WO2014034522A1 - 二相ステンレス鋼管及びその製造方法 - Google Patents

二相ステンレス鋼管及びその製造方法 Download PDF

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Publication number
WO2014034522A1
WO2014034522A1 PCT/JP2013/072424 JP2013072424W WO2014034522A1 WO 2014034522 A1 WO2014034522 A1 WO 2014034522A1 JP 2013072424 W JP2013072424 W JP 2013072424W WO 2014034522 A1 WO2014034522 A1 WO 2014034522A1
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Prior art keywords
stainless steel
duplex stainless
yield strength
pipe
heat treatment
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PCT/JP2013/072424
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English (en)
French (fr)
Japanese (ja)
Inventor
直樹 澤渡
黒田　浩一
正樹 上山
裕介 鵜川
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新日鐵住金株式会社
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Application filed by 新日鐵住金株式会社 filed Critical 新日鐵住金株式会社
Priority to US14/402,882 priority Critical patent/US10184160B2/en
Priority to JP2013542276A priority patent/JP5500324B1/ja
Priority to ES13833720.9T priority patent/ES2623731T3/es
Priority to AU2013310286A priority patent/AU2013310286B2/en
Priority to CN201380034033.1A priority patent/CN104395491A/zh
Priority to IN9674DEN2014 priority patent/IN2014DN09674A/en
Priority to EP13833720.9A priority patent/EP2853614B1/en
Priority to BR112014032621-5A priority patent/BR112014032621B1/pt
Publication of WO2014034522A1 publication Critical patent/WO2014034522A1/ja

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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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
    • B21B3/02—Rolling special iron alloys, e.g. stainless steel
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D3/00—Straightening or restoring form of metal rods, metal tubes, metal profiles, or specific articles made therefrom, whether or not in combination with sheet metal parts
    • B21D3/02—Straightening or restoring form of metal rods, metal tubes, metal profiles, or specific articles made therefrom, whether or not in combination with sheet metal parts by rollers
    • B21D3/04—Straightening or restoring form of metal rods, metal tubes, metal profiles, or specific articles made therefrom, whether or not in combination with sheet metal parts by rollers arranged on axes skew to the path of the work
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/02—Modifying the physical properties of iron or steel by deformation by cold working
    • C21D7/10—Modifying the physical properties of iron or steel by deformation by cold working of the whole cross-section, e.g. of concrete reinforcing bars
    • 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
    • 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
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • 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
    • 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
    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B19/00—Tube-rolling by rollers arranged outside the work and having their axes not perpendicular to the axis of the work
    • B21B19/02—Tube-rolling by rollers arranged outside the work and having their axes not perpendicular to the axis of the work the axes of the rollers being arranged essentially diagonally to the axis of the work, e.g. "cross" tube-rolling ; Diescher mills, Stiefel disc piercers or Stiefel rotary piercers
    • B21B19/06—Rolling hollow basic material, e.g. Assel mills
    • 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
    • C21D2211/001—Austenite
    • 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
    • C21D2211/005—Ferrite

Definitions

  • the present invention relates to a duplex stainless steel pipe and a method for producing the same.
  • This application claims priority based on Japanese Patent Application No. 2012-190996 for which it applied to Japan on August 31, 2012, and uses the content here.
  • Oil well pipes are used for oil wells and gas wells (herein, oil wells and gas wells are collectively referred to as “oil wells”).
  • the oil well has a corrosive environment. Therefore, oil well pipes are required to have corrosion resistance.
  • a duplex stainless steel composed of a duplex structure of austenite and ferrite has excellent corrosion resistance. Therefore, the duplex stainless steel pipe is used for an oil well pipe.
  • casing There are two types of oil well pipes: casing and tubing.
  • the casing is inserted into the well.
  • Cement is filled between the casing and the pit wall, and the casing is fixed in the pit.
  • Tubing is inserted into the casing and allows production fluids such as oil and gas to pass through.
  • Oil well pipes are required to have high strength as well as corrosion resistance.
