WO2011093117A1 - ラインパイプ用継目無鋼管の製造方法及びラインパイプ用継目無鋼管 - Google Patents
ラインパイプ用継目無鋼管の製造方法及びラインパイプ用継目無鋼管 Download PDFInfo
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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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/10—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies
- C21D8/105—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies of ferrous alloys
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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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
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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
- 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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- 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
- 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
- C21D9/085—Cooling or quenching
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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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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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
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
-
- 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
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
-
- 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
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with 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
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
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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
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
- F16L—PIPES; JOINTS OR FITTINGS FOR PIPES; SUPPORTS FOR PIPES, CABLES OR PROTECTIVE TUBING; MEANS FOR THERMAL INSULATION IN GENERAL
- F16L9/00—Rigid pipes
- F16L9/02—Rigid pipes of metal
Definitions
- the present invention relates to a method for producing a seamless steel pipe and a seamless steel pipe, and more particularly to a method for producing a seamless steel pipe for a line pipe and a seamless steel pipe for a line pipe.
- ⁇ Pipelines placed on the ocean floor allow high pressure fluid to pass through. Pipelines are also subject to repeated wave distortions and seawater pressure. Therefore, high strength and high toughness are required for steel pipes used in submarine pipelines.
- High strength can be obtained by increasing the thickness of seamless pipes for line pipes.
- the wall thickness is thick, brittle fracture is likely to occur and the toughness is reduced. Therefore, excellent toughness is particularly required for seamless steel pipes for line pipes used on the sea floor.
- Patent Document 1 A manufacturing method for improving the toughness of a seamless steel pipe for a line pipe is disclosed in Japanese Patent Application Laid-Open No. 2000-104117 (Patent Document 1).
- the steel pipe temperature immediately after piercing and rolling is set to 950 ° C. or higher.
- the steel pipe is soaked to a temperature of 900 ° C. to 1000 ° C. without making the steel pipe temperature below the Ar3 point.
- the soaked steel pipe is cooled at a cooling rate of 5 ° C./sec or more.
- Patent Document 2 A manufacturing method for improving the toughness of other steel pipes that are not seamless pipes for line pipes is disclosed in JP-A-63-215309 (Patent Document 2), JP-A-9-3539 (Patent Document 3), Japanese Patent Application Laid-Open No. 2008-266700 (Patent Document 4), Japanese Patent No. 3755163 (Patent Document 5) and Japanese Patent No. 3855300 (Patent Document 6).
- Patent Document 2 uses a piercer, a mandrel mill, a cooling facility, a reheat furnace, and a stretch reducer.
- a billet is perforated with a piercer to form a blank tube.
- the base tube is drawn and rolled by a mandrel mill.
- the stretched and rolled raw tube is cooled to a point below Ar1 by a cooling facility.
- the cooled raw tube is subjected to constant diameter rolling with a stretch reducer.
- Patent Document 3 cools a finish-rolled steel pipe at a cooling rate equal to or higher than air cooling from a temperature equal to or higher than the Ar3 point. And the cooled steel pipe is tempered at the temperature below Ac1 point.
- Patent Document 4 accelerates and cools a steel pipe that has been rolled with a constant diameter. Then, the accelerated-cooled steel pipe is maintained at a temperature of 350 to 600 ° C.
- Patent Document 5 heats a finish-rolled steel pipe to 850 to 1100 ° C. Then, the heated steel pipe is quenched.
- the quenching cooling rate is not particularly limited.
- Patent Document 6 cools a finish-rolled steel pipe to a temperature of Ar 3 point or less at a cooling rate of 80 ° C./min or more. Then, the cooled steel pipe is quenched and tempered.
- Patent Document 1 improves the toughness of seamless steel pipes for line pipes to some extent. Recently, however, further improvement in toughness of seamless steel pipes for line pipes has been demanded.
- the manufacturing methods of Patent Documents 2 to 6 manufacture steel pipes of different steel types from seamless steel pipes for line pipes. Therefore, these manufacturing methods are not necessarily suitable for improving the toughness of seamless steel pipes for line pipes.
- An object of the present invention is to provide a method for producing a seamless steel pipe for line pipe, which can improve the toughness of the seamless steel pipe for line pipe.
- the present inventors examined a method for further refinement of steel crystal grains in order to improve the toughness of seamless steel pipes for line pipes.
- the present inventors thought that the crystal grain of a steel pipe is refined
- the crystal grains of the seamless steel pipe for line pipe manufactured by this manufacturing method are refined and the toughness is improved.
- the present inventors further thought that the crystal grains are further refined if the water cooling stop temperature is lowered in the accelerated cooling.
- the water cooling stop temperature means the surface temperature of the steel pipe when water cooling is stopped in the accelerated cooling.
- a bainite structure is generated in the steel if the water cooling stop temperature is low.
- the bainite structure is considered to be generated by lattice transformation similarly to the martensite structure, and includes high-density lattice defects such as dislocations.
