WO2020202334A1 - Electric resistance welded steel pipe and method for manufacturing same, and steel pipe pile - Google Patents
Electric resistance welded steel pipe and method for manufacturing same, and steel pipe pile Download PDFInfo
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B17/00—Tube-rolling by rollers of which the axes are arranged essentially perpendicular to the axis of the work, e.g. "axial" tube-rolling
- B21B17/14—Tube-rolling by rollers of which the axes are arranged essentially perpendicular to the axis of the work, e.g. "axial" tube-rolling without mandrel, e.g. stretch-reducing mills
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
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- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/08—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes
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- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/002—Bainite
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
Abstract
Description
[1] 母材部と鋼軸方向に溶接部を有する電縫鋼管であって、
前記母材部の成分組成は、質量%で、
C:0.12~0.20%、
Si:0.60%以下、
Mn:0.50~1.70%、
P:0.030%以下、
S:0.015%以下、
Al:0.010~0.060%、
Nb:0.010~0.080%、
Ti:0.010~0.050%、
N:0.006%以下
を含有し、残部がFeおよび不可避的不純物からなり、
前記母材部の板厚をtとしたとき、前記電縫鋼管の外表面から板厚tの1/4t深さ位置における鋼組織は、
ベイナイトが面積率で60%以上であり、
前記ベイナイトの平均有効粒径が平均円相当径で20.0μm以下、かつ前記ベイナイトの平均アスペクト比が0.1~0.8であり、
管軸方向の引張強さが590MPa以上、0.2%耐力が450MPa以上、降伏比が80~90%であり、
前記母材部における管軸方向を試験片長手方向とした-30℃におけるシャルピー吸収エネルギーが70J以上であり、
前記母材部における鋼管外表面の管軸方向における残留応力が250MPa以下である電縫鋼管。
[2] 前記成分組成に加えてさらに、質量%で、B:0.008%以下を含有する[1]に記載の電縫鋼管。
[3] 前記成分組成に加えてさらに、質量%で、
Cr:0.01~1.0%、
V:0.010~0.060%、
Mo:0.01~1.0%、
Cu:0.01~0.50%、
Ni:0.01~1.0%、
Ca:0.0005~0.010%
のうちから選ばれた1種または2種以上を含有する[1]または[2]に記載の電縫鋼管。
[4] 鋼素材に、熱間圧延工程、冷却工程をこの順に施して熱延鋼板とし、さらに、該熱延鋼板に冷間ロール成形工程を施して電縫鋼管とする電縫鋼管の製造方法であって、
前記鋼素材は、[1]~[3]のいずれか1つに記載の成分組成を有し、
前記熱間圧延工程は、前記鋼素材を加熱温度:1100~1280℃に加熱した後、粗圧延終了温度:850~1150℃、仕上圧延終了温度:750~850℃、かつ、粗圧延と仕上圧延における930℃以下での合計圧下率:65%以上とする粗圧延および仕上圧延を施して熱延板とする工程であり、
前記冷却工程は、前記熱延板を、板厚中心温度で冷却開始から冷却停止までの平均冷却速度:5~25℃/s、冷却停止温度:450~650℃で冷却する工程であり、
前記冷間ロール成形工程は、前記熱延鋼板にロール成形加工を施した鋼管素材を溶接し、溶接後の鋼管外面の周長に対して縮径率:0.2~0.5%の縮径圧延を行う電縫鋼管の製造方法。
[5] [1]~[3]のいずれか1つに記載の成分組成を有し、板厚をtとしたとき、外表面から板厚tの1/4t深さ位置における鋼組織は、ベイナイトが面積率で60%以上であり、前記ベイナイトの平均有効粒径が平均円相当径で20.0μm以下、かつ前記ベイナイトの平均アスペクト比が0.1~0.8である熱延鋼板に冷間ロール成形工程を施して電縫鋼管とする電縫鋼管の製造方法であって、
前記冷間ロール成形工程は、前記熱延鋼板にロール成形加工を施した鋼管素材を溶接し、溶接後の鋼管外面の周長に対して縮径率:0.2~0.5%の縮径圧延を行う電縫鋼管の製造方法。
[6] [1]~[3]のいずれか1つに記載の電縫鋼管を用いた鋼管杭。 The present invention has been completed by further studying based on such findings, and the gist of the present invention is as follows.
[1] An electric resistance pipe having a base metal portion and a welded portion in the steel axis direction.
The component composition of the base material portion is mass%.
C: 0.12 to 0.20%,
Si: 0.60% or less,
Mn: 0.50 to 1.70%,
P: 0.030% or less,
S: 0.015% or less,
Al: 0.010 to 0.060%,
Nb: 0.010 to 0.080%,
Ti: 0.010 to 0.050%,
N: Contains 0.006% or less, the balance consists of Fe and unavoidable impurities,
When the plate thickness of the base metal portion is t, the steel structure at a depth of 1/4 t of the plate thickness t from the outer surface of the electrosewn steel pipe is
Bainite has an area ratio of 60% or more,
The average effective particle size of the bainite is 20.0 μm or less in the diameter equivalent to the average circle, and the average aspect ratio of the bainite is 0.1 to 0.8.
The tensile strength in the tube axis direction is 590 MPa or more, the 0.2% proof stress is 450 MPa or more, and the yield ratio is 80 to 90%.
The Charpy absorption energy at −30 ° C. with the tube axis direction in the base metal portion as the longitudinal direction of the test piece is 70 J or more.
An electrosewn steel pipe having a residual stress of 250 MPa or less in the pipe axial direction on the outer surface of the steel pipe in the base material portion.
[2] The electric resistance welded steel pipe according to [1], which further contains B: 0.008% or less in mass% in addition to the component composition.
[3] In addition to the above component composition, in mass%,
Cr: 0.01-1.0%,
V: 0.010 to 0.060%,
Mo: 0.01-1.0%,
Cu: 0.01-0.50%,
Ni: 0.01-1.0%,
Ca: 0.0005-0.010%
The electric resistance pipe according to [1] or [2], which contains one or more selected from the above.
[4] A method for manufacturing an electric resistance-sewn steel pipe in which a hot-rolling process and a cooling process are applied to a steel material in this order to obtain a hot-rolled steel sheet, and the hot-rolled steel sheet is further subjected to a cold roll forming process to obtain an electric-sewn steel pipe. And
The steel material has the component composition according to any one of [1] to [3].