  • the strength grade of an oil well pipe is generally defined by the tensile yield strength in the pipe axis direction.
  • the user of the oil well pipe calculates the well environment (the formation pressure, the temperature and pressure of the production fluid) to be drilled from the test drill and the geological survey, and selects the oil well pipe of the strength grade that can be used.
  • Patent Document 1 Japanese Laid-Open Patent Publication No. 10-80715 (Patent Document 1) and Japanese Laid-Open Patent Publication No. 11-57842 (Patent Document 2) propose a manufacturing method for increasing the compressive yield strength in the tube axis direction.
  • An object of the present invention is to provide a duplex stainless steel pipe that can be used even when a different stress distribution is applied depending on the use environment.
  • a duplex stainless steel pipe has a tensile yield strength YS LT of 689.1 to 1000.5 MPa in the axial direction of the duplex stainless steel pipe, and the tensile yield strength YS LT , the compressive yield strength YS LC in the pipe axis direction, the tensile yield strength YS CT in the pipe circumferential direction of the duplex stainless steel pipe, and the compressive yield strength YS CC in the pipe circumferential direction all satisfy formulas a to d.
  • the duplex stainless steel pipe described in the above (1) is, in mass%, C: 0.008 to 0.03%; Si: 0 to 1%; Mn: 0.1 to 2%; Cr: 20 Ni: 3-10%; Mo: 0-4%; W: 0-6%; Cu: 0-3%; N: 0.15-0.35% with the balance being iron and It may consist of impurities.
  • duplex stainless steel pipe described in the above (1) or (2) is manufactured by cold working and then performing straightening and low temperature heat treatment at a heat treatment temperature of 350 to 450 ° C. Also good.
  • the duplex stainless steel pipe according to (3) may be manufactured by performing the low-temperature heat treatment after the straightening process.
  • a method for manufacturing a duplex stainless steel pipe according to the second aspect of the present invention includes a process of manufacturing a duplex stainless steel pipe; a process of cold working the blank; By performing straightening and low temperature heat treatment at a heat treatment temperature of 350 to 450 ° C., the tensile yield strength YS LT of 689.1 to 1000.5 MPa is obtained in the tube axis direction of the duplex stainless steel pipe.
  • the tensile yield strength YS LT , the compressive yield strength YS LC in the pipe axis direction, the tensile yield strength YS CT in the pipe circumferential direction of the duplex stainless steel pipe, and the compressive yield strength YS CC in the pipe circumferential direction are: Producing the duplex stainless steel pipe that satisfies all of the formulas (d) to (d).
  • the low-temperature heat treatment may be performed on the raw pipe after the straightening process.
  • the base pipe is, by mass%, C: 0.008 to 0.03%; Si: 0 to 1% Mn: 0.1 to 2%; Cr: 20 to 35%; Ni: 3 to 10%; Mo: 0 to 4%; W: 0 to 6%; Cu: 0 to 3%; N: 0.15 It may contain ⁇ 0.35% with the balance being iron and impurities.
  • duplex stainless steel pipe according to the above aspect of the present invention has a small anisotropy in yield strength, it can be used even when a different stress distribution is applied depending on the use environment.
  • FIG. 1 It is a schematic diagram of an oil well and an oil well pipe. It is sectional drawing of the oil well pipe in FIG. It is other sectional drawing of the oil well pipe in FIG. 1 different from FIG. It is a schematic diagram for demonstrating the cold working of a duplex stainless steel pipe. It is a schematic diagram for demonstrating the behavior of the dislocation within the crystal grain of the duplex stainless steel pipe
  • the present inventors obtained the following knowledge by carrying out various studies and investigations.
  • FIG. 1 is a schematic diagram of an oil well 102 and an oil well pipe 101.
  • oil well pipe 101 is inserted into formation 100.
  • the lower end of the oil well pipe 101 is disposed in the oil well 102.
  • the oil well pipe 101 receives a tensile load FT in the pipe axis direction by its own weight.