- fine ⁇ grains are generated starting from high-density lattice defects. Therefore, the crystal grain of the steel pipe after quenching and tempering is refined, and the toughness of the steel pipe is improved.
- FIG. 1 The relationship between the water cooling stop temperature and toughness in accelerated cooling was investigated.
- the relationship between the water cooling stop temperature and toughness is shown in FIG. FIG. 1 was obtained by the following method. A plurality of billets having chemical compositions shown in Table 1 were prepared.
- each billet was heated in a heating furnace. Subsequently, each billet was pierced and rolled by a piercing machine into a raw pipe. Subsequently, each raw tube was stretch-rolled with a stretching mill. Subsequently, each raw pipe was subjected to constant diameter rolling with a constant diameter rolling mill to produce a plurality of seamless steel pipes for line pipes. Subsequently, each manufactured seamless steel pipe was water-cooled (accelerated cooling). At this time, the water cooling stop temperature was changed for each seamless steel pipe. The surface temperature (outer surface temperature) of the seamless steel pipe at the start of water cooling was 1100 ° C. Each seamless steel pipe after cooling was quenched. The quenching temperature was 950 ° C., soaking for 40 minutes. After quenching, each seamless steel pipe was tempered. The tempering temperature was 650 ° C., and soaking was performed for 30 minutes. The seamless pipe for line pipes was manufactured by the above process.
- a v-notch test piece in accordance with JIS Z 2202 was collected from the thickness center of each manufactured seamless steel pipe for line pipe. And using each v notch test piece, the Charpy impact test based on JISZ2242 was implemented, energy transition temperature vTE was calculated
- the method for producing a seamless steel pipe for a line pipe includes, in mass%, C: 0.02 to 0.15%, Si: 0.5% or less, and Mn: 0.5 to 2.5%.
- the balance is a step of heating a round billet having a chemical composition comprising Fe and impurities, a step of piercing and rolling the heated round billet, and manufacturing a blank, A step of producing a steelless tube, a step of water-cooling the produced seamless steel tube, stopping the water cooling when the temperature of the seamless steel tube becomes 450 ° C. or less, and a step of quenching the water-cooled seamless steel tube; And tempering the quenched seamless steel pipe.
- the method for producing a seamless steel pipe for a line pipe further includes a step of heating the produced seamless steel pipe to 900 ° C. to 1100 ° C. In the water cooling step, the heated seamless steel pipe is water cooled.
- the chemical composition of the round billet is further Cu: 1.5% or less, Ni: 1.5% or less, Cr: 1.0% or less, Mo: 0.8% or less, V: 0.2% or less Nb: 0.06% or less and Ti: 0.05% or less, or one or more selected from the group consisting of 0.05% or less.
- the seamless steel pipe for line pipe according to the present invention is manufactured by the above-described manufacturing method.
- FIG. 1 is a diagram showing the relationship between the energy transition temperature and the water cooling stop temperature of a seamless steel pipe for a line pipe according to the present invention.
- FIG. 2 is a block diagram showing a configuration of a production equipment line for seamless pipes for line pipes according to the present invention.
- FIG. 3 is a flowchart showing a manufacturing flow of a seamless steel pipe for a line pipe using the manufacturing equipment line shown in FIG.
- FIG. 4 is a diagram showing changes in the surface temperature of the material in each step in the manufacturing flow shown in FIG.
- FIG. 5 is a graph showing the relationship between the strength of the seamless steel pipe for line pipe of Example 1 and the water cooling stop temperature.
- FIG. 6 is a diagram showing the relationship between the strength of the seamless steel pipe for line pipe of Example 2 and the water cooling stop temperature.
- FIG. 7 is a graph showing the relationship between the energy transition temperature and the water cooling stop temperature of the seamless steel pipe for line pipe of Example 2.
- the seamless steel pipe for line pipes according to the embodiment of the present invention has the following chemical composition.
- % regarding an alloy element means the mass%.
- C 0.02 to 0.15% Carbon (C) improves the strength of the steel.
- the lower limit value of the C content is 0.02%.
- the upper limit of C content is 0.15%.
- the C content is preferably 0.04 to 0.12%, more preferably 0.04 to 0.09%.
- Si 0.5% or less Silicon (Si) deoxidizes steel. However, when Si is contained excessively, the toughness of steel decreases. Therefore, the Si content is 0.5% or less. A preferable Si content is 0.05 to 0.35%.
- Mn 0.5 to 2.5%
- Mn Manganese
- the lower limit of the Mn content is 0.5%.
- Mn is segregated. Therefore, the toughness of the weld heat affected zone and the base material decreases. Therefore, the upper limit of Mn content is 2.5%.
- a preferable Mn content is 0.5 to 2.2%.
- the balance is iron (Fe) and impurities.
- Impurities include phosphorus (P), sulfur (S), oxygen (O), nitrogen (N), aluminum (Al), and the like.
- P causes central segregation.
- S forms Mn and MnS and lowers the toughness of the steel.
- O reduces the cleanliness of the steel.
- N dissolves in steel and lowers the toughness of the steel.