In the hot rolling step, after heating the steel material to a heating temperature of 1100 to 1280 ° C., rough rolling end temperature: 850 to 1150 ° C., finish rolling end temperature: 750 to 850 ° C., and rough rolling and finish rolling. Total rolling reduction at 930 ° C. or lower: 65% or more in rough rolling and finish rolling to obtain a hot-rolled plate.
The cooling step is a step of cooling the hot-rolled plate at a plate thickness center temperature at an average cooling rate of 5 to 25 ° C./s from the start of cooling to the stop of cooling and a cooling stop temperature of 450 to 650 ° C.
In the cold roll forming step, a steel pipe material that has been roll-formed is welded to the hot-rolled steel sheet, and the diameter reduction ratio is 0.2 to 0.5% with respect to the peripheral length of the outer surface of the steel pipe after welding. A method for manufacturing an electrosewn steel pipe for diameter rolling.
[5] When the composition has the component composition according to any one of [1] to [3] and the plate thickness is t, the steel structure at a depth of 1/4 t from the outer surface to the plate thickness t is For hot-rolled steel sheets in which bainite has an area ratio of 60% or more, the average effective particle size of the bainite is 20.0 μm or less in the equivalent circle diameter, and the average aspect ratio of the bainite is 0.1 to 0.8. This is a method for manufacturing a bainite steel pipe that is subjected to a cold roll forming process to form a bainite steel pipe.
In the cold roll forming step, a steel pipe material that has been roll-formed is welded to the hot-rolled steel sheet, and the diameter reduction ratio is 0.2 to 0.5% with respect to the peripheral length of the outer surface of the steel pipe after welding. A method for manufacturing an electrosewn steel pipe for diameter rolling.
[6] A steel pipe pile using the electrosewn steel pipe according to any one of [1] to [3].
Cは、固溶強化により鋼管(電縫鋼管)の強度を増加させるとともに、ベイナイトなどの鋼組織の生成に関与する元素である。また、Cは、降伏比の適正化に有効な元素である。比較的板厚の大きい鋼管(例えば、板厚が16mm以上の鋼管)は、外径と内径の差が大きいため、鋼管を製造する際の加工度が大きく、降伏比が上昇しやすい。このため、Cを多く含有する必要がある。したがって、上記した効果を得るためには、0.12%以上のCの含有を必要とする。一方、0.20%を超えるCの含有は、マルテンサイトが生成しやすくなり、本発明で目的とする鋼組織が得られない。その結果、本発明で目的とする高靱性を確保することができなくなる。よって、Cは0.12~0.20%とする。Cは、好ましくは0.13%以上とし、より好ましくは0.14%以上とする。Cは、好ましくは0.19%以下とし、より好ましくは0.18%以下とする。 C: 0.12 to 0.20%
C is an element that increases the strength of steel pipes (electrically sewn steel pipes) by solid solution strengthening and is involved in the formation of steel structures such as bainite. Further, C is an element effective for optimizing the yield ratio. A steel pipe having a relatively large plate thickness (for example, a steel pipe having a plate thickness of 16 mm or more) has a large difference between the outer diameter and the inner diameter, so that the degree of processing when manufacturing the steel pipe is large and the yield ratio tends to increase. Therefore, it is necessary to contain a large amount of C. Therefore, in order to obtain the above-mentioned effect, the content of C of 0.12% or more is required. On the other hand, if the content of C exceeds 0.20%, martensite is likely to be formed, and the steel structure desired in the present invention cannot be obtained. As a result, the high toughness intended by the present invention cannot be ensured. Therefore, C is set to 0.12 to 0.20%. C is preferably 0.13% or more, and more preferably 0.14% or more. C is preferably 0.19% or less, and more preferably 0.18% or less.
Siは、脱酸剤として作用するとともに、鋼管の強度を増加させることができる元素である。しかし、Siを過剰に含有すると靱性が低下する。このようなことから、Siは0.60%以下とする。Siは、好ましくは0.50%以下とし、より好ましくは0.45%以下とする。なお、Siの下限は特に規定しないが、電縫溶接性の観点より、0.01%以上とすることが好ましい。より好ましくは0.02%以上とする。 Si: 0.60% or less Si is an element that can act as an antacid and increase the strength of steel pipes. However, if Si is contained in excess, the toughness decreases. For this reason, Si is set to 0.60% or less. Si is preferably 0.50% or less, and more preferably 0.45% or less. Although the lower limit of Si is not particularly specified, it is preferably 0.01% or more from the viewpoint of electric sewing weldability. More preferably, it is 0.02% or more.
Mnは、固溶強化を介して鋼管の強度を増加させる元素である。このような効果を得て、本発明で目的とする高強度を確保するためには、0.50%以上のMnの含有を必要とする。一方、1.70%を超えてMnを含有すると、鋼組織が微細化し、降伏強度が高くなり、本発明で目的とする降伏比を確保できなくなる。このため、Mnは0.50~1.70%とする。Mnは、好ましくは0.55%以上とし、より好ましくは0.60%以上とする。Mnは、好ましくは1.65%以下とし、より好ましくは1.60%以下とする。 Mn: 0.50 to 1.70%
Mn is an element that increases the strength of steel pipes through solid solution strengthening. In order to obtain such an effect and secure the high strength desired in the present invention, the content of Mn of 0.50% or more is required. On the other hand, if Mn is contained in excess of 1.70%, the steel structure becomes finer and the yield strength becomes high, so that the yield ratio desired in the present invention cannot be secured. Therefore, Mn is set to 0.50 to 1.70%. Mn is preferably 0.55% or more, and more preferably 0.60% or more. Mn is preferably 1.65% or less, and more preferably 1.60% or less.
Pは、結晶粒界に偏析して靭性を低下させる元素であり、不純物としてできるだけ低減することが望ましいが、本発明では、0.030%までは許容できる。このようなことから、Pは0.030%以下とする。Pは、好ましくは0.025%以下とし、より好ましくは0.020%以下とする。しかし、Pの過度の低減は、精錬コストの高騰を招くため、Pは0.002%以上とすることが好ましい。より好ましくは0.003%以上とする。 P: 0.030% or less P is an element that segregates at grain boundaries and lowers toughness, and it is desirable to reduce it as an impurity as much as possible, but in the present invention, up to 0.030% is acceptable. For this reason, P is set to 0.030% or less. P is preferably 0.025% or less, and more preferably 0.020% or less. However, since excessive reduction of P causes an increase in refining cost, P is preferably 0.002% or more. More preferably, it is 0.003% or more.