  • the production fluid 103 passes through the oil well pipe 101. Since the production fluid 103 has a high temperature, the oil well pipe 101 is thermally expanded. Usually, the upper end and the lower end of the oil well pipe 101 are fixed.
  • the oil well pipe 101 passes the production fluid 103, the oil well pipe 101 receives the compression load FI in the pipe axis direction. As described above, the oil well pipe 101 receives the tensile load FT and the compressive load FI in the pipe axis direction.
  • FIG. 2 is a cross-sectional view of the oil well pipe 101 in FIG. Referring to FIG. 2, when oil well pipe 101 passes production fluid 103 therein, internal pressure PI is applied to oil well pipe 101 by production fluid 103. A tensile load FT is applied in the pipe circumferential direction of the oil well pipe 101 by the internal pressure PI. Further, a compressive load FI is applied in the tube axis direction due to the tensile load FT in the tube circumferential direction.
  • a formation pressure PO that is an external pressure is applied to the outer surface of the oil well pipe 101.
  • a compression load FI is applied in the pipe circumferential direction of the oil well pipe 101 by the formation pressure PO. Then, due to the compressive load FI in the pipe circumferential direction, a tensile load FT is applied in the pipe axis direction.
  • Such a stress distribution also varies depending on the location of the oil well pipe 101.
  • the tubing digs in the ground while rotating around the tube axis. At this time, the most distal portion of the tubing repeatedly receives the tensile load FT and the compressive load FI in the tube axis direction. Further, the oil well pipe 101 arranged in the vicinity of the ground surface is loaded with a tensile load FT in the pipe axis direction and receives a large internal pressure PI.
  • the duplex stainless steel pipe 1 used as the oil well pipe 101 is required not only to have a balance between the tensile yield strength and the compressive yield strength in the tube axis direction but also to have internal pressure resistance and external pressure resistance.
  • the anisotropy of the tensile yield strength and the compressive yield strength of the duplex stainless steel pipe 1 in the tube axial direction and the pipe circumferential direction may be reduced.
  • the cold-worked duplex stainless steel pipe 1 is straightened by an inclined roll type straightening machine 200 and is subjected to low-temperature heat treatment at 350 to 450 ° C.
  • the following (1) to (4) specimen sampling direction of the manufactured duplex stainless steel pipe 1 and the ratio of the yield strength to the tensile yield strength and the compressive yield strength (compression yield) The difference in strength / tensile yield strength is reduced. That is, the anisotropy of yield strength is reduced.
  • the tensile yield strength YS LT (MPa) in the pipe axis direction of the duplex stainless steel pipe 1 the compressive yield strength YS LC (MPa) in the pipe axis direction, and the tensile yield strength in the pipe circumferential direction of the duplex stainless steel pipe 1.
  • YS CT (MPa) and the compressive yield strength YS CC (MPa) in the pipe circumferential direction satisfy Formulas 1 to 4.
  • the reason why the anisotropy of the yield strength of the duplex stainless steel pipe 1 is reduced by performing the straightening process by the inclined roll type straightening machine 200 and the low temperature heat treatment is estimated as follows.
  • the duplex stainless steel pipe 1 In cold working, the duplex stainless steel pipe 1 is stretched in the axial direction while reducing the diameter. Therefore, cold working introduces tensile strain in the axial direction of the duplex stainless steel pipe 1 and introduces compressive strain in the circumferential direction. As shown in FIG. 4, attention is paid to an arbitrary crystal grain 10 in the duplex stainless steel pipe 1.
  • a tensile load FT is applied in the tube axis direction of the duplex stainless steel tube 1.
  • a plurality of dislocations 12 are generated in the slip system 11.
  • the dislocation 12 moves in the sliding system 11 in the direction X1 shown in FIG. 5 and is deposited near the grain boundary GB.
  • a repulsive force RF acts between the accumulated dislocations 12.
  • a compressive load FI is applied in the tube axis direction of the duplex stainless steel tube 1 as cold worked (As Cold Worked).
