu: 0 to 0.5%, Mo: 0 to 0.4%, Nb: 0 to 0.06%, B: 0 to 0.002%, V: 0 to 0.06% and a balance of Fe and impurities, a tensile strength of the base metal being 480 to 620 MPa, a chemical composition of a weld metal of the steel pipe containing, by mass %, C: 0.03 to 0.10%, Si: 0.03 to 0.50%, Mn: 0.5 to 2.0%, P: 0.015% or less, S: 0.010% or less, Al: 0.001 to 0.030%, Ti: 0.005 to 0.040%, N: 0.002 to 0.006%, B: 0 to 0.035%, O: 0.015 to 0.055%, Ni: 0 to 0.60%, Cr: 0 to 0.50%, Cu: 0 to 0.50%, Mo: 0 to 0.40%, V: 0 to 0.06%, Ca: 0 to 0.005%, Mg: 0 to 0.010%, Nb: 0 to 0.060% and a balance of Fe and impurities, wherein when % X expresses a content of an element X in the weld metal, Pcm defined by Pcm=% C+% Si/30+(% Mn+% Cu+% Cr)/20+% Ni/60+% Mo/15+% V/10+5% B is 0.2% or less, Ceq defined by Ceq=% C+% Mn/6+(% Cr+% Mo+% V)/5+(% Ni+% Cu)/15 is 0.35 to 0.45%, defined by =(1.5(% O0.89% Al)+3.4% N% Ti)1000 is 20 to 40, and % Al/% O is 0.3 to 0.8.

2. The longitudinal seam welded steel pipe according to claim 1 wherein the satisfies 1000% O101000% O+1.

3. The longitudinal seam welded steel pipe according to claim 1, wherein the microstructure of the weld metal comprises, by area ratio, acicular ferrite 70% or more, grain boundary ferrite 15% or less, and martensite-austenite constituent 3% or less and has an EBSD grain size of 10 m or less.

4. The longitudinal seam welded steel pipe according to claim 1 wherein a tensile strength of the weld metal is 1.05 times or more of tensile strength of the base metal.

5. The longitudinal seam welded steel pipe according to claim 1, wherein the hardness of the weld metal is larger than the hardness of the base metal and a difference of the same is 10 Hv or more.

6. The longitudinal seam welded steel pipe according to claim 1, wherein a Charpy absorption energy at 10 C. of the weld metal is 100 J or more.

7. The longitudinal seam welded steel pipe according to claim 1, wherein a Charpy absorption energy at 1300% O60( C.) of the weld metal is 100 J or more.

8. The longitudinal seam welded steel pipe according to claim 2, wherein the microstructure of the weld metal comprises, by area ratio, acicular ferrite 70% or more, grain boundary ferrite 15% or less, and martensite-austenite constituent 3% or less and has an EBSD grain size of 10 m or less.

9. The longitudinal seam welded steel pipe according to claim 2 wherein a tensile strength of the weld metal is 1.05 times or more of tensile strength of the base metal.

10. The longitudinal seam welded steel pipe according to claim 3 wherein a tensile strength of the weld metal is 1.05 times or more of tensile strength of the base metal.

11. The longitudinal seam welded steel pipe according to claim 2, wherein the hardness of the weld metal is larger than the hardness of the base metal and a difference of the same is 10 Hv or more.

12. The longitudinal seam welded steel pipe according to claim 3, wherein the hardness of the weld metal is larger than the hardness of the base metal and a difference of the same is 10 Hv or more.

13. The longitudinal seam welded steel pipe according to claim 4, wherein the hardness of the weld metal is larger than the hardness of the base metal and a difference of the same is 10 Hv or more.

14. The longitudinal seam welded steel pipe according to claim 2, wherein a Charpy absorption energy at 10 C. of the weld metal is 100 J or more.

15. The longitudinal seam welded steel pipe according to claim 3, wherein a Charpy absorption energy at 10 C. of the weld metal is 100 J or more.

16. The longitudinal seam welded steel pipe according to claim 4, wherein a Charpy absorption energy at 10 C. of the weld metal is 100 J or more.

17. The longitudinal seam welded steel pipe according to claim 5, wherein a Charpy absorption energy at 10 C. of the weld metal is 100 J or more.

18. The longitudinal seam welded steel pipe according to claim 2, wherein a Charpy absorption energy at 1300% O60( C.) of the weld metal is 100 J or more.

19. The longitudinal seam welded steel pipe according to claim 3, wherein a Charpy absorption energy at 1300% O60( C.) of the weld metal is 100 J or more.

20. A longitudinal seam welded steel pipe having weld zones welded at an inside surface and outside surface in a longitudinal direction, a chemical composition of a base metal of the steel pipe comprising, by mass %, C: 0.01 to 0.1%, Si: less than 0.5%, Mn: 0.5 to 2.0%, P: 0.015% or less, S: 0.01% or less, Al: 0.01 to 0.05%, Ti: 0.005 to 0.03%, N: 0.002 to 0.006%, O: 0.005% or less, Mg: 0 to 0.01%, Ca: 0 to 0.03%, Ni: 0 to 0.6%, Cr: 0 to 0.5%, Cu: 0 to 0.5%, Mo: 0 to 0.4%, Nb: 0 to 0.06%, B: 0 to 0.002%, V: 0 to 0.06% and a balance of Fe and impurities, a tensile strength of the base metal being 480 to 620 MPa, a chemical composition of a weld metal of the steel pipe comprising, by mass %, C: 0.03 to 0.10%, Si: 0.03 to 0.50%, Mn: 0.5 to 2.0%, P: 0.015% or less, S: 0.010% or less, Al: 0.001 to 0.030%, Ti: 0.005 to 0.040%, N: 0.002 to 0.006%, B: 0 to 0.035%, O: 0.015 to 0.055%, Ni: 0 to 0.60%, Cr: 0 to 0.50%, Cu: 0 to 0.50%, Mo: 0 to 0.40%, V: 0 to 0.06%, Ca: 0 to 0.005%, Mg: 0 to 0.010%, Nb: 0 to 0.060% and a balance of Fe and impurities, wherein when % X expresses a content of an element X in the weld metal, Pcm defined by Pcm=% C+% Si/30+(% Mn+% Cu+% Cr)/20+% Ni/60+% Mo/15+% V/10+5% B is 0.2% or less, Ceq defined by Ceq=% C+% Mn/6+(% Cr+% Mo+% V)/5+(% Ni+% Cu)/15 is 0.35 to 0.45%, defined by =(1.5(% O0.89% Al)+3.4% N% Ti)1000 is 20 to 40, and % Al/% O is 0.3 to 0.8.

Description

BRIEF DESCRIPTION OF DRAWINGS

[0017] FIG. 1 gives views explaining amounts in the weld metal and low temperature toughness, wherein (a) shows the relationship between the amount of O and and (b) shows the relationship between and the absorption energy at 10 C.

[0018] FIG. 2 gives examples of structures of the weld metal, wherein (a) and (b) show the structures of the weld metal of longitudinal seam welded steel pipes of the present invention and (c) and (d) show the structures of the weld metal of longitudinal seam welded steel pipes of conventional examples.