Sは、鋼管の素材である熱延鋼板を製造する際、鋼中でMnSとして存在し、熱間圧延工程で薄く延伸されることにより、鋼管の延性および靭性に悪影響を及ぼす。このため、本発明ではSを不純物としてできるだけ低減することが望ましいが、Sの含有は0.015%までは許容できる。このため、Sは0.015%以下とする。Sは、好ましくは0.010%以下とし、より好ましくは0.008%以下とする。しかし、Sの過度の低減は、精錬コストの高騰を招くため、Sは0.0002%以上とすることが好ましい。より好ましくは0.001%以上とする。 S: 0.015% or less S exists as MnS in steel when manufacturing a hot-rolled steel sheet, which is a material for steel pipes, and is thinly stretched in a hot rolling process, which adversely affects the ductility and toughness of steel pipes. To exert. Therefore, in the present invention, it is desirable to reduce S as an impurity as much as possible, but the content of S can be up to 0.015%. Therefore, S is set to 0.015% or less. S is preferably 0.010% or less, and more preferably 0.008% or less. However, since excessive reduction of S causes an increase in refining cost, it is preferable that S is 0.0002% or more. More preferably, it is 0.001% or more.
Alは、脱酸剤として作用するとともに、Nと結合してAlNを形成し、結晶粒の微細化に寄与する。このような効果を得るためには、0.010%以上のAlを含有する必要がある。一方、0.060%を超える多量のAlの含有は、鋼材(鋼管の素材である熱延鋼板)の清浄度を低下させ、鋼管の延性および靭性を低下させる。このため、Alは0.010~0.060%とする。Alは、好ましくは0.015%以上とし、より好ましくは0.020%以上とする。Alは、好ましくは0.055%以下とし、より好ましくは0.050%以下とする。 Al: 0.010 to 0.060%
Al acts as an antacid and combines with N to form AlN, which contributes to the refinement of crystal grains. In order to obtain such an effect, it is necessary to contain 0.010% or more of Al. On the other hand, the content of a large amount of Al exceeding 0.060% lowers the cleanliness of the steel material (hot-rolled steel sheet which is the material of the steel pipe), and lowers the ductility and toughness of the steel pipe. Therefore, Al is set to 0.010 to 0.060%. Al is preferably 0.015% or more, and more preferably 0.020% or more. Al is preferably 0.055% or less, and more preferably 0.050% or less.
Nbは、炭素や窒素と結合して微細な析出物を形成し、析出強化によって鋼管の強度を増加させる。このような効果を得るためには、Nbを0.010%以上含有する必要がある。一方、0.080%を超えてNbを含有すると、鋼管の素材である熱延鋼板を製造する際、熱間圧延工程における加熱で固溶させることが難しくなる。その結果、粗大な析出物として残留し、靱性が低下する。このため、Nbは0.010~0.080%とする。Nbは、好ましくは0.015%以上とし、より好ましくは0.020%以上とする。Nbは、好ましくは0.075%以下とし、より好ましくは0.070%以下とする。 Nb: 0.010 to 0.080%
Nb combines with carbon and nitrogen to form fine precipitates, and the strength of the steel pipe is increased by strengthening the precipitation. In order to obtain such an effect, it is necessary to contain 0.010% or more of Nb. On the other hand, if Nb is contained in an amount of more than 0.080%, it becomes difficult to dissolve the hot-rolled steel sheet, which is a material of the steel pipe, by heating in the hot rolling step. As a result, it remains as a coarse precipitate and the toughness is lowered. Therefore, Nb is set to 0.010 to 0.080%. Nb is preferably 0.015% or more, and more preferably 0.020% or more. Nb is preferably 0.075% or less, and more preferably 0.070% or less.
Tiは、炭素や窒素と結合して微細な析出物を形成し、析出強化によって鋼管の強度を増加させる。このような効果を得るためには、Tiを0.010%以上含有する必要がある。一方、0.050%を超えてTiを含有すると、析出物が粗大化し、靱性が低下する。このため、Tiは0.010~0.050%とする。Tiは、好ましくは0.012%以上とし、より好ましくは0.015%以上とする。Tiは、好ましくは0.045%以下とし、より好ましくは0.040%以下とする。 Ti: 0.010 to 0.050%
Ti combines with carbon and nitrogen to form fine precipitates, which increase the strength of the steel pipe by strengthening the precipitates. In order to obtain such an effect, it is necessary to contain 0.010% or more of Ti. On the other hand, if Ti is contained in excess of 0.050%, the precipitate becomes coarse and the toughness decreases. Therefore, Ti is set to 0.010 to 0.050%. Ti is preferably 0.012% or more, more preferably 0.015% or more. Ti is preferably 0.045% or less, and more preferably 0.040% or less.
Nは、微量であれば鋼管の強度を増加させる効果を有するが、多量に含有すると高温で粗大な析出物を形成し、靱性を低下させる。このため、Nは0.006%以下とする。Nの過度な低減は、精錬コストの高騰を招くため、好ましくは0.001%以上とし、より好ましくは0.002%以上とする。Nは、好ましくは0.005%以下とし、より好ましくは0.004%以下とする。 N: 0.006% or less N has the effect of increasing the strength of the steel pipe if it is in a small amount, but if it is contained in a large amount, coarse precipitates are formed at high temperature and the toughness is lowered. Therefore, N is set to 0.006% or less. Excessive reduction of N causes an increase in refining cost, so it is preferably 0.001% or more, more preferably 0.002% or more. N is preferably 0.005% or less, and more preferably 0.004% or less.
Bは、フェライト変態開始温度を低下させることで鋼組織の微細化に寄与する元素であり、必要に応じて含有することができる。しかし、Bの含有量が0.008%を超えると、結晶粒界に偏析しやすくなり、靱性が低下する恐れがある。したがって、Bを含有する場合には、Bを0.008%以下とすることが好ましい。より好ましくは0.006%以下とする。なお、Bは、好ましくは0.0003%以上とする。 B: 0.008% or less B is an element that contributes to the miniaturization of the steel structure by lowering the ferrite transformation start temperature, and can be contained as necessary. However, if the B content exceeds 0.008%, segregation is likely to occur at the grain boundaries, and the toughness may decrease. Therefore, when B is contained, it is preferable that B is 0.008% or less. More preferably, it is 0.006% or less. B is preferably 0.0003% or more.