- Al deoxidizes steel. However, Al decreases the cleanliness of steel and decreases toughness. Therefore, in the present invention, Al is an impurity.
- Preferred P content is 0.015% or less.
- a preferable S content is 0.004% or less.
- a preferable O content is 0.01% or less.
- a preferable N content is 0.007% or less.
- a preferable Al content is 0.05% or less.
- the chemical composition of the seamless steel pipe for line pipe according to the present embodiment may further contain a selective element described below.
- Cu copper
- Ni nickel
- Cr chromium
- Mo molybdenum
- Cu 1.5% or less Copper (Cu) is a selective element. Cu increases the hardenability of the steel and improves the strength of the steel. If Cu is contained even a little, the above effect can be obtained. A preferable Cu content is 0.05% or more. On the other hand, if Cu is contained excessively, the weldability of the steel decreases. Furthermore, since Cu lowers the grain boundary strength at high temperatures, the steel tends to crack during hot rolling. Therefore, the Cu content is 1.5% or less.
- Nickel (Ni) is a selective element. Ni increases the hardenability of the steel and improves the strength of the steel. If Ni is contained even a little, the above effect can be obtained. A preferable Ni content is 0.05% or more. On the other hand, if Ni is contained excessively, the above effect is saturated. Therefore, the Ni content is 1.5% or less.
- Chromium (Cr) is a selective element. Cr increases the hardenability of the steel and improves the strength of the steel. Cr further increases the temper softening resistance of the steel. If Cr is contained even a little, the above effect can be obtained. A preferable Cr content is 0.02% or more. On the other hand, if Cr is excessively contained, the weldability of the steel is lowered and the toughness of the steel is also lowered. Therefore, the Cr content is 1.0% or less.
- Mo 0.8% or less Molybdenum (Mo) is a selective element. Mo increases the hardenability of the steel and improves the strength of the steel. If Mo is contained even a little, the above effect can be obtained. A preferable Mo content is 0.02% or more. On the other hand, if Mo is contained excessively, the toughness of the steel is lowered and the weldability is also lowered. Therefore, the Mo content is 0.8% or less.
- V, Nb, and Ti all precipitate carbonitride and improve the strength and toughness of the steel.
- these elements will be described in detail.
- V 0.2% or less
- Nb 0.06% or less
- V and Nb both generate carbonitrides and contribute to the refinement of steel crystal grains. Therefore, V and Nb improve the strength and toughness of steel. If V and / or Nb is contained even a little, the above effect can be obtained.
- a preferable V content is 0.01% or more, and a preferable Nb content is 0.01% or more.
- V and Nb are contained excessively, the toughness of the welded portion of steel is lowered. Therefore, the V content is 0.2% or less and the Nb content is 0.06% or less.
- the upper limit of the preferable V content is 0.1%, and the upper limit of the preferable Nb content is 0.03%.
- Titanium (Ti) is a selective element. Ti generates carbonitrides and contributes to refinement of steel crystal grains. Therefore, Ti improves the strength and toughness of steel. If Ti is contained even a little, the above effect can be obtained. A preferable Ti content is 0.002% or more. However, if Ti is excessively contained, the toughness of the steel is lowered. Therefore, the Ti content is 0.05% or less. A preferable upper limit of the Ti content is 0.03%.
- FIG. 2 is a block diagram showing an example of a production line for seamless steel pipes for line pipes according to the present embodiment.
- the production line includes a heating furnace 1, a piercing machine 2, a drawing mill 3, a constant diameter rolling mill 4, a reheating furnace 5, a water cooling device 6, a quenching device 7, A tempering device 8 is provided.
- a plurality of transport rollers 10 are arranged between the devices.
- a quenching device 7 and a tempering device 8 are also included in the production line.
- the hardening device 7 and the tempering device 8 may be arranged away from the production line. In short, the hardening device 7 and the tempering device 8 may be arranged off-line.
- FIG. 3 is a flowchart showing the manufacturing process of the seamless steel pipe according to the present embodiment, and FIG. 4 shows the change of the surface temperature with respect to the time of the rolled material (round billet, blank pipe and seamless steel pipe) being manufactured.
- FIG. 4 shows the change of the surface temperature with respect to the time of the rolled material (round billet, blank pipe and seamless steel pipe) being manufactured.
- the round billet is heated in heating furnace 1 (S1). Subsequently, the heated round billet is hot-worked into a seamless steel pipe (S2 and S3). Specifically, a round billet is pierced and rolled by a piercing machine 2 to form a raw pipe (S2). Further, the raw pipe is rolled by a drawing mill 3 or a constant diameter rolling mill 4 to obtain a seamless steel pipe (S3).
- the seamless steel pipe manufactured by hot working is heated to a predetermined temperature by the auxiliary heating furnace 5 as necessary (S4).
- the seamless steel pipe is cooled with water by the water cooling device 6 (accelerated cooling), and the surface temperature of the seamless steel pipe is set to 450 ° C. or less (S5).
- the water-cooled seamless steel pipe is quenched by the quenching device 7 (S6) and tempered by the tempering device 8 (S7).