DESCRIPTION OF EMBODIMENTS

[0019] Below, embodiments of the present invention will be explained in detail.

[0020] To start, the chemical composition of the weld metal will be explained. Note that, below, the % relating to the chemical composition will be deemed to indicate mass %.

[0021] C: 0.03 to 0.10%

[0022] C is an element required for securing strength of steel. 0.03% or more must be contained. If the amount of C is large, at the weld seam part, weld high temperature cracking easily occurs, so the upper limit is made 0.10%. C is preferably 0.05% to 0.065%.

[0023] Si: 0.03 to 0.50%

[0024] Si prevents blowholes, so 0.03% or more must be contained. If the amount of S is large, martensite-austenite constituent easily form and low temperature toughness is made to remarkably deteriorate, so the upper limit is made 0.50%. Si is preferably 0.15% to 0.25%.

[0025] Mn: 0.5 to 2.0%

[0026] Mn acts as an element improving the hardenability. To make the weld metal a structure of mainly acicular ferrite, 0.5% or more has to be contained. If the amount of Mn is large, coarse MnS is formed and becomes starting points of fracture, so the upper limit is made 2.0%. Mn is preferably 1.2% to 1.5%.

[0027] P: 0.015% or Less (Including 0%)

[0028] S: 0.010% or Less (Including 0%)

[0029] P and S are both impurities and elements causing deterioration of the toughness of the joint. P is restricted to 0.015% or less, while S is restricted to 0.010% or less. The contents of these are preferably as low as possible. Preferably, P is 0.008% or less. Preferably, S is 0.003% or less.

[0030] Al: 0.001 to 0.030%

[0031] Al acts as a deoxidizing element and is necessary for control of the amount of oxygen for causing dispersion of the Ti oxides effective as sites for formation of acicular ferrite nuclei. If considering dilution by the base metal, 0.001% or more has to be contained. If the amount of Al is over 0.030%, formation of oxides is inhibited and the toughness cannot be secured, so the upper limit is made 0.030%. Preferably, the content is 0.010% to 0.015%.

[0032] Ti: 0.005 to 0.040%

[0033] Ti reacts with the oxygen in the weld metal to form Ti oxides acting as nuclei for acicular ferrite. These oxides are made to finely disperse in large numbers in the weld metal, so 0.005% or more has to be contained. If the amount of Ti becomes excessive, the Ti oxides agglomerate and coarsen and the ability to form nuclei of acicular ferrite falls. Further, the Ti oxides become starting points of fracture resulting in toughness not being able to be obtained, so the upper limit is made 0.040%. Preferably, the content is 0.009% to 0.015%.

[0034] N: 0.002 to 0.006%

[0035] N is an element effective for adjusting the amount of Ti effective for forming acicular ferrite structures, so 0.002% or more has to be contained. However, if over 0.006%, the solid solution N remaining without reacting with the Ti causes the toughness to remarkably fall, so the upper limit is preferably made 0.006%. Preferably, the content is 0.003% to 0.004%.

[0036] B: 0 to 0.035% or Less

[0037] B promotes the formation of acicular ferrite by B in the solid solution state suppressing the formation of grain boundary ferrite of the weld metal. B need not be contained, but to obtain this effect, 0.0001% or more is preferably contained. If the amount of B exceeds 0.035, the strength becomes too high and the toughness falls, so the upper limit is made 0.035%. B may be added to the weld metal from any of the thick plate base metal, flux, or wire. For example, if the base metal is steel to which B is not added, a flux containing B oxides may be used. B is preferably 0.0005% to 0.010%.

[0038] O: 0.015 to 0.055%

[0039] O is an element required for forming oxides acting as nuclei for acicular ferrite. For this reason, 0.015% or more has to be contained. If the amount of O is over 0.055%, the toughness falls due to the excessive formation, agglomeration, and coarsening of the oxides, so the upper limit is made 0.055%. Preferably, the content is 0.020% to 0.030%.

[0040] Ni: 0 to 0.60%

[0041] Ni is an element able to improve the strength of the weld metal without causing a drop in the toughness. Ni is not necessarily contained. If exceeding 0.60%, the effect becomes saturated, so the upper limit is made 0.60%.

[0042] Cr: 0 to 0.50%

[0043] Cr is an element able to improve the strength of the weld metal. Inclusion of Cr is not essential. If over 0.50%, the effect becomes saturated, so the upper limit is made 0.50%.

[0044] Cu: 0 to 0.50%

[0045] Cu is an element able to improve the strength of the weld metal. Inclusion of Cu is not essential. If over 0.50%, the effect becomes saturated, so the upper limit is made 0.50%.

[0046] Mo: 0 to 0.40%

[0047] Mo is an element able to improve the strength of the weld metal. Inclusion of Mo is not essential. If over 0.40%, the effect becomes saturated, so the upper limit is made 0.40%.

[0048] V: 0 to 0.06%

[0049] V is an element able to improve the strength of the weld metal. Inclusion of V is not essential. If over 0.06%, the effect becomes saturated, so the upper limit is made 0.06%.

[0050] Ca: 0 to 0.005%

[0051] Ca is an element effective for improvement of the ductility and refinement of the structure by control of the morphology. Inclusion of Ca is not essential. If the amount of Ca is large the sulfides and oxides become coarser and the ductility and toughness deteriorate, so the upper limit is made 0.005%.

[0052] Mg: 0 to 0.010%

[0053] Mg forms MgS or MgAl.sub.2O.sub.4 which act as pinning particles. Inclusion of Mg is not essential. To suppress growth of austenite grains at the weld metal, 0.001% or more is preferably included. If over 0.010%, the effect becomes saturated, so the upper limit is made 0.010%. Preferably, the content is 0.0015% to 0.0025%.

[0054] Nb: 0 to 0.06%

[0055] Nb is an element effective for causing the presence of solid solution B effective for improving the strength and suppressing grain boundary ferrite. Inclusion of Nb is not essential. If the amount of Nb exceeds 0.06%, martensite-austenite constituent easily form and the toughness falls, so the upper limit is made 0.06%. Preferably, the content is 0.02%.

[0056] The balance of the weld metal is Fe and impurities. The impurities mean constituents entering from the weld wire, flux, steel plate, surrounding atmosphere, etc. in the process of welding and mean constituents not intentionally contained.

[0057] Specifically, P, S, N, Sb, Sn, W, Co, As, Pb, Bi, and H may be mentioned. Among these, P and S, as explained above, have to be controlled so that P: 0.015% or less and S: 0.01% or less.

[0058] Regarding other elements, usually Sb, Sn, W, Co, and As may be contained in 0.1% or less, Pb and Bi may be contained in 0.005% or less, and H may be contained in 0.0005% or less as unavoidable impurities, but if in the usual ranges, do not have to be particularly controlled.

[0059] The constituents of the weld metal in the present embodiment further have to satisfy the relationships explained below.

[0060] Pcm: 0.2% or Less

[0061] The composition of constituents of the weld metal has to be one where the Pcm expressed by the following formula becomes 0.2% or less. The % X in the formula means the content (mass %) of the element X in the weld metal (same in following explanation). Further, an element not added to the weld metal is counted as zero (same in following explanation).