Cr:0.01~1.0%
Crは、焼入れ性を高めることで、鋼管の強度を上昇させる元素であり、必要に応じて含有することができる。このような効果を得るためには、Crを0.01%以上含有することが好ましい。一方、1.0%を超えてCrを含有すると、靱性や溶接性を低下させる恐れがあるため、1.0%以下とすることが好ましい。したがって、Crを含有する場合には、Crを0.01~1.0%とすることが好ましい。Crは、より好ましくは0.02%以上とし、より一層好ましくは0.03%以上とする。Crは、より好ましくは0.8%以下とし、より一層好ましくは0.6%以下とする。 Cr: 0.01 to 1.0%, V: 0.010 to 0.060%, Mo: 0.01 to 1.0%, Cu: 0.01 to 0.50%, Ni: 0.01 to One or more selected from 1.0%, Ca: 0.0005 to 0.010% Cr: 0.01 to 1.0%
Cr is an element that increases the strength of steel pipes by enhancing hardenability, and can be contained as needed. In order to obtain such an effect, it is preferable to contain Cr in an amount of 0.01% or more. On the other hand, if Cr is contained in excess of 1.0%, the toughness and weldability may be lowered, so the content is preferably 1.0% or less. Therefore, when Cr is contained, it is preferable that Cr is 0.01 to 1.0%. Cr is more preferably 0.02% or more, and even more preferably 0.03% or more. Cr is more preferably 0.8% or less, and even more preferably 0.6% or less.
Vは、炭素や窒素と結合して微細な析出物を形成し、析出強化によって鋼管の強度を増加させる元素であり、必要に応じて含有することができる。このような効果を得るためには、Vを0.010%以上含有する必要がある。一方、0.060%を超えてVを含有すると、析出物が粗大化し、上記した効果が飽和しやすくなす。このため、Vは0.010~0.060%とする。Vは、好ましくは0.012%以上とし、より好ましくは0.015%以上とする。Vは、好ましくは0.055%以下とし、より好ましくは0.050%以下とする。 V: 0.010 to 0.060%
V is an element that combines with carbon and nitrogen to form fine precipitates and increases the strength of the steel pipe by strengthening the precipitation, and can be contained as needed. In order to obtain such an effect, it is necessary to contain 0.010% or more of V. On the other hand, if V is contained in excess of 0.060%, the precipitate becomes coarse and the above-mentioned effect tends to be saturated. Therefore, V is set to 0.010 to 0.060%. V is preferably 0.012% or more, and more preferably 0.015% or more. V is preferably 0.055% or less, and more preferably 0.050% or less.
Moは、焼入れ性を高めることで、鋼管の強度を上昇させる元素であり、必要に応じて含有することができる。このような効果を得るためには、Moを0.01%以上含有することが好ましい。一方、1.0%を超えてMoを含有すると、靱性を低下させるおそれがあるため、1.0%以下とすることが好ましい。したがって、Moを含有する場合には、Moを0.01~1.0%とすることが好ましい。Moは、より好ましくは0.02%以上とし、より一層好ましくは0.03%以上とする。Moは、より好ましくは0.8%以下とし、より一層好ましくは0.6%以下とする。 Mo: 0.01-1.0%
Mo is an element that increases the strength of steel pipes by enhancing hardenability, and can be contained as needed. In order to obtain such an effect, it is preferable to contain Mo in 0.01% or more. On the other hand, if Mo is contained in excess of 1.0%, the toughness may be lowered, so the content is preferably 1.0% or less. Therefore, when Mo is contained, it is preferable that Mo is 0.01 to 1.0%. Mo is more preferably 0.02% or more, and even more preferably 0.03% or more. Mo is more preferably 0.8% or less, and even more preferably 0.6% or less.
Cuは、固溶強化により鋼管の強度を上昇させる元素であり、必要に応じて含有することができる。このような効果を得るためには、Cuを0.01%以上含有することが好ましい。一方、0.50%を超えてCuを含有すると、靱性を低下させるおそれがあるため、0.50%以下とすることが好ましい。したがって、Cuを含有する場合には、Cuを0.01~0.50%とすることが好ましい。Cuは、より好ましくは0.02%以上とし、より一層好ましくは0.03%以上とする。Cuは、より好ましくは0.45%以下とし、より一層好ましくは0.40%以下とする。 Cu: 0.01-0.50%
Cu is an element that increases the strength of steel pipes by solid solution strengthening, and can be contained as needed. In order to obtain such an effect, it is preferable to contain 0.01% or more of Cu. On the other hand, if Cu is contained in excess of 0.50%, the toughness may be lowered, so the content is preferably 0.50% or less. Therefore, when Cu is contained, it is preferable that Cu is 0.01 to 0.50%. Cu is more preferably 0.02% or more, and even more preferably 0.03% or more. Cu is more preferably 0.45% or less, and even more preferably 0.40% or less.
Niは、固溶強化により鋼管の強度を上昇させる元素であり、必要に応じて含有することができる。このような効果を得るためには、Niを0.01%以上含有することが好ましい。一方、1.0%を超えてNiを含有すると、靱性を低下させるおそれがあるため、1.0%以下とすることが好ましい。したがって、Niを含有する場合には、Niを0.01~1.0%とすることが好ましい。Niは、より好ましくは0.02%以上とし、より一層好ましくは0.03%以上とする。Niは、より好ましくは0.8%以下とし、より一層好ましくは0.6%以下とする。 Ni: 0.01-1.0%
Ni is an element that increases the strength of steel pipes by solid solution strengthening, and can be contained as needed. In order to obtain such an effect, it is preferable to contain 0.01% or more of Ni. On the other hand, if Ni is contained in excess of 1.0%, the toughness may be lowered, so the content is preferably 1.0% or less. Therefore, when Ni is contained, it is preferable that Ni is 0.01 to 1.0%. Ni is more preferably 0.02% or more, and even more preferably 0.03% or more. Ni is more preferably 0.8% or less, and even more preferably 0.6% or less.