- S6 quenching device 7
- S7 tempering device 8
- Heating step (S1) First, the round billet is heated in the heating furnace 1.
- a preferred heating temperature is 1050 ° C. to 1300 ° C. If the round billet is heated within this temperature range, the hot workability of the round billet during piercing and rolling is good, and the occurrence of surface flaws is suppressed. Moreover, if a round billet is heated in this temperature range, the coarsening of a crystal grain will be suppressed.
- the heating furnace 1 is, for example, a known walking beam furnace or a rotary furnace.
- the round billet is taken out from the heating furnace 1. Then, the heated round billet is pierced and rolled by the piercing machine 2.
- the drilling machine 2 has a known configuration. Specifically, the punching machine 2 includes a pair of inclined rolls and a plug disposed between the inclined rolls.
- a preferred drilling machine 2 is a cross-type drilling machine. This is because piercing and rolling with a high expansion ratio is possible.
- the drawing mill 3 includes a plurality of roll stands arranged in series.
- the drawing mill 3 is, for example, a mandrel mill.
- the drawn and rolled raw pipe is subjected to constant diameter rolling by a constant diameter rolling mill 4 to produce a seamless steel pipe.
- the constant diameter rolling mill 4 includes a plurality of roll stands arranged in series.
- the constant diameter rolling mill 4 is, for example, a sizer or a stretch reducer.
- the temperature of the outer surface of the raw tube rolled by the last roll stand among the plurality of roll stands of the constant diameter rolling mill 4 is defined as “finishing temperature”.
- the finishing temperature is measured by, for example, a temperature sensor arranged on the exit side of the last roll stand of the constant diameter rolling mill 4.
- a preferable finishing temperature is not less than A3 point (more specifically, Ac3 point) as shown in FIG. 4, preferably 900 ° C. or more, and more preferably 950 ° C. or more.
- the Ac3 point of the seamless steel pipe having the chemical composition of the present invention is 750 to 950 ° C.
- the finishing temperature is 900 ° C. or higher, heat loss due to heat removal from the roll is small in the raw tube during constant diameter rolling. Therefore, the temperature unevenness of the manufactured seamless steel pipe can be reduced.
- a heating furnace may be disposed between the stretching mill 3 and the constant diameter mill 4.
- the stretched and rolled raw tube is heated in a heating furnace.
- the heated raw tube is subjected to constant diameter rolling by a constant diameter rolling mill 4. Therefore, the raw tube temperature at the time of constant diameter rolling becomes high, and the load applied to the constant diameter rolling mill 4 is reduced.
- a reheating process (S4) is implemented as needed.
- the reheating step may not be performed.
- the supplementary heating furnace 5 is not arrange
- the manufactured seamless steel pipe is charged into the reheating furnace 5 and heated. Thereby, the temperature nonuniformity of the manufactured seamless steel pipe can be reduced.
- the heating temperature in the auxiliary heating furnace 5 is Ar 3 to 1100 ° C., preferably 900 to 1100 ° C., more preferably 950 to 1100 ° C. If the heating temperature is less than the Ar3 point, the ⁇ phase precipitates, the structure becomes non-uniform, and the strength variation increases. On the other hand, when heating temperature exceeds 1100 degreeC, a crystal grain will coarsen.
- a preferred heating time is 1 to 30 minutes.
- the seamless steel pipe manufactured in step S3 or the seamless steel pipe reheated in step S4 is water cooled (accelerated cooling) by the water cooling device 6.
- the surface temperature of the seamless steel pipe immediately before water cooling is substantially the same as the finishing temperature or the heating temperature in the auxiliary heating furnace. That is, the surface temperature of the seamless steel pipe immediately before water cooling is Ar3 point or higher, preferably 900 ° C or higher, more preferably 950 ° C or higher.
- the water cooling device 6 includes a plurality of rotating rollers, a laminar water flow device, and a jet water flow device.
- the plurality of rotating rollers are arranged in two rows, and the seamless steel pipe is arranged between the plurality of rotating rollers arranged in two rows. At this time, each of the two rows of rotating rollers comes into contact with the lower part of the outer surface of the seamless steel pipe.
- the laminar water flow device is disposed above the rotating roller and pours water from above into the seamless steel pipe. At this time, the water poured into the seamless steel pipe forms a laminar water flow.
- the jet water flow device is arranged in the vicinity of the end of the seamless steel pipe arranged on the rotating roller.
- a jet water flow apparatus injects a jet water flow toward the inside of a steel pipe from the end of a seamless steel pipe. The outer surface and the inner surface of the seamless steel pipe are simultaneously cooled by the laminar water flow device and the jet water flow device.
- the water cooling device 6 cools the seamless steel pipe until the surface temperature of the seamless steel pipe becomes 450 ° C. or less.
- the water cooling stop temperature is 450 ° C. or lower. If the water cooling stop temperature is set to 450 ° C. or lower, the structure undergoes bainite transformation as described above. By quenching in the subsequent process, the crystal grains of the seamless steel pipe are further refined. As a result, the toughness of the seamless pipe for line pipe is improved.