Pcm=% C+% Si/30+(% Mn+% Cu+% Cr)/20+% Ni/60+% Mo/15+% V/10+5% B

[0062] Pcm is called the weld sensitivity and quantitatively evaluates the effects of the chemical constituents of the steel material on the low temperature cracking. If Pcm is over 0.2%, low temperature cracking easily occurs, so the upper limit is made 0.2%.

[0063] Ceq: 0.35 to 0.45%

[0064] The composition of constituents of the weld metal has to be one where the Ceq expressed by the following formula becomes 0.35 to 0.45%.

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

[0065] Regarding the hardenability due to the effect of weld heat of the base metal, Ceq is obtained by respectively converting the hardenabilities of the different alloy elements to amounts of C and totaling them up. To make the weld metal reach the desired tensile strength, Ceq is controlled to 0.35 to 0.45%. Preferably, Ceq is made 0.40 to 0.43%.

[0066] : 2040

[0067] The composition of constituents of the weld metal of the weld joint has to have an expressed by the following formula of 20 to 40.

=(1.5(% O0.89% Al)+3.4% N% Ti)1000

[0068] is a parameter showing the effective ability to form acicular ferrite based on the stoichiometric ratios of Al, O, and Ti, N. By controlling to 20 to 40 in range, the ability to form acicular ferrite is improved.

[0069] If is less than 20, either of the amounts of Al and Ti becomes excessively large or the amounts of N and O become excessively small, so the ability to form acicular ferrite remarkably decreases. If is over 40, either of the amounts of Al and Ti becomes excessively small or the amounts of N and O become excessively large, so the ability to form acicular ferrite remarkably decreases.

[0070] % Al/% O: 0.30 to 0.80%

[0071] % Al/% O is the ratio of the amount of Al and the amount of O and is an indicator showing the oxygen potential after the end of deoxidation of the aluminum. By controlling % Al/% O to 0.3 to 0.80, the amount of formation of acicular ferrite can be raised.

[0072] If the % Al/% O ratio is less than 0.30, the amount of O becomes excessively large and dissolved oxygen not forming Ti oxides lowers the cleanliness of the steel, so the toughness falls. On the other hand, if % Al/% O is over 0.80, the amount of Al becomes excessively large, the amount of O bonding with Ti is decreased, the Ti oxides acting as nuclei for acicular ferrite are decreased and the toughness falls. Accordingly, % Al/% O is made 0.30 to 0.80.

[0073] Next, the preferable metal structure of the weld metal will be explained.

[0074] If making the constituents and parameters of the weld metal the above ranges and welding steel plate having an X60 to X70 class strength by submerged arc welding by the weld heat input 15 to 110 kJ/cm, the metal structure of the weld metal becomes a structure mainly comprised of acicular ferrite. The UO steel pipe covered by the present invention has a plate thickness of 6 to 40 mm or so. To weld steel plate of such a thickness by submerged arc welding, the welding is performed by a weld heat input of 15 to 110 kJ/cm in range. This being so, the cooling rate of the weld metal is determined. The metal structure of the weld metal of the final pass becomes the following structure. The ratios shown below are area ratios.

[0075] Acicular Ferrite: 70% or More

[0076] Acicular ferrite is a pin-shaped ferrite structure having Ti-based oxides as nuclei. The larger the ratio, the finer the units of fracture of the weld metal part. To obtain this effect, the acicular ferrite is preferably made 70% or more.

[0077] Grain Boundary Ferrite: 15% or Less

[0078] The grain boundary ferrite is one type of brittle phase. It becomes the starting point of fracture and a cause of drop of the toughness. For this reason, the grain boundary ferrite is preferably made 15% or less.

[0079] Martensite-Austenite Constituent: 3% or Less

[0080] A martensite-austenite constituent is one type of brittle phase. It is extremely high in hardness, so becomes the starting point of fracture and a cause of drop of the toughness. For this reason, martensite-austenite constituent are preferably made 3% or less.

[0081] EBSD Grain Size: 10 m or Less

[0082] The EBSD (electron back scatter diffraction) particle size is the size of crystal grains forming the basis for the units of fracture. If the EBSD grain size is 10 m or less, the units of fracture become finer. This is preferable from the viewpoint of securing toughness at low temperature.

[0083] By making the weld metal one with constituents satisfying the above condition and welding by a weld heat input of 15 to 110 kJ/cm, it is possible to obtain a submerged arc welded joint with a tensile strength of the weld metal of 480 to 620 MPa and a Charpy absorption energy at 10 C. of the weld metal measured in accordance with JIS Z2242 of 100 J or more.

[0084] The low temperature toughness differs depending on the parameter showing the effective ability to form acicular ferrite. There is a more preferable range of depending on the concentration of oxygen in the weld metal. Specifically, it is preferable that 1000% O101000% O+1 (FIG. 1). By adjusting to this range, the ability to form acicular ferrite is improved, the low temperature toughness is improved, and a submerged arc welded joint with a Charpy absorption energy at 1300% O60( C.) of 100 J or more can be obtained.

[0085] Further, by making the weld metal one with constituents satisfying the above condition and welding it by a weld heat input of 15 to 110 kJ/cm, the hardness of the weld metal becomes larger than the hardness of the base metal. Preferably, the difference becomes 10 Hv or more in terms of Vickers hardness. Furthermore, the tensile strength of the weld metal preferably becomes 1.05 times or more of the tensile strength of the base metal.

[0086] The base metal is not particularly limited in structure so long as steel plate having a X60 to X70 class strength (steel plate with a tensile strength of the base metal of 480 to 620 MPa). Below, the constituents of the steel plate having a strength of the X60 to X70 class suitable as the base metal of the longitudinal seam welded steel pipe of the present invention will be shown.

[0087] C: 0.01 to 0.1%

[0088] C is effective for improving the strength of steel and is included in 0.01% or more. If the amount of C is too large, the low temperature toughness of the base metal and HAZ deteriorate and, further, the weldability deteriorates, so the amount of C is made 0.1% or less. Preferably, the content is 0.03 to 0.07%.

[0089] Si: Less than 0.5%

[0090] Si is an element required for deoxidation. If the amount of Si is large, martensite-austenite constituent easily form, and the low temperature toughness is made to remarkably deteriorate, so the amount of Si is made less than 0.5%. Preferably, the content is less than 0.35%. The deoxidation is also performed by Al and Ti, so addition of Si is not essential.

[0091] Mn: 0.5 to 2.0%

[0092] Mn acts as an element improving hardenability. To obtain this effect, 0.5% or more is included. If the amount of Mn is large, the hardenability of the steel increases and the HAZ toughness and weldability deteriorate. Furthermore, center segregation of the continuous cast steel slab is aided and the base metal deteriorates in low temperature toughness, so the amount of Mn is made 2.0% or less. Preferably, the content is 1.0 to 1.8%.