Caは、鋼管の素材である熱延鋼板を製造する際、熱間圧延工程で薄く延伸されるMnS等の硫化物を、球状化することで鋼の靱性向上に寄与する元素であり、必要に応じて含有することができる。このような効果を得るため、Caを含有する場合には、0.0005%以上含有することが好ましい。しかし、Caの含有量が0.010%を超えると、鋼中にCa酸化物クラスターが形成され、靱性が悪化する恐れがある。したがって、Caを含有する場合には、Caを0.0005%~0.010%とすることが好ましい。Caは、より好ましくは0.0010%以上とし、より一層好ましくは0.0015%以上とする。Caは、より好ましくは0.005%以下とし、より一層好ましくは0.004%以下とする。 Ca: 0.0005-0.010%
Ca is an element that contributes to improving the toughness of steel by spheroidizing sulfides such as MnS that are thinly stretched in the hot rolling process when manufacturing hot-rolled steel sheets that are the material of steel pipes. It can be contained accordingly. In order to obtain such an effect, when Ca is contained, it is preferably contained in an amount of 0.0005% or more. However, if the Ca content exceeds 0.010%, Ca oxide clusters may be formed in the steel and the toughness may deteriorate. Therefore, when Ca is contained, it is preferable that Ca is 0.0005% to 0.010%. Ca is more preferably 0.0010% or more, and even more preferably 0.0015% or more. Ca is more preferably 0.005% or less, and even more preferably 0.004% or less.
本発明において高強度と高靱性を両立するために、ベイナイトを面積率で60%以上含有することが重要である。ベイナイトが60%未満であると、本発明で目的とする強度が得にくくなる。したがって、鋼管の外表面から板厚tの1/4t深さ位置における鋼組織は、ベイナイトを面積率で60%以上とする。好ましくは65%以上である。なお、ベイナイトの面積率が過剰であると降伏比が高くなり過ぎるために、ベイナイトは面積率で98%以下とすることが好ましい。より好ましくは95%以下とする。 Area ratio of bainite: 60% or more In order to achieve both high strength and high toughness in the present invention, it is important to contain bainite in an area ratio of 60% or more. If bainite is less than 60%, it becomes difficult to obtain the strength desired in the present invention. Therefore, in the steel structure at a depth of 1/4 t of the plate thickness t from the outer surface of the steel pipe, bainite is set to 60% or more in area ratio. It is preferably 65% or more. If the area ratio of bainite is excessive, the yield ratio becomes too high. Therefore, the area ratio of bainite is preferably 98% or less. More preferably, it is 95% or less.
本発明において高強度と高靱性を両立するために、ベイナイトの平均有効粒径の平均円相当径を20.0μm以下とすることが重要である。ベイナイトの平均有効粒径が、平均円相当径で20.0μmを超えると、本発明で目的とする靱性が得られなくなる。また、本発明で目的とする強度が得られなくなる。好ましくは15.0μm以下とする。なお、ベイナイトが微細になり過ぎると降伏比が高くなり過ぎるために、ベイナイトの平均有効粒径の平均円相当径を1.0μm以上とすることが好ましく、2.0μm以上とすることがより好ましい。 Average effective particle size of bainite: 20.0 μm or less in average effective particle diameter In order to achieve both high strength and high toughness in the present invention, the average effective particle size of bainite may be 20.0 μm or less. is important. If the average effective particle size of bainite exceeds 20.0 μm in the diameter equivalent to an average circle, the toughness intended by the present invention cannot be obtained. In addition, the strength desired in the present invention cannot be obtained. It is preferably 15.0 μm or less. If the bainite becomes too fine, the yield ratio becomes too high. Therefore, the average effective particle size of bainite is preferably 1.0 μm or more, and more preferably 2.0 μm or more. ..
本発明において管軸方向の降伏比を80~90%に制御するためには、ベイナイトの平均アスペクト比を0.1~0.8とすることが必要となる。ここでは、上述のベイナイトの結晶粒において、(板厚方向の長さの平均)/(管軸方向の長さの平均)を算出し、ベイナイトの平均アスペクト比とした。ベイナイトの平均アスペクト比が0.8を超えると、管軸方向の塑性変形能が低下し、降伏比が90%を超えやすくなる。一方、ベイナイトの平均アスペクト比が0.1未満では、管軸方向の強度が低下し、本発明で目的とする強度が得られなくなる。 Bainite average aspect ratio: 0.1-0.8
In the present invention, in order to control the yield ratio in the tube axis direction to 80 to 90%, it is necessary to set the average aspect ratio of bainite to 0.1 to 0.8. Here, in the above-mentioned bainite crystal grains, (average length in the plate thickness direction) / (average length in the tube axis direction) was calculated and used as the average aspect ratio of bainite. When the average aspect ratio of bainite exceeds 0.8, the plastic deformability in the tube axis direction decreases, and the yield ratio tends to exceed 90%. On the other hand, if the average aspect ratio of bainite is less than 0.1, the strength in the tube axis direction decreases, and the strength desired in the present invention cannot be obtained.
加熱温度が1100℃未満の場合は、鋳造時に生成した鋼素材中に存在する粗大な炭化物を固溶することができない。その結果、含有する炭化物形成元素の効果を十分に得ることができない。一方、加熱温度が1280℃を超えて高温となると、結晶粒が著しく粗大化し、鋼管の素材である熱延鋼板の組織が粗大化し、本発明で目的とする特性を確保することが困難となる。このため、鋼素材の加熱温度は1100~1280℃とする必要がある。好ましくは1120~1230℃とする。なお、この温度は、加熱炉の炉内設定温度とする。 Heating temperature: 1100-1280 ° C
If the heating temperature is less than 1100 ° C., the coarse carbides present in the steel material produced during casting cannot be solid-solved. As a result, the effect of the contained carbide-forming element cannot be sufficiently obtained. On the other hand, when the heating temperature exceeds 1280 ° C. and becomes high, the crystal grains become remarkably coarse, and the structure of the hot-rolled steel sheet, which is the material of the steel pipe, becomes coarse, and it becomes difficult to secure the characteristics intended by the present invention. .. Therefore, the heating temperature of the steel material needs to be 1100 to 1280 ° C. The temperature is preferably 1120 to 1230 ° C. This temperature is the set temperature inside the heating furnace.