- the water cooling stop temperature is 300 ° C. or higher, more preferably 350 ° C. or higher, and further preferably 400 ° C. or higher. If the water cooling stop temperature is made as high as possible within the range of 450 ° C. or less, the time required to heat the seamless steel pipe to the quenching temperature can be shortened at the time of quenching in the next step. Moreover, the amount of heat required for heating the seamless steel pipe to the quenching temperature can be reduced.
- the preferable cooling rate of the water cooling device 6 is 10 ° C./sec or more.
- the water cooling device 6 may be a device other than the above-described rotating roller, laminar water flow device, and jet water flow device.
- the water cooling device 6 may be a water tank, for example. In this case, the seamless steel pipe manufactured in step S3 is immersed in the water tank and cooled. Such a cooling method is called “dobu-zuke”.
- the water cooling device 6 may also be only a laminar water flow device. In short, the type of the cooling device 6 is not limited as long as the seamless steel pipe can be cooled at a cooling rate of 10 ° C./sec or more.
- the water cooling device 6 and the quenching device 7 for the next process are preferably arranged continuously. This is because the closer the quenching device 7 is to the water cooling device 6, the more the amount of heat required to heat the seamless tube after the water cooling step to the quenching temperature can be reduced.
- the seamless steel pipe cooled by the water cooling device 6 is quenched. Specifically, the seamless steel pipe is heated to the quenching temperature and soaked at the quenching temperature. After soaking, the seamless steel pipe is quenched by water cooling or the like. A preferable quenching temperature is higher than the Ac3 point and 1000 ° C. or lower.
- the structure of the seamless steel pipe transforms from bainite to a fine austenite structure. That is, reverse transformation occurs. At this time, the crystal grains are refined.
- accelerated cooling is performed in step S5, and the water cooling stop temperature is set to 450 ° C. or lower, whereby the refinement of crystal grains can be promoted in the quenching process.
- the quenching temperature is less than the Ac3 transformation point, the reverse transformation does not occur sufficiently.
- the quenching temperature exceeds 1000 ° C., the crystal grains become coarse.
- a preferable soaking time for the quenching treatment is 10 seconds to 30 minutes.
- Tempered steel pipes are tempered.
- the tempering temperature is equal to or lower than the Ac1 point, and is adjusted based on desired mechanical characteristics.
- the Ac1 point of the seamless steel pipe having the chemical composition of the present invention is 680 to 720 ° C.
- the strength grade of the seamless steel pipe of the present invention can be adjusted to X60 (yield stress is 415 MPa or more and tensile strength is 520 MPa or more) based on the API standard.
- the variation in the tempering temperature is preferably ⁇ 10 ° C., more preferably ⁇ 5 ° C. If the variation in the tempering temperature is small, the desired mechanical properties are easily obtained.
- the manufactured seamless steel pipe for line pipes has excellent toughness as described above.
- a seamless steel pipe for line pipes having the chemical composition shown in Table 1 was produced, and the strength and toughness were investigated.
- the quenching temperature was 950 ° C., soaking for 40 minutes. After quenching, each seamless steel pipe was tempered. The tempering temperature was 650 ° C., and soaking was performed for 30 minutes. The seamless pipe for line pipes was manufactured by the above process.
- FIG. 5 shows the relationship between the obtained yield stress and tensile strength and the water cooling stop temperature.
- S1 in FIG. 5 is a graph of yield stress.
- S2 is a graph of tensile strength.
- the strength grade of the sample whose water cooling stop temperature is 450 ° C. or less was API standard X60 or more (yield stress is 415 MPa or more, and tensile strength is 520 MPa or more).
- a plurality of billets having the chemical composition shown in Table 2 were produced.
- Example 2 By the same manufacturing method as Example 1, the steel pipe for line pipes was manufactured using each billet. And by the same test method as Example 1, the relationship between strength (yield stress and tensile strength) and the water cooling stop temperature and the relationship between the energy transition temperature vTE (° C.) and the water cooling stop temperature were determined.
- the finishing temperature of the seamless steel pipe was 1050 ° C.
- the quenching temperature was 920 ° C., and the soaking time was 20 minutes.
- the tempering temperature was 650 ° C., and the soaking time was 30 minutes.
- Other conditions were the same as in Example 1.
- FIG. 6 shows the relationship between the obtained yield stress and tensile strength and the water cooling stop temperature.
- S1 is a yield stress graph
- S2 is a tensile strength graph.
- the relationship between the obtained energy transition temperature and water cooling stop temperature is shown in FIG.
- the energy transition temperature rapidly decreased with a decrease in temperature until reaching 450 ° C., as in FIG. And at 450 degrees C or less, the energy transition temperature did not fall so much with respect to the fall of water cooling stop temperature.
- the water cooling stop temperature was 450 ° C. or lower, the energy transition temperature was ⁇ 60 ° C. or lower, indicating good toughness.