[0093] P: 0.015% or Less

[0094] S: 0.01% or Less

[0095] P and S are both impurities and elements causing deterioration of the toughness of the joint. The contents of these are preferably as low as possible. P is made 0.015% or less, while S is made 0.01% or less. Preferably, P is 0.008% or less. Preferably, S is 0.003% or less.

[0096] Al: 0.01 to 0.05%

[0097] Al is an element contained in the steel material as a deoxidizing material. Al further bonds with N to form AlN and suppress the coarsening of the crystal grains at the hardened part of the steel material. If the content of Al is too low, this effect cannot be obtained, so 0.01% or more is included. If the content of Al is too high, the high frequency hardenability of the steel material falls, so the amount of Al is made 0.05% or less. Preferably, the content is 0.02 to 0.04%.

[0098] Ti: 0.005 to 0.03%

[0099] Ti forms fine TiN in the steel. These alone or as composite inclusions with Mg (MgAl.sub.2O.sub.4) oxides act as pinning particles. As a result, coarsening of the austenite grains of the HAZ is suppressed, the microstructure is refined, and the low temperature toughness is improved. To obtain this effect, Ti is included in 0.005% or more. If the amount of Ti becomes greater, the Ti oxides agglomerate and coarsen and the toughness deteriorates, so the amount of Ti is made 0.03% or less. Preferably, the content is 0.01 to 0.02%.

[0100] N: 0.002 to 0.006%

[0101] N is an element bonding with Ti to form TiN and is included in 0.002% or more. If the amount of N is large, the solid solution N not bonded with the Ti lowers the toughness, so the amount of N is made 0.006% or less. Preferably, the content is 0.003 to 0.005%.

[0102] O: 0.005% or Less

[0103] O is an element forming pinning particles. However, if O is included, the cleanliness of the steel falls, so the smaller the content the better. The content is made 0.005% or less. Preferably, the content is 0.003% or less.

[0104] Mg: 0 to 0.01%

[0105] Mg is an element forming inclusions such as MgAl.sub.2O.sub.4 and MgS. MgAl.sub.2O.sub.4 precipitates on the TiN. These inclusions act as pinning particles. They suppress coarsening of the austenite grains of the HAZ to refine the microstructure and improve the low temperature toughness. If the amount of Mg becomes greater, the effect becomes saturated. Mg does not necessarily have to be contained in the base metal of the longitudinal seam welded steel pipe. The preferable amount of Mg is 0 to 0.01%.

[0106] Ca: 0 to 0.03%

[0107] Ca is an element controlling the morphology of the sulfide-based inclusions and improving the low temperature toughness. Further, it forms phosphides and sulfides to substantively reduce the concentrations of P and S and improve the sulfide stress fraction resistance. If the amount of Ca is large, the CaOCaS become large clusters or inclusions which are liable to have a detrimental effect on the toughness. Ca does not necessarily have to be contained in the base metal of the longitudinal seam welded steel pipe. The preferable amount of Ca is 0 to 0.03%.

[0108] Ni: 0 to 0.6%

[0109] Ni is an element able to raise the strength of the base metal without causing a drop in the toughness. If the amount of Ni becomes greater, the effect becomes saturated. Ni does not necessarily have to be contained in the base metal of the longitudinal seam welded steel pipe. The preferable amount of Ni is 0 to 0.6%.

[0110] Cr: 0 to 0.5%

[0111] Cr is an element able to improve the strength of the base metal. If the amount of Cr becomes greater, the effect becomes saturated. Cr does not necessarily have to be contained in the base metal of the longitudinal seam welded steel pipe. The preferable amount of Cr is 0 to 0.5%.

[0112] Cu: 0 to 0.5%

[0113] Cu is an element able to improve the strength of the base metal. If the amount of Cu increases, the effect becomes saturated. Cu does not necessarily have to be contained in the base metal of the longitudinal seam welded steel pipe. The preferable amount of Cu is 0 to 0.5%.

[0114] Mo: 0 to 0.4%

[0115] Mo is an element able to improve the strength of the base metal. If the amount of Mo becomes greater, the effect becomes saturated and the toughness falls. Mo does not necessarily have to be contained in the base metal of the longitudinal seam welded steel pipe. The preferable amount of Mo is 0 to 0.4%.

[0116] Nb: 0 to 0.060%

[0117] Nb is an element improving the strength of the base metal. If the amount of Nb becomes greater, the martensite-austenite constituent more easily form and the toughness falls. Nb does not necessarily have to be contained in the base metal of the longitudinal seam welded steel pipe. The preferable amount of Nb is 0 to 0.40%.

[0118] B: 0 to 0.002%

[0119] B is an element effective for improvement of the hardenability of the base metal and suppression of formation of grain boundary ferrite. If the amount of B becomes greater, the effect becomes saturated. B does not necessarily have to be contained in the base metal of the longitudinal seam welded steel pipe. The preferable amount of B is 0 to 0.002%.

[0120] V: 0 to 0.06%

[0121] V is an element improving the strength of the base metal. If the amount of V becomes greater, the yield ratio can be raised by the precipitation hardening. V does not necessarily have to be contained in the base metal of the longitudinal seam welded steel pipe. The preferable amount of V is 0 to 0.06%.

[0122] The balance of elements other than those explained above is comprised of Fe and impurities. The impurities mean constituents contained in the raw materials or entering in the process of manufacture and not intentionally included in the steel.

[0123] Specifically, P, S, O, Sb, Sn, W, Co, As, Pb, Bi, and H may be mentioned. Among these, P, S, and O are preferably controlled so as to become the above preferable ranges.

[0124] Regarding other elements, usually Sb, Sn, W, Co, and As can enter in 0.1% or less, Pb and Bi can enter in 0.005% or less, and H can enter in 0.0005% or less as unavoidable impurities, but do not particularly have to be controlled if in the usual ranges.

[0125] The method of production of the steel plate used as the base metal is not particularly limited. A general method of production of steel plate having a strength of the X60 to X70 class may be used. A longitudinal seam welded steel pipe is obtained by joining the ends of thick steel plate serving as the base metal having a thickness of 6 to 40 mm or so by submerged arc welding. UOE steel pipe and JCOE steel pipe are examples of this.

[0126] The welding method will be explained in detail.

[0127] First, the above thick steel plate is formed with a groove of a predetermined shape. The shape of the groove is not particularly limited. A longitudinal seam welded steel pipe can be produced by forming a groove shape enabling welding from the two top and bottom surfaces of the end parts of the thick steel plate, for example, an X-shaped groove, making the end parts abut, completing the submerged arc welding from the inside surface side, then performing submerged arc welding from the outside surface side in the longitudinal direction.

[0128] Further, flux is spread inside the groove and steel wire for submerged arc welding use is used to join the ends by large heat input submerged arc welding by a heat input of 15 to 110 kJ/cm. The flux and steel wire are not particularly limited. Known ones may be used. If using steel wire, as the flux, known bond flux, melt flux, etc. may be used. If possible to obtain the above constituents of the weld metal by this, weld metal excellent in toughness is obtained. Further, according to need, the flux may also be preheated before welding.

[0129] The method of submerged arc welding is not particularly limited. Multielectrode submerged arc welding is included. Any known welding method may be applied. The welding conditions are also not particularly limited.