粗圧延終了温度が850℃未満の場合、熱間圧延中の組織の回復が起こらず圧延方向に過度に伸長した結晶粒が生成しやすくなる。その結果、ベイナイトの平均アスペクト比が0.1未満となりやすい。一方、粗圧延終了温度が1150℃を超えると、オーステナイト未再結晶温度域での圧下量が不足し、微細なオーステナイト粒が得られず、その結果、本発明で目的とするベイナイトの平均有効粒径を確保することが困難となる。このため、粗圧延終了温度は850~1150℃とする。好ましくは860~1000℃とする。 Rough rolling end temperature: 850 to 1150 ° C
When the rough rolling end temperature is less than 850 ° C., the structure during hot rolling does not recover and crystal grains that are excessively elongated in the rolling direction are likely to be generated. As a result, the average aspect ratio of bainite tends to be less than 0.1. On the other hand, when the rough rolling end temperature exceeds 1150 ° C., the amount of reduction in the austenite unrecrystallized temperature range is insufficient, and fine austenite grains cannot be obtained. As a result, the average effective grain of bainite, which is the object of the present invention, is obtained. It becomes difficult to secure the diameter. Therefore, the rough rolling end temperature is set to 850 to 1150 ° C. The temperature is preferably 860 to 1000 ° C.
仕上圧延終了温度が750℃未満の場合、熱間圧延中の組織の回復が起こらず圧延方向に過度に伸長した結晶粒が生成しやすくなる。その結果、ベイナイトの平均アスペクト比が0.1未満となりやすい。一方、仕上圧延終了温度が850℃を超えると、オーステナイト未再結晶温度域での圧下量が不足し、微細なオーステナイト粒が得られず、その結果、本発明で目的とするベイナイトの平均有効粒径を確保することが困難となる。このため、仕上圧延終了温度は750~850℃とする。好ましくは770~830℃とする。 Finish rolling end temperature: 750 to 850 ° C
When the finish rolling end temperature is less than 750 ° C., the structure during hot rolling does not recover and crystal grains that are excessively elongated in the rolling direction are likely to be generated. As a result, the average aspect ratio of bainite tends to be less than 0.1. On the other hand, when the finish rolling end temperature exceeds 850 ° C., the amount of rolling in the austenite unrecrystallized temperature range is insufficient, and fine austenite grains cannot be obtained. As a result, the average effective grain of bainite, which is the object of the present invention, is obtained. It becomes difficult to secure the diameter. Therefore, the finish rolling end temperature is set to 750 to 850 ° C. The temperature is preferably 770 to 830 ° C.
本発明では、熱間圧延工程においてオーステナイトを微細化することで、続く冷却工程、巻取工程で生成するベイナイトおよび残部組織を微細化し、本発明で目的とする強度および靱性を有する電縫鋼管の素材として適した熱延鋼板を得られる。熱間圧延工程においてオーステナイトを微細化するためには、オーステナイト未再結晶温度域での圧下率を高くし、十分な加工ひずみを導入する必要がある。この効果を得るため、本発明では、930℃以下仕上圧延終了温度までの温度域における合計圧下率を65%以上とする。ここで、合計圧下率とは、930℃以下仕上圧延終了温度までの温度域における各圧延パスの圧下率の合計をさす。 Total rolling reduction at 930 ° C or lower in rough rolling and finish rolling: 65% or more In the present invention, by refining austenite in the hot rolling process, bainite and the residual structure generated in the subsequent cooling process and winding process are produced. It is possible to obtain a hot-rolled steel sheet that is miniaturized and has the strength and toughness desired in the present invention and is suitable as a material for bainite pipes. In order to miniaturize austenite in the hot rolling process, it is necessary to increase the rolling reduction in the austenite unrecrystallized temperature range and introduce sufficient processing strain. In order to obtain this effect, in the present invention, the total reduction rate in the temperature range up to the finish rolling end temperature of 930 ° C. or lower is set to 65% or more. Here, the total rolling reduction rate refers to the total rolling reduction rate of each rolling path in the temperature range up to the finish rolling end temperature of 930 ° C. or lower.
熱延板の板厚中心温度で、冷却開始から後述する冷却停止温度までの温度域における平均冷却速度が5℃/s未満では、フェライトの生成により、ベイナイトの面積率が低下し、本発明で目的とする強度を得られない。一方で、平均冷却速度が25℃/sを超えると、ベイナイトの平均アスペクト比が0.8を超える。その結果、降伏比が90%を超えやすくなる。平均冷却速度は、好ましくは10℃/s以上とし、好ましくは20℃/s以下とする。 Average cooling rate from the start of cooling to the stop of cooling: 5 to 25 ° C / s
At the center temperature of the thickness of the hot-rolled plate, when the average cooling rate in the temperature range from the start of cooling to the cooling stop temperature described later is less than 5 ° C./s, the area ratio of bainite decreases due to the formation of ferrite, and in the present invention. The desired strength cannot be obtained. On the other hand, when the average cooling rate exceeds 25 ° C./s, the average aspect ratio of bainite exceeds 0.8. As a result, the yield ratio tends to exceed 90%. The average cooling rate is preferably 10 ° C./s or higher, and preferably 20 ° C./s or lower.
熱延板の板厚中心温度で、冷却停止温度が450℃未満では、ベイナイトの平均アスペクト比が0.8を超え、その結果、降伏比が90%を超えやすくなる。一方で、冷却停止温度が650℃を超えると、ベイナイト変態開始温度を上回るためベイナイトの面積率を60%以上とすることができない。冷却停止温度は、好ましくは480℃以上とし、好ましくは620℃以下とする。 Cooling stop temperature: 450-650 ° C
At the center temperature of the thickness of the hot-rolled plate, when the cooling stop temperature is less than 450 ° C., the average aspect ratio of bainite exceeds 0.8, and as a result, the yield ratio tends to exceed 90%. On the other hand, when the cooling stop temperature exceeds 650 ° C., the bainite transformation start temperature is exceeded, so that the area ratio of bainite cannot be 60% or more. The cooling stop temperature is preferably 480 ° C. or higher, and preferably 620 ° C. or lower.
縮径圧延での縮径率が0.2%未満の場合、上記した本発明の鋼管の鋼素材では塑性変形による残留応力の低減が不十分となる。その結果、鋼管外表面における管軸方向の残留応力が250MPaを超える。また、加工度不足により降伏比が80%未満となる。一方、縮径圧延での縮径率が0.5%を超えると、加工硬化により、降伏比が90%を超える。その結果、所望の塑性変形能、すなわち耐座屈性能を得られなくなる。また、上記の残留応力が250MPaを超えても、耐座屈性能が低下する。 Diameter reduction ratio in reduced diameter rolling: 0.2 to 0.5%
When the diameter reduction ratio in the reduced diameter rolling is less than 0.2%, the steel material of the steel pipe of the present invention described above is insufficient in reducing the residual stress due to plastic deformation. As a result, the residual stress in the pipe axial direction on the outer surface of the steel pipe exceeds 250 MPa. In addition, the yield ratio is less than 80% due to insufficient processing. On the other hand, when the diameter reduction ratio in diameter reduction rolling exceeds 0.5%, the yield ratio exceeds 90% due to work hardening. As a result, the desired plastic deformability, that is, the buckling resistance performance cannot be obtained. Further, even if the residual stress exceeds 250 MPa, the buckling resistance performance deteriorates.