- the strength grade of the sample whose water cooling stop temperature is 450 ° C. or lower was API standard X70 or higher (yield stress is 485 MPa or higher, and tensile strength is 570 MPa or higher).
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Abstract
Description
本発明の実施の形態によるラインパイプ用継目無鋼管は、以下の化学組成を有する。以降、合金元素に関する%は質量%を意味する。
炭素(C)は、鋼の強度を向上する。ラインパイプに必要な強度を有するために、C含有量の下限値は0.02%である。一方、Cが過剰に含有されると、ラインパイプの溶接部の溶接熱影響部及び母材の靭性が低下する。そのため、C含有量の上限値は0.15%である。好ましいC含有量は、0.04~0.12%であり、さらに好ましくは、0.04~0.09%である。
珪素(Si)は、鋼を脱酸する。しかしながら、Siが過剰に含有されると、鋼の靭性が低下する。そのため、Si含有量は0.5%以下とする。好ましいSi含有量は、0.05~0.35%である。
マンガン(Mn)は鋼の焼入れ性を高め、鋼の強度を向上する。ラインパイプに必要な強度を有するために、Mn含有量の下限値は0.5%である。一方、Mnが過剰に含有されると、Mnが偏析する。そのため、溶接熱影響部及び母材の靭性が低下する。そのため、Mn含有量の上限値は2.5%である。好ましいMn含有量は0.5~2.2%である。
銅(Cu)は選択元素である。Cuは鋼の焼入れ性を高め、鋼の強度を向上する。Cuが少しでも含有されれば、上記効果が得られる。好ましいCu含有量は0.05%以上である。一方、Cuが過剰に含有されれば、鋼の溶接性が低下する。さらに、Cuは高温における粒界強度を下げるため、熱間圧延時に鋼が割れやすくなる。したがって、Cu含有量は1.5%以下である。
ニッケル(Ni)は選択元素である。Niは鋼の焼入れ性を高め、鋼の強度を向上する。Niが少しでも含有されれば、上記効果が得られる。好ましいNi含有量は0.05%以上である。一方、Niが過剰に含有されれば、上記効果は飽和する。したがって、Ni含有量は1.5%以下である。
クロム(Cr)は選択元素である。Crは鋼の焼入れ性を高め、鋼の強度を向上する。Crはさらに、鋼の焼戻し軟化抵抗を高める。Crが少しでも含有されれば、上記効果が得られる。好ましいCr含有量は0.02%以上である。一方、Crが過剰に含有されれば、鋼の溶接性が低下し、鋼の靭性も低下する。したがって、Cr含有量は1.0%以下である。
モリブデン(Mo)は選択元素である。Moは鋼の焼入れ性を高め、鋼の強度を向上する。Moが少しでも含有されれば、上記効果が得られる。好ましいMo含有量は0.02%以上である。一方、Moが過剰に含有されれば、鋼の靭性が低下し、溶接性も低下する。したがって、Mo含有量は0.8%以下である。
Nb:0.06%以下
バナジウム(V)及びニオブ(Nb)はいずれも選択元素である。V及びNbはいずれも、炭窒化物を生成して、鋼の結晶粒の微細化に寄与する。そのため、V及びNbは、鋼の強度及び靭性を向上する。V及び/又はNbが少しでも含有されれば、上記効果が得られる。好ましいV含有量は、0.01%以上であり、好ましいNb含有量は0.01%以上である。一方、V及びNbが過剰に含有されれば、鋼の溶接部の靭性が低下する。したがって、V含有量は0.2%以下であり、Nb含有量は0.06%以下である。好ましいV含有量の上限は0.1%であり、好ましいNb含有量の上限は0.03%である。
チタン(Ti)は、選択元素である。Tiは炭窒化物を生成して、鋼の結晶粒の微細化に寄与する。そのため、Tiは鋼の強度及び靭性を向上する。Tiが少しでも含有されれば、上記効果が得られる。好ましいTi含有量は、0.002%以上である。しかしながら、Tiが過剰に含有されれば、かえって鋼の靭性が低下する。したがって、Ti含有量は0.05%以下である。好ましいTi含有量の上限は、0.03%である。
図2は、本実施の形態によるラインパイプ用継目無鋼管の製造ラインの一例を示すブロック図である。図2を参照して、製造ラインは、加熱炉1と、穿孔機2と、延伸圧延機3と、定径圧延機4と、補熱炉5と、水冷装置6と、焼入れ装置7と、焼戻し装置8とを備える。各装置間には、複数の搬送ローラ10が配置される。図2では、焼入れ装置7及び焼戻し装置8も製造ラインに含まれている。しかしながら、焼入れ装置7及び焼戻し装置8は、製造ラインから離れて配置されていてもよい。要するに、焼入れ装置7及び焼戻し装置8はオフラインに配置されていてもよい。
図3は、本実施の形態による継目無鋼管の製造工程を示すフロー図であり、図4は、製造中の圧延素材(丸ビレット、素管及び継目無鋼管)の時間に対する表面温度の変化を示す図である。