Examples

[0130] Next, examples of the present invention will be explained. The conditions in the examples are illustrations of conditions employed for confirming the workability and effects of the present invention. The present invention is not limited to these illustration of conditions. The present invention can employ various conditions so long as not deviating from the gist of the present invention and achieving the object of the present invention.

[0131] Steel materials of various compositions of constituents were smelted and refined. The molten steel was continuously cast into slabs. These were heated to 1100 C., then hot rolled. The finishing temperature of the hot rolling was made 780 C. The steels were air cooled down to 750 C., then water cooled from 750 C. down to ordinary temperature to thereby prepare steel plates with various compositions of constituents and strengths of the X60 to X70 class. Table 1 shows the thicknesses, the compositions of constituents, and the tensile strengths of the steel plates.

TABLE-US-00001 TABLE 1 Steel Plate thickness Chemical constituents (mass %) plate (mm) C Si Mn P S Al Ti N O Mg A 38 0.060 0.240 1.55 0.008 0.0024 0.039 0.012 0.0048 0.0020 B 25 0.052 0.193 1.58 0.010 0.0012 0.024 0.011 0.0052 0.0021 C 20 0.075 0.050 1.41 0.010 0.0030 0.030 0.013 0.0055 0.0020 0.003 D 30 0.046 0.220 1.45 0.005 0.0020 0.018 0.025 0.0040 0.0014 E 40 0.015 0.200 1.85 0.009 0.0020 0.030 0.012 0.0044 0.0020 F 6 0.063 0.450 1.25 0.010 0.0020 0.042 0.012 0.0037 0.0019 0.002 G 25 0.095 0.200 0.80 0.009 0.0030 0.035 0.014 0.0039 0.0022 H 32 0.030 0.150 1.75 0.007 0.0020 0.015 0.020 0.0042 0.0025 I 35 0.055 0.170 1.63 0.010 0.0020 0.010 0.010 0.0040 0.0020 J 38 0.063 0.200 1.30 0.008 0.0030 0.019 0.006 0.0022 0.0019 0.002 K 20 0.042 0.130 1.20 0.007 0.0002 0.020 0.010 0.0040 0.0020 L 18 0.045 0.180 1.30 0.007 0.0005 0.025 0.009 0.0035 0.0022 0.001 M 18 0.055 0.170 1.75 0.007 0.0009 0.016 0.012 0.0037 0.0023 N 20 0.060 0.150 1.25 0.006 0.0006 0.015 0.011 0.0034 0.0020 Steel Chemical constituents (mass %) TS plate Ca Cu Ni Cr Mo V Nb B Ceq Pcm (MPa) A 0.30 0.42 0.15 0.010 0.02 0.020 0.40 0.18 523 B 0.0023 0.02 0.02 0.29 0.136 0.020 0.40 0.16 524 C 0.35 0.35 0.015 0.36 0.17 499 D 0.0016 0.01 0.02 0.20 0.110 0.018 0.35 0.14 492 E 0.45 0.100 0.020 0.43 0.14 577 F 0.0020 0.25 0.25 0.300 0.01 0.012 0.37 0.18 513 G 0.30 0.300 0.015 0.0005 0.35 0.18 518 H 0.30 0.250 0.01 0.012 0.39 0.15 551 I 0.0010 0.20 0.20 0.02 0.015 0.36 0.16 500 J 0.0010 0.20 0.20 0.15 0.150 0.04 0.012 0.37 0.17 524 K 0.0020 0.30 0.30 0.020 0.32 0.13 501 L 0.0250 0.40 0.250 0.015 0.34 0.14 504 M 0.0280 0.25 0.019 0.40 0.16 555 N 0.0220 0.35 0.25 0.300 0.05 0.020 0.41 0.17 576

[0132] Next, an X-shaped groove was formed in each fabricated steel plate. This was shaped into a tube and welded by submerged arc welding at the inside surface side and outside surface side of the tube in that order using a known wire and flux to obtain a UO steel pipe. At the time of welding, the weld speed etc. were adjusted to give a heat input of 65 kJ/cm or so. The compositions of constituents of each steel plate and weld metal are shown using Tables 2 to 4.

TABLE-US-00002 TABLE 2 Steel Chemical constituents (mass %) plate C Si Mn P S Al Ti N O B Ex. 1 A 0.060 0.20 1.57 0.010 0.004 0.015 0.0115 0.0038 0.0190 0.0006 Ex. 2 A 0.060 0.20 1.57 0.010 0.004 0.0145 0.01 0.0045 0.0200 0.0006 Ex. 3 B 0.060 0.20 1.57 0.010 0.004 0.017 0.006 0.0049 0.0230 0.0006 Ex. 4 A 0.060 0.20 1.57 0.010 0.0040 0.0120 0.0250 0.0040 0.0180 0.0006 Ex. 5 A 0.060 0.25 1.51 0.010 0.0040 0.0130 0.0160 0.0037 0.0280 0.0032 Ex. 6 B 0.060 0.25 1.51 0.010 0.0040 0.0120 0.0150 0.0046 0.0270 0.0032 Ex. 7 A 0.060 0.25 1.51 0.010 0.0040 0.0180 0.0140 0.0044 0.0290 0.0032 Ex. 8 A 0.060 0.25 1.51 0.010 0.0040 0.0110 0.0105 0.0040 0.0300 0.0032 Ex. 9 A 0.055 0.22 1.41 0.005 0.0030 0.0180 0.0214 0.0055 0.0390 0.0025 Ex. 10 B 0.055 0.22 1.41 0.005 0.0030 0.0200 0.0180 0.0044 0.0420 0.0025 Ex. 11 A 0.055 0.22 1.41 0.005 0.0030 0.0200 0.0320 0.0058 0.0440 0.0025 Ex. 12 A 0.055 0.22 1.41 0.005 0.0030 0.0290 0.0400 0.0032 0.0400 0.0025 Comp. Ex. 1 A 0.060 0.20 1.57 0.010 0.0040 0.0135 0.0390 0.0021 0.0174 0.0006 Comp. Ex. 2 A 0.060 0.25 1.51 0.010 0.0040 0.0190 0.0390 0.0021 0.0240 0.0032 Comp. Ex. 3 B 0.060 0.25 1.51 0.010 0.0040 0.0130 0.0055 0.0055 0.0320 0.0032 Comp. Ex. 4 A 0.055 0.22 1.41 0.005 0.0030 0.0220 0.0399 0.0021 0.0280 0.0025 Comp. Ex. 5 A 0.055 0.22 1.41 0.005 0.0030 0.0120 0.0210 0.0045 0.0480 0.0025 Chemical constituents (mass %) Cu Ni Cr Mo V Nb Mg Ceq Pcm Al/O Ex. 1 0.15 0.30 0.13 0.12 0.006 0.40 0.18 0.79 9.895 Ex. 2 0.15 0.30 0.13 0.12 0.006 0.40 0.18 0.73 15.943 Ex. 3 0.15 0.30 0.13 0.12 0.006 0.40 0.18 0.74 22.465 Ex. 4 0.15 0.30 0.13 0.12 0.006 0.40 0.18 0.67 0.420 Ex. 5 0.20 0.10 0.13 0.01 0.02 0.021 0.36 0.18 0.46 21.225 Ex. 6 0.20 0.10 0.13 0.01 0.02 0.021 0.36 0.18 0.44 25.120 Ex. 7 0.20 0.10 0.13 0.01 0.02 0.021 0.36 0.18 0.62 20.430 Ex. 8 0.20 0.10 0.13 0.01 0.02 0.021 0.36 0.18 0.37 33.415 Ex. 9 0.24 0.40 0.10 0.020 0.35 0.17 0.46 31.770 Ex. 10 0.24 0.40 0.10 0.020 0.35 0.17 0.48 33.260 Ex. 11 0.24 0.40 0.10 0.020 0.35 0.17 0.45 27.020 Ex. 12 0.24 0.40 0.10 0.020 0.35 0.17 0.73 7.835 Comp. Ex. 1 0.15 0.30 0.13 0.12 0.006 0.40 0.18 0.78 23.783 Comp. Ex. 2 0.20 0.10 0.13 0.01 0.02 0.021 0.36 0.18 0.79 21.225 Comp. Ex. 3 0.20 0.10 0.13 0.01 0.02 0.021 0.36 0.18 0.41 43.845 Comp. Ex. 4 0.24 0.40 0.10 0.020 0.35 0.17 0.79 20.130 Comp. Ex. 5 0.24 0.40 0.10 0.020 0.35 0.17 0.25 50.280