組織観察用の試験片は、電縫溶接部を0°としたとき円周方向90°位置の管軸方向断面が観察面となるように採取し、研磨した後、ナイタール腐食して作製した。組織観察は、光学顕微鏡(倍率:1000倍)または走査型電子顕微鏡(SEM、倍率:1000倍)を用いて、電縫鋼管の外表面から板厚tの1/4t深さ位置における組織を観察し、撮像した。得られた光学顕微鏡像およびSEM像から、ベイナイトの面積率を求めた。ベイナイトの面積率は、5視野以上で観察を行い、各視野で得られた値の平均値として算出した。 [Tissue observation]
The test piece for observing the structure was prepared by collecting the test piece so that the cross section in the pipe axis direction at the position of 90 ° in the circumferential direction becomes the observation surface when the electric stitch welded portion was set to 0 °, polishing it, and then corroding it with nital. For microstructure observation, use an optical microscope (magnification: 1000 times) or a scanning electron microscope (SEM, magnification: 1000 times) to observe the structure at a depth of 1/4 t of the plate thickness t from the outer surface of the electrosewn steel tube. And imaged. The area ratio of bainite was determined from the obtained optical microscope image and SEM image. The area ratio of bainite was calculated as the average value of the values obtained in each field of view by observing in 5 or more fields of view.
引張試験は、得られた電縫鋼管の電縫溶接部を0°としたとき円周方向90°位置において、引張方向が管軸方向と平行になるように、JIS5号の引張試験片を採取した。JIS Z 2241の規定に準拠して引張試験を実施した。0.2%耐力(降伏強度YS)、引張強さTSを測定し、(0.2%耐力)/(引張強さ)で定義される降伏比を算出した。 [Tensile test]
In the tensile test, a tensile test piece of JIS No. 5 was collected so that the tensile direction was parallel to the pipe axis direction at a position of 90 ° in the circumferential direction when the electric resistance welded portion of the obtained electric resistance pipe was 0 °. did. Tensile tests were carried out in accordance with JIS Z 2241. 0.2% proof stress (yield strength YS) and tensile strength TS were measured, and the yield ratio defined by (0.2% proof stress) / (tensile strength) was calculated.
シャルピー衝撃試験は、得られた電縫鋼管の電縫溶接部を0°としたとき円周方向90°位置において、板厚t/2位置から、試験片長手方向が管軸方向と平行となるように、Vノッチ試験片を採取した。JIS Z 2242の規定に準拠して、試験温度:-30℃でシャルピー衝撃試験を実施し、吸収エネルギー(J)を求めた。なお、試験片の本数は各3本とし、その平均値を算出して吸収エネルギー(J)を求めた。 [Charpy impact test]
In the Charpy impact test, the longitudinal direction of the test piece is parallel to the pipe axis direction from the plate thickness t / 2 position at the position of 90 ° in the circumferential direction when the power stitch welded portion of the obtained power-sewn steel pipe is 0 °. As described above, a V-notch test piece was collected. The Charpy impact test was carried out at a test temperature of −30 ° C. in accordance with JIS Z 2242 to determine the absorbed energy (J). The number of test pieces was 3 each, and the average value was calculated to obtain the absorbed energy (J).
残留応力は、パルステック製 μ-X360を用いてX線回折 cosα法により測定した。残留応力の測定位置は、得られた電縫鋼管の管長手中央の外面とし、電縫溶接部を0°としたとき、90°位置、180°位置、270°位置の3か所とした。得られた3か所の測定値の平均値を残留応力とした。なお、応力測定方向は管軸方向とした。 [Measurement of residual stress]
The residual stress was measured by the X-ray diffraction cosα method using μ-X360 manufactured by Pulstec. The residual stress was measured at three positions, 90 °, 180 °, and 270 °, when the electric resistance welded portion was 0 °, with the outer surface of the obtained electric resistance pipe at the center of the length of the pipe. The average value of the obtained three measured values was taken as the residual stress. The stress measurement direction was the pipe axis direction.
本発明では、鋼管杭としての性能評価のために、部材圧縮試験を行い、座屈強度比σcr / σy(なお、σcrは座屈応力度、σyは材料降伏強度である。)を求めた。座屈強度比が低減係数R = 0.8+2.5×t / r(なお、tは板厚、rは半径である。)より大きければ鋼管杭の性能として重要な座屈強度が十分であると判断できる。 [Member compression test]
In the present invention, in order to evaluate the performance of the steel pipe pile, a member compression test was performed to determine the buckling strength ratio σcr / σy (where σcr is the buckling stress and σy is the material yield strength). If the buckling strength ratio is larger than the reduction coefficient R = 0.8 + 2.5 × t / r (t is the plate thickness and r is the radius), the buckling strength, which is important for the performance of steel pipe piles, is sufficient. I can judge.
Claims (6)
- 母材部と管軸方向に溶接部を有する電縫鋼管であって、
母材部の成分組成は、質量%で、
C:0.12~0.20%、
Si:0.60%以下、
Mn:0.50~1.70%、
P:0.030%以下、
S:0.015%以下、
Al:0.010~0.060%、
Nb:0.010~0.080%、
Ti:0.010~0.050%、
N:0.006%以下
を含有し、残部がFeおよび不可避的不純物からなり、
前記母材部の板厚をtとしたとき、前記電縫鋼管の外表面から板厚tの1/4t深さ位置における鋼組織は、
ベイナイトが面積率で60%以上であり、
前記ベイナイトの平均有効粒径が平均円相当径で20.0μm以下、かつ前記ベイナイトの平均アスペクト比が0.1~0.8であり、
管軸方向の引張強さが590MPa以上、0.2%耐力が450MPa以上、降伏比が80~90%であり、
前記母材部における管軸方向を試験片長手方向とした-30℃におけるシャルピー吸収エネルギーが70J以上であり、
前記母材部における鋼管外表面の管軸方向における残留応力が250MPa以下である電縫鋼管。 An electrosewn steel pipe having a base metal part and a welded part in the pipe axis direction.