初めに、丸ビレットを加熱炉1で加熱する。好ましい加熱温度は1050℃~1300℃である。この温度範囲で丸ビレットを加熱すれば、穿孔圧延時の丸ビレットの熱間加工性は良好であり、表面疵の発生が抑制される。また、この温度範囲で丸ビレットを加熱すれば、結晶粒の粗大化が抑制される。加熱炉1はたとえば、周知のウォーキングビーム炉やロータリー炉である。
丸ビレットを加熱炉1から出す。そして、加熱された丸ビレットを穿孔機2により穿孔圧延する。穿孔機2は周知の構成を有する。具体的には、穿孔機2は、一対の傾斜ロールと、傾斜ロール間に配置されるプラグとを備える。好ましい穿孔機2は交叉型の穿孔機である。高い拡管率での穿孔圧延が可能だからである。
次に、素管を延伸圧延機3により延伸圧延する。延伸圧延機3は直列に配列された複数のロールスタンドを含む。延伸圧延機3はたとえば、マンドレルミルである。続いて、延伸圧延された素管を、定径圧延機4により定径圧延して、継目無鋼管を製造する。定径圧延機4は、直列に配列された複数のロールスタンドを含む。定径圧延機4はたとえば、サイザやストレッチレデューサである。
再加熱工程(S4)は、必要に応じて実施される。要するに、再加熱工程を実施しなくてもよい。再加熱工程を実施しない場合、図3において、ステップS3からステップS5に進む。また、再加熱工程を実施しない場合、図2において、補熱炉5は配置されない。
ステップS3で製造された継目無鋼管、又は、ステップS4で再加熱された継目無鋼管を水冷装置6により水冷(加速冷却)する。水冷直前の継目無鋼管の表面温度は仕上げ温度又は補熱炉での加熱温度と実質的に同じである。つまり、水冷直前の継目無鋼管の表面温度は、Ar3点以上であり、好ましくは900℃以上、さらに好ましくは950℃以上である。
水冷装置6により水冷された継目無鋼管を焼入れする。具体的には、継目無鋼管を焼入れ温度まで加熱し、焼入れ温度で均熱する。均熱後、継目無鋼管を水冷等により急冷する。好ましい焼入れ温度はAc3点よりも高く1000℃以下である。継目無鋼管を上記焼入れ温度に加熱すると、継目無鋼管の組織は、ベイナイトから微細なオーステナイト組織に変態する。つまり、逆変態が起こる。このとき、結晶粒が微細化される。つまり、ステップS5で加速冷却が実施され、水冷停止温度を450℃以下にすることにより、焼入れ工程において結晶粒の微細化を促進できる。
焼入れされた鋼管を、焼戻しする。焼戻し温度は、Ac1点以下であり、所望の力学特性に基づいて調整される。本発明の化学組成を有する継目無鋼管のAc1点は、680~720℃である。焼戻し処理により、本発明の継目無鋼管の強度グレードを、API規格に基づくX60(降伏応力が415MPa以上、引張り強度が520MPa以上)以上に調整できる。焼戻し温度のばらつきは、好ましくは±10℃であり、さらに好ましくは±5℃である。焼戻し温度のばらつきが小さければ、所望の力学特性が得られやすい。
表1に示す化学組成を有する複数のビレットを製造した。製造された各ビレット加熱炉により加熱した。続いて、穿孔機により各ビレットを穿孔圧延して素管にした。続いて、マンドレルミルにより各素管を延伸圧延した。続いて、サイザにより各素管を定径圧延し、複数のラインパイプ用継目無鋼管を製造した。続いて、製造された各鋼管を水冷(加速冷却)した。このとき、水冷停止温度を鋼管ごとに変えた。継目無鋼管の仕上げ温度はいずれも1100℃であった。冷却後の各継目無鋼管を焼入れした。焼入れ温度は950℃であり、40分均熱した。焼入れ後、各継目無鋼管を焼戻しした。焼戻し温度は650℃であり、30分均熱した。以上の工程によりラインパイプ用継目無鋼管を製造した。
製造された各ラインパイプ用継目無鋼管の肉厚中央部からJIS Z 2201に準拠した引張り試験片を採取した。そして、引張り試験片を用いて、JIS Z 2241に準拠した引張り試験を常温(25℃)の大気中で実施した。引張り試験により、降伏応力及び引張強度を求めた。本実施例では、降伏応力を0.5%全伸び法により求めた。
製造された各ラインパイプ用継目無鋼管の肉厚中央部からJIS Z 2202に準拠したvノッチ試験片を採取した。そして、各vノッチ試験片を用いて、JIS Z 2242に準拠したシャルピー衝撃試験を実施し、エネルギ遷移温度vTE(℃)を求めた。
得られた降伏応力及び引張強度と水冷停止温度との関係を図5に示す。図5中のS1は、降伏応力のグラフである。S2は引張り強度のグラフである。また、得られたエネルギ遷移温度と水冷停止温度との関係を図1に示す。図1を参照して、水冷停止温度=450℃を境に、曲線C1の傾きが変化した。より具体的には、水冷停止温度が低下するとき、水冷停止温度が450℃になるまで、エネルギ遷移温度は急速に低下した。一方、450℃以下の温度範囲において、水冷停止温度が低下しても、エネルギ遷移温度はそれほど低下しなかった。そして、水冷停止温度が450℃以下である場合、エネルギ遷移温度は-55℃以下となり、良好な靭性を示した。