TABLE-US-00003 TABLE 3 (Continued from Table 2) Steel Chemical constituents (mass %) plate C Si Mn P S Al Ti N O B Ex. 13 A 0.059 0.18 1.80 0.010 0.0030 0.0140 0.0080 0.0038 0.0180 0.0008 Ex. 14 A 0.056 0.12 1.65 0.010 0.0030 0.0140 0.0100 0.0045 0.0200 Ex. 15 B 0.035 0.40 1.48 0.010 0.0030 0.0150 0.0060 0.0055 0.0230 0.0031 Ex. 16 A 0.063 0.20 1.50 0.010 0.0040 0.0120 0.0320 0.0030 0.0180 Ex. 17 A 0.063 0.24 1.63 0.008 0.0024 0.0120 0.0210 0.0041 0.0270 0.0031 Ex. 18 A 0.056 0.18 1.46 0.010 0.0030 0.0150 0.0350 0.0046 0.0270 0.0028 Ex. 19 A 0.065 0.17 1.48 0.010 0.0030 0.0170 0.0140 0.0044 0.0290 0.0031 Ex. 20 B 0.063 0.20 1.50 0.010 0.0040 0.0170 0.0100 0.0040 0.0300 Ex. 21 A 0.063 0.15 1.60 0.007 0.0030 0.0200 0.0180 0.0044 0.0420 0.0020 Ex. 22 B 0.048 0.28 1.45 0.005 0.0030 0.0110 0.0250 0.0058 0.0370 Ex. 23 A 0.068 0.20 1.50 0.007 0.0030 0.0300 0.0380 0.0032 0.0400 Ex. 24 A 0.095 0.20 1.55 0.009 0.0020 0.0180 0.0150 0.0040 0.0350 0.0010 Comp. Ex. 6 A 0.050 0.05 1.60 0.010 0.0030 0.0120 0.0080 0.0038 0.0180 0.0008 Comp. Ex. 7 A 0.085 0.45 1.48 0.010 0.0030 0.0140 0.0100 0.0045 0.0200 Comp. Ex. 8 B 0.050 0.15 1.52 0.010 0.0030 0.0250 0.0060 0.0055 0.0230 0.0031 Comp. Ex. 9 A 0.063 0.19 1.50 0.010 0.0040 0.0050 0.0250 0.0030 0.0180 Comp. Ex. 10 A 0.063 0.24 1.63 0.008 0.0024 0.0120 0.0210 0.0041 0.0270 0.0031 Comp. Ex. 11 A 0.098 0.45 1.46 0.010 0.0030 0.0150 0.0350 0.0046 0.0270 0.0028 Comp. Ex. 12 B 0.065 0.17 1.48 0.010 0.0030 0.0250 0.0140 0.0044 0.0290 0.0031 Comp. Ex. 13 A 0.063 0.20 1.50 0.010 0.0040 0.0060 0.0120 0.0040 0.0300 Comp. Ex. 14 A 0.045 0.15 0.64 0.007 0.0030 0.0180 0.0150 0.0035 0.0420 0.0020 Comp. Ex. 15 B 0.095 0.45 1.45 0.005 0.0030 0.0250 0.0370 0.0058 0.0370 Comp. Ex. 16 A 0.068 0.20 1.50 0.007 0.0030 0.0290 0.0340 0.0032 0.0350 Comp. Ex. 17 A 0.085 0.20 1.55 0.009 0.0020 0.0090 0.0190 0.0040 0.0350 0.0010 Chemical constituents (mass %) Cu Ni Cr Mo V Nb Mg Ceq Pcm Al/O Ex. 13 0.15 0.31 0.13 0.14 0.011 0.44 0.19 0.78 13.230 Ex. 14 0.23 0.50 0.03 0.015 0.39 0.16 0.70 16.610 Ex. 15 0.40 0.30 0.40 0.010 0.41 0.19 0.65 27.175 Ex. 16 0.30 0.30 0.012 0.002 0.43 0.18 0.67 10.820 Ex. 17 0.40 0.40 0.01 0.015 0.39 0.20 0.44 17.420 Ex. 18 0.30 0.50 0.03 0.015 0.36 0.17 0.56 1.115 Ex. 19 0.30 0.35 0.010 0.36 0.18 0.59 21.765 Ex. 20 0.30 0.30 0.015 0.002 0.43 0.18 0.57 25.905 Ex. 21 0.15 0.10 0.20 0.30 0.020 0.45 0.20 0.48 33.260 Ex. 22 0.45 0.40 0.20 0.05 0.012 0.002 0.40 0.18 0.30 35.535 Ex. 23 0.30 0.30 0.005 0.44 0.18 0.75 7.170 Ex. 24 0.15 0.30 0.15 0.01 0.015 0.42 0.21 0.51 27.070 Comp. Ex. 6 0.25 0.30 0.40 0.14 0.020 0.46 0.18 0.67 15.900 Comp. Ex. 7 0.20 0.20 0.32 0.015 0.45 0.21 0.70 16.610 Comp. Ex. 8 0.40 0.30 0.45 0.010 0.44 0.20 1.09 13.825 Comp. Ex. 9 0.30 0.30 0.012 0.002 0.43 0.18 0.28 5.525 Comp. Ex. 10 0.40 0.40 0.20 0.30 0.01 0.015 0.49 0.23 0.44 17.420 Comp. Ex. 11 0.23 0.50 0.03 0.010 0.40 0.22 0.56 1.115 Comp. Ex. 12 0.40 0.35 0.015 0.36 0.19 0.86 11.085 Comp. Ex. 13 0.30 0.30 0.012 0.002 0.43 0.18 0.20 38.590 Comp. Ex. 14 0.28 0.25 0.28 0.30 0.020 0.30 0.14 0.43 35.870 Comp. Ex. 15 0.45 0.40 0.20 0.05 0.015 0.002 0.44 0.23 0.68 4.845 Comp. Ex. 16 0.30 0.30 0.012 0.44 0.18 0.83 9.335 Comp. Ex. 17 0.15 0.30 0.15 0.01 0.010 0.41 0.20 0.26 35.085