The composition of the base material is mass%,
C: 0.12 to 0.20%,
Si: 0.60% or less,
Mn: 0.50 to 1.70%,
P: 0.030% or less,
S: 0.015% or less,
Al: 0.010 to 0.060%,
Nb: 0.010 to 0.080%,
Ti: 0.010 to 0.050%,
N: Contains 0.006% or less, the balance consists of Fe and unavoidable impurities,
When the plate thickness of the base metal portion is t, the steel structure at a depth of 1/4 t of the plate thickness t from the outer surface of the electrosewn steel pipe is
Bainite has an area ratio of 60% or more,
The average effective particle size of the bainite is 20.0 μm or less in the diameter equivalent to the average circle, and the average aspect ratio of the bainite is 0.1 to 0.8.
The tensile strength in the tube axis direction is 590 MPa or more, the 0.2% proof stress is 450 MPa or more, and the yield ratio is 80 to 90%.
The Charpy absorption energy at −30 ° C. with the tube axis direction in the base metal portion as the longitudinal direction of the test piece is 70 J or more.
An electrosewn steel pipe having a residual stress of 250 MPa or less in the pipe axial direction on the outer surface of the steel pipe in the base material portion. - 前記成分組成に加えてさらに、質量%で、B:0.008%以下を含有することを特徴とする請求項1に記載の電縫鋼管。 The electric resistance steel pipe according to claim 1, further containing B: 0.008% or less in mass% in addition to the component composition.
- 前記成分組成に加えてさらに、質量%で、
Cr:0.01~1.0%、
V:0.010~0.060%、
Mo:0.01~1.0%、
Cu:0.01~0.50%、
Ni:0.01~1.0%、
Ca:0.0005~0.010%
のうちから選ばれた1種または2種以上を含有する請求項1または2に記載の電縫鋼管。 In addition to the above component composition, in% by mass,
Cr: 0.01-1.0%,
V: 0.010 to 0.060%,
Mo: 0.01-1.0%,
Cu: 0.01-0.50%,
Ni: 0.01-1.0%,
Ca: 0.0005-0.010%
The electric resistance welded steel pipe according to claim 1 or 2, which contains one or more selected from the above. - 鋼素材に、熱間圧延工程、冷却工程をこの順に施して熱延鋼板とし、さらに、該熱延鋼板に冷間ロール成形工程を施して電縫鋼管とする電縫鋼管の製造方法であって、
前記鋼素材は、請求項1~3のいずれか1項に記載の成分組成を有し、
前記熱間圧延工程は、前記鋼素材を加熱温度:1100~1280℃に加熱した後、粗圧延終了温度:850~1150℃、仕上圧延終了温度:750~850℃、かつ、粗圧延と仕上圧延における930℃以下での合計圧下率:65%以上とする粗圧延および仕上圧延を施して熱延板とする工程であり、
前記冷却工程は、前記熱延板を、板厚中心温度で、冷却開始から冷却停止までの平均冷却速度:5~25℃/s、冷却停止温度:450~650℃で冷却する工程であり、
前記冷間ロール成形工程は、前記熱延鋼板にロール成形加工を施した鋼管素材を溶接し、溶接後の鋼管外面の周長に対して縮径率:0.2~0.5%の縮径圧延を行う電縫鋼管の製造方法。 This is a method for manufacturing a hot-rolled steel pipe in which a hot-rolling process and a cooling process are applied to a steel material in this order to obtain a hot-rolled steel sheet, and further, a cold roll forming process is applied to the hot-rolled steel sheet to obtain an electric-sewn steel pipe. ,
The steel material has the component composition according to any one of claims 1 to 3.
In the hot rolling step, after heating the steel material to a heating temperature of 1100 to 1280 ° C., rough rolling end temperature: 850 to 1150 ° C., finish rolling end temperature: 750 to 850 ° C., and rough rolling and finish rolling. Total rolling reduction at 930 ° C. or lower: 65% or more in rough rolling and finish rolling to obtain a hot-rolled plate.
The cooling step is a step of cooling the hot-rolled plate at a plate thickness center temperature at an average cooling rate of 5 to 25 ° C./s from the start of cooling to the stop of cooling and a cooling stop temperature of 450 to 650 ° C.
In the cold roll forming step, a steel pipe material that has been roll-formed is welded to the hot-rolled steel sheet, and the diameter reduction ratio is 0.2 to 0.5% with respect to the peripheral length of the outer surface of the steel pipe after welding. A method for manufacturing an electrosewn steel pipe for diameter rolling. - 請求項1~3のいずれか1項に記載の成分組成を有し、板厚をtとしたとき、外表面から板厚tの1/4t深さ位置における鋼組織は、ベイナイトが面積率で60%以上であり、前記ベイナイトの平均有効粒径が平均円相当径で20.0μm以下、かつ前記ベイナイトの平均アスペクト比が0.1~0.8である熱延鋼板に冷間ロール成形工程を施して電縫鋼管とする電縫鋼管の製造方法であって、
前記冷間ロール成形工程は、前記熱延鋼板にロール成形加工を施した鋼管素材を溶接し、溶接後の鋼管外面の周長に対して縮径率:0.2~0.5%の縮径圧延を行う電縫鋼管の製造方法。 When the composition has the component composition according to any one of claims 1 to 3 and the plate thickness is t, bainite is the area ratio of the steel structure at the depth position of 1/4 t of the plate thickness t from the outer surface. A cold roll forming step on a hot-rolled steel sheet having 60% or more, an average effective particle size of the bainite of 20.0 μm or less in an average circle equivalent diameter, and an average aspect ratio of the bainite of 0.1 to 0.8. This is a method for manufacturing bainite steel pipes that are made into bainite steel pipes.
In the cold roll forming step, a steel pipe material that has been roll-formed is welded to the hot-rolled steel sheet, and the diameter reduction ratio is 0.2 to 0.5% with respect to the peripheral length of the outer surface of the steel pipe after welding. A method for manufacturing an electrosewn steel pipe for diameter rolling. - 請求項1~3のいずれか1項に記載の電縫鋼管を用いた鋼管杭。 A steel pipe pile using the electric pipe sewn steel pipe according to any one of claims 1 to 3.
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