実施例1と同じ製造方法により、各ビレットを用いてラインパイプ用鋼管を製造した。そして、実施例1と同じ試験方法により、強度(降伏応力及び引張強度)と水冷停止温度との関係、及び、エネルギ遷移温度vTE(℃)と水冷停止温度との関係を求めた。なお、実施例2では、継目無鋼管の仕上げ温度は1050℃であった。焼入れ温度は920℃であり、均熱時間は20分であった。焼戻し温度は650℃であり、均熱時間は30分であった。その他の条件は実施例1と同じであった。
得られた降伏応力及び引張強度と水冷停止温度との関係を図6に示す。図6中のS1は、降伏応力のグラフであり、S2は引張強度のグラフである。また、得られたエネルギ遷移温度と水冷停止温度との関係を図7に示す。
Claims (8)
- 質量%で、C:0.02~0.15%、Si:0.5%以下、Mn:0.5~2.5%を含有し、残部はFe及び不純物からなる化学組成を有する丸ビレットを加熱する工程と、
加熱された丸ビレットを穿孔圧延して素管を製造する工程と、
前記素管を延伸圧延及び定径圧延して継目無鋼管を製造する工程と、
前記継目無鋼管を水冷し、前記継目無鋼管の温度が450℃以下となったときに水冷を停止する工程と、
水冷された前記継目無鋼管を焼入れする工程と、
焼入れされた前記継目無鋼管を焼戻しする工程とを備える、ラインパイプ用継目無鋼管の製造方法。 - 請求項1に記載のラインパイプ用継目無鋼管の製造方法であってさらに、
前記製造された継目無鋼管を900℃~1100℃に加熱する工程を備え、
前記水冷する工程では、前記加熱された継目無鋼管を水冷する、ラインパイプ用継目無鋼管の製造方法。 - 請求項1に記載のラインパイプ用継目無鋼管の製造方法であって、
前記化学組成はさらに、
Cu:1.5%以下、Ni:1.5%以下、Cr:1.0%以下、Mo:0.8%以下、V:0.2%以下、Nb:0.06%以下及びTi:0.05%以下からなる群から選択される1種又は2種以上を含有する、ラインパイプ用継目無鋼管の製造方法。 - 請求項2に記載のラインパイプ用継目無鋼管の製造方法であって、
前記化学組成はさらに、
Cu:1.5%以下、Ni:1.5%以下、Cr:1.0%以下、Mo:0.8%以下、V:0.2%以下、Nb:0.06%以下及びTi:0.05%以下からなる群から選択される1種又は2種以上を含有する、ラインパイプ用継目無鋼管の製造方法。 - 質量%で、C:0.02~0.15%、Si:0.5%以下、Mn:0.5~2.5%を含有し、残部はFe及び不純物からなる化学組成を有し、
熱間加工された後、水冷され、450℃以下となったときに前記水冷を停止され、さらに、焼入れ及び焼戻しされて製造される、ラインパイプ用継目無鋼管。 - 請求項5に記載のラインパイプ用継目無鋼管であってさらに、
前記熱間加工された後であって、水冷される前に、900~1100℃に加熱される、ラインパイプ用継目無鋼管。 - 請求項5に記載のラインパイプ用継目無鋼管であって、
前記化学組成はさらに、
Cu:1.5%以下、Ni:1.5%以下、Cr:1.0%以下、Mo:0.8%以下、V:0.2%以下、Nb:0.06%以下及びTi:0.05%以下からなる群から選択される1種又は2種以上を含有する、ラインパイプ用継目無鋼管。 - 請求項6に記載のラインパイプ用継目無鋼管であって、
前記化学組成はさらに、
Cu:1.5%以下、Ni:1.5%以下、Cr:1.0%以下、Mo:0.8%以下、V:0.2%以下、Nb:0.06%以下及びTi:0.05%以下からなる群から選択される1種又は2種以上を含有する、ラインパイプ用継目無鋼管。
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AU2011210499A1 (en) | 2012-07-19 |
CA2785425A1 (en) | 2011-08-04 |
CN102725428A (zh) | 2012-10-10 |
EP2530172A1 (en) | 2012-12-05 |
CN102725428B (zh) | 2014-01-15 |
US9175360B2 (en) | 2015-11-03 |
BR112012016517A2 (pt) | 2019-01-22 |
MX2012008841A (es) | 2012-12-10 |
EP2530172A4 (en) | 2016-05-11 |
US20120267014A1 (en) | 2012-10-25 |
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JPWO2011093117A1 (ja) | 2013-05-30 |
AR080040A1 (es) | 2012-03-07 |
CA2785425C (en) | 2014-06-03 |
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