TABLE-US-00004 TABLE 4 (Continued from Table 3) Steel Chemical constituents (mass %) plate C Si Mn P S Al Ti N O B Comp. Ex. 18 A 0.020 0.20 1.50 0.010 0.0030 0.0130 0.0135 0.0038 0.0180 0.0008 Comp. Ex. 19 A 0.150 0.12 1.35 0.010 0.0030 0.0120 0.0130 0.0042 0.0190 0.0020 Comp. Ex. 20 A 0.060 0.24 1.63 0.008 0.0024 0.0100 0.0210 0.0041 0.0130 0.0031 Comp. Ex. 21 A 0.061 0.18 1.35 0.008 0.0024 0.0180 0.0270 0.0044 0.0590 0.0031 Comp. Ex. 22 A 0.053 0.24 1.63 0.008 0.0024 0.0120 0.0030 0.0041 0.0270 0.0031 Comp. Ex. 23 A 0.068 0.18 1.50 0.008 0.0024 0.0100 0.0500 0.0044 0.0280 0.0031 Comp. Ex. 24 A 0.040 0.15 1.57 0.010 0.0030 0.0400 0.0135 0.0038 0.0540 0.0008 Comp. Ex. 25 A 0.045 0.20 1.52 0.010 0.0030 0.0120 0.0135 0.0080 0.0170 0.0008 Ex. 25 C 0.052 0.12 1.35 0.010 0.0030 0.0070 0.0120 0.0040 0.0200 0.0003 Ex. 26 D 0.031 0.22 1.25 0.010 0.0030 0.0090 0.0200 0.0044 0.0210 Ex. 27 E 0.063 0.25 1.40 0.010 0.0040 0.0130 0.0180 0.0038 0.0190 0.0010 Ex. 28 F 0.080 0.21 0.60 0.007 0.0030 0.0150 0.0300 0.0042 0.0210 0.0005 Ex. 29 G 0.058 0.23 1.35 0.005 0.0030 0.0130 0.0140 0.0025 0.0280 0.0030 Ex. 130 H 0.062 0.11 1.65 0.007 0.0030 0.0200 0.0120 0.0034 0.0310 0.0025 Ex. 31 I 0.051 0.26 1.57 0.009 0.0020 0.0100 0.0130 0.0045 0.0290 0.0010 Ex. 32 J 0.070 0.04 1.57 0.010 0.0030 0.0120 0.0210 0.0038 0.0320 Ex. 33 K 0.065 0.20 1.51 0.010 0.0030 0.0210 0.0090 0.0042 0.0350 0.0020 Ex. 34 L 0.061 0.15 1.55 0.010 0.0030 0.0120 0.0150 0.0039 0.0380 0.0010 Ex. 35 M 0.055 0.23 1.42 0.010 0.0040 0.0200 0.0150 0.0040 0.0410 0.0005 Ex. 36 N 0.052 0.21 1.50 0.001 0.0030 0.0280 0.0200 0.0041 0.0540 0.0003 Chemical constituents (mass %) Cu Ni Cr Mo V Nb Mg Ceq Pcm Al/O Comp. Ex. 18 0.15 0.31 0.13 0.14 0.011 0.35 0.13 0.72 9.065 Comp. Ex. 19 0.40 0.10 0.01 0.011 0.002 0.42 0.26 0.63 13.760 Comp. Ex. 20 0.40 0.40 0.015 0.39 0.19 0.77 0.910 Comp. Ex. 21 0.50 0.10 0.012 0.41 0.18 0.31 52.430 Comp. Ex. 22 0.50 0.50 0.015 0.39 0.19 0.44 35.420 Comp. Ex. 23 0.40 0.02 0.012 0.40 0.19 0.36 6.390 Comp. Ex. 24 0.15 0.31 0.20 0.14 0.011 0.002 0.40 0.16 0.74 27.020 Comp. Ex. 25 0.50 0.14 0.011 0.36 0.15 0.71 23.180 Ex. 25 0.40 0.30 0.40 0.010 0.40 0.18 0.35 22.255 Ex. 26 0.30 0.30 0.012 0.002 0.36 0.14 0.43 14.445 Ex. 27 0.40 0.20 0.35 0.01 0.012 0.41 0.19 0.68 6.065 Ex. 28 0.45 0.45 0.40 0.30 0.01 0.012 0.38 0.19 0.71 4.245 Ex. 29 0.20 0.30 0.35 0.020 0.43 0.20 0.46 19.145 Ex. 130 0.35 0.30 0.25 0.03 0.012 0.44 0.20 0.65 19.360 Ex. 31 0.15 0.30 0.20 0.19 0.012 0.42 0.18 0.34 32.450 Ex. 32 0.20 0.19 0.015 0.003 0.41 0.17 0.38 23.900 Ex. 33 0.20 0.30 0.20 0.01 0.012 0.39 0.18 0.60 29.745 Ex. 34 0.15 0.30 0.15 0.012 0.38 0.17 0.32 39.240 Ex. 35 0.40 0.40 0.012 0.40 0.17 0.49 33.400 Ex. 36 0.35 0.28 0.30 0.01 0.012 0.41 0.17 0.52 37.560

[0133] After the submerged arc welding, the area ratios (%) of the weld metal structure (total of acicular ferrite, grain boundary ferrite, and martensite-austenite constituent), the EBSD grain size of the weld metal part, the tensile strength of the weld metal, the difference of hardness of the weld metal and the base metal, and the absorption energy of the Charpy impact test were measured. Tables 5 to 7 show the results. The AF ratio, GBF ratio, and MA ratio in Tables 5 to 7 respectively show the area ratios of the acicular ferrite, grain boundary ferrite, martensite-austenite constituent in the weld metal structure.

TABLE-US-00005 TABLE 5 AF GBF MA EBSD grain 10 C. absorption Charpy absorption ratio ratio ratio size TS(WM) H(Hv) energy (J) energy (J) Ex. 1 91.0 5.0 1.2 5.6 562 13 235 180 J (@30 C.) Ex. 2 90.0 6.0 1.1 5.5 604 27 231 165 J (@30 C.) Ex. 3 85.0 9.0 0.9 7.1 592 23 200 Ex. 4 80.0 10.0 0.8 7.9 575 17 180 Ex. 5 96.0 4.0 0.9 4.9 554 10 246 221 J (@45 C.) Ex. 6 94.5 5.0 1.0 5.3 559 12 225 190 J (@45 C.) Ex. 7 97.0 3.0 1.1 4.3 577 18 239 198 J (@45 C.) Ex. 8 84.0 5.0 0.8 5.9 559 12 178 Ex. 9 82.0 10.0 1.2 8.1 559 12 132 103 J (@20 C.) Ex. 10 81.0 9.5 1.1 7.9 556 10 139 101 J (@20 C.) Ex. 11 78.0 12.0 1.1 8.3 556 11 113 Ex. 12 75.0 12.5 1.2 8.5 559 12 109 Comp. Ex. 1 51.0 20.5 1.3 24.5 562 13 79 Comp. Ex. 2 60.0 18.9 1.4 31.2 554 10 80 Comp. Ex. 3 49.0 23.4 1.2 24.9 561 12 88 Comp. Ex. 4 65.0 22.0 1.1 29.8 559 12 54 Comp. Ex. 5 48.0 19.9 1.0 34.5 554 10 55

TABLE-US-00006 TABLE 6 (Continued from Table 5) AF GBF MA EBSD grain 10 C. absorption Charpy absorption ratio ratio ratio size TS(WM) H(Hv) energy (J) energy (J) Ex. 13 91.0 4.0 1.2 6.8 621 33 235 165 J (@30 C.) Ex. 14 90.0 5.0 1.6 7.5 610 29 229 165 J (@30 C.) Ex. 15 81.0 10.0 1.3 7.1 586 20 153 Ex. 16 83.0 8.0 1.5 8.1 606 28 160 Ex. 17 95.0 3.0 1.1 4.3 586 21 241 179 J (@45 C.) Ex. 18 81.0 9.0 1.2 6.1 572 16 173 Ex. 19 94.0 2.5 1.4 5.0 562 13 245 171 J (@45 C.) Ex. 20 92.0 7.8 1.3 6.3 646 41 237 171 J (@45 C.) Ex. 21 81.0 10.3 1.2 8.9 625 34 135 104 J (@20 C.) Ex. 22 76.0 12.5 1.3 8.5 555 10 107 101 J (@20 C.) Ex. 23 74.0 11.8 1.2 8.3 613 30 125 Ex. 24 83.0 9.7 2.5 7.9 621 33 139 103 J (@20 C.) Comp. Ex. 6 88.0 5.6 1.1 8.1 646 41 81 Comp. Ex. 7 85.0 6.3 2.3 7.9 629 35 90 Comp. Ex. 8 41.0 25.4 1.2 40.0 616 31 41 Comp. Ex. 9 61.0 20.3 1.3 30.0 606 28 43 Comp. Ex. 10 94.0 4.2 1.1 5.6 686 54 89 Comp. Ex. 11 87.0 6.3 3.1 6.0 554 10 93 Comp. Ex. 12 39.0 26.6 1.2 31.0 556 11 33 Comp. Ex. 13 60.0 23.2 1.3 25.0 606 28 40 Comp. Ex. 14 79.0 18.5 1.2 13.5 424 33 59 Comp. Ex. 15 73.0 13.8 3.3 8.1 621 32 82 Comp. Ex. 16 29.0 26.3 1.4 30.0 613 30 10 Comp. Ex. 17 41.0 22.1 1.3 45.0 567 15 15

TABLE-US-00007 TABLE 7 (Continued from Table 6) AF GBF MA EBSD grain 10 C. absorption Charpy absorption ratio ratio ratio size TS(WM) H(Hv) energy (J) energy (J) Comp. Ex. 18 81.0 11.0 1.5 7.8 497 9 80 Comp. Ex. 19 86.0 9.0 5.1 8.1 593 23 79 Comp. Ex. 20 68.0 18.0 1.2 18.5 589 22 61 Comp. Ex. 21 71.0 11.0 1.3 9.5 568 15 75 Comp. Ex. 22 67.0 19.0 1.1 19.1 588 22 43 Comp. Ex. 23 73.0 10.0 1.3 9.4 603 27 69 Comp. Ex. 24 71.0 9.0 1.2 9.7 560 12 80 Comp. Ex. 25 80.0 8.0 1.4 8.9 564 13 49 Ex. 25 90.0 5.1 1.3 6.1 619 40 210 Ex. 26 95.0 2.7 1.2 4.3 533 14 241 182 J (@30 C.) Ex. 27 88.0 7.1 1.5 7.0 612 12 208 Ex. 28 90.0 4.8 1.2 5.9 575 20 191 Ex. 29 97.0 1.3 1.1 4.4 607 30 245 192 J (@45 C.) Ex. 30 91.0 4.0 1.2 5.0 621 23 231 Ex. 31 84.0 6.9 1.4 6.9 599 33 155 Ex. 32 95.0 2.0 1.3 4.1 584 20 251 189 J (@45 C.) Ex. 33 83.0 7.1 1.5 5.5 589 29 134 105 J (@20 C.) Ex. 34 71.0 11.8 1.7 8.9 571 22 107 Ex. 35 81.0 9.5 1.5 7.0 588 11 115 109 J (@20 C.) Ex. 36 72.0 14.0 1.5 8.8 608 11 103

[0134] The absorption energy of the Charpy impact test was measured as follows.

[0135] At a cross-section of plate thickness parallel to a direction including the HAZ and the weld metal, a Charpy test piece was taken from the center of the weld metal part 2 mm below the surface layer of the steel plate. In accordance with JIS Z2242, a Charpy impact test was performed at 10 C. to measure the absorption energy. The absorption energy was found by performing the Charpy impact test three times and obtaining the average value. A sample with a value of less than 100 J was judged as poor in toughness. Some samples were also measured for Charpy absorption energy at a temperature of other than 10 C.

[0136] The area ratios of the structures were measured as follows:

[0137] A part of the weld bead width at the t/4 position of thickness from the surface layer at the second pass was taken as a test piece. This was polished, then corroded by Nital corrosion and LePera corrosion. The revealed structure was observed by an optical microscope in a 1000 m1000 m range. 10 fields of the structure were measured. The obtained images were analyzed and the average area ratios of the structures were calculated.

[0138] The EBSD grain size was obtained by EBSD analysis of 20 fields in a range of 500 m500 m and averaging the crystal grain sizes when divided into sections of a crystal orientation difference of 15.

[0139] As shown in Tables 5 to 7, the invention examples satisfying the composition of constituents of a welded joint of the present invention all had a Charpy absorption energy at 10 C. of 100 J or more and an excellent toughness of the weld metal part.

[0140] As opposed to this, comparative examples not satisfying the composition of constituents of a welded joint of the present invention had a Charpy absorption energy at 10 C. of less than 100 J and a low toughness of the weld metal part and welded joint.

[0141] Further, in the invention examples, a high Charpy absorption energy was obtained in accordance with the amounts of O in the weld metal even at 20 C., 30 C., and 45 C.

[0142] FIG. 2 gives examples of structures of the weld metal. (a) and (b) show the structures of invention examples, while (c) and (d) show the structures of comparative examples. In the invention examples, it is learned that the structures of the weld metal are made finer.

INDUSTRIAL APPLICABILITY

[0143] According to the present invention, it is possible to provide longitudinal seam welded steel pipe excellent in toughness of the weld metal part even if joining thick steel plate by large heat input welding. Accordingly, the present invention is high in industrial applicability.