  • the dislocation 12 in addition to the applied stress sigma FI based on compressive load FI, by utilizing the repulsive force RF, of the slip system 11, it moves in the direction X2 opposite to the direction X1.
  • the dislocations 12 start to operate with a load stress ⁇ FI lower than the true yield stress ⁇ t.
  • the Bauschinger effect is generated by cold working, and the compressive yield strength YS LC in the tube axis direction is lowered.
  • Straightening by the inclined roll type straightening machine 200 suppresses the Bauschinger effect and increases the compressive yield strength YS LC of the duplex stainless steel pipe 1 in the tube axis direction. The reason is not clear, but is estimated as follows.
  • the duplex stainless steel pipe 1 In the straightening process by the inclined roll type straightening machine 200, the duplex stainless steel pipe 1 is sandwiched between the inclined rolls 22 and moves forward while rotating around the pipe axis. At this time, the duplex stainless steel pipe 1 receives the external force FO from the direction different from the cold working (mainly from the radial direction) by the inclined roll 22. Therefore, in the straightening process, as shown in FIG. 7, the dislocation 14 is generated in the slip system 13 different from the slip system 11 introduced by the cold work due to the external force FO and is activated.
  • the dislocation 14 introduced by the straightening process functions as a forest dislocation with respect to the dislocation 12. Further, the dislocation 12 and the dislocation 14 intersect and cut each other. As a result, dislocations 12 and 14 having a kink portion and a jog portion are generated. The kink part and the jog part are formed on a slip surface different from other dislocation parts. Therefore, the movement of the dislocation 12 and the dislocation 14 having the kink portion or the jog portion is limited. As a result, even when the compressive load FI is applied as shown in FIG. 6, the dislocation 12 is difficult to move, and the decrease in the compressive yield strength YS LC is suppressed.
  • the duplex stainless steel pipe 1 according to the present embodiment contains carbon (C) and nitrogen (N). These elements are smaller in size than elements such as Fe and Ni. Therefore, C and N are diffused in the steel by the low temperature heat treatment and are fixed in the vicinity of the dislocation core. C and N adhering to the vicinity of the dislocation core hinder the activities of the dislocations 12 and 14 due to the Cottrell effect.
  • FIG. 8 is a diagram showing the relationship between the heat treatment temperature (° C.) in the low-temperature heat treatment and the diffusion movement distances of C atoms and N atoms in the austenite phase when held at the heat treatment temperature for 10 minutes.
  • FIG. 9 is a diagram showing the relationship between the heat treatment temperature (° C.) in the low-temperature heat treatment and the diffusion movement distances of C atoms and N atoms in the ferrite phase when held at the heat treatment temperature for 10 minutes.
  • the mark “ ⁇ ” indicates the diffusion movement distance (nm) of C.
  • the mark “ ⁇ ” indicates the diffusion movement distance (nm) of N.
  • the diffusion transfer distance does not increase so much even if the heat treatment temperature increases until the heat treatment temperature reaches around 350 ° C.
  • the diffusion movement distance increases remarkably as the temperature rises thereafter. Specifically, if the heat treatment temperature of 350 ° C. or higher is maintained for 10 minutes or more, the diffusion movement distance of C atoms and N atoms in the austenite phase is 10 nm or more, and the diffusion movement distance of C atoms and N atoms in the ferrite phase is 10 ⁇ m. That's it.
  • the heat treatment temperature in the low-temperature heat treatment is set to 350 ° C. or higher and maintained at the heat treatment temperature for 10 minutes or more, the C and N atoms are sufficiently diffused and fixed to the dislocation core introduced into the steel by cold working. And since the Cottrell effect occurs due to the fixation of C and N atoms, and the movement of the dislocations 12 and 14 is hindered, the tensile yield strength and the compressive yield strength of the steel tend to increase, but the direction decreased by the Bauschinger effect Appears prominently.
  • the dislocation density of cold-worked steel is generally about 10 14 to 23 / m 2 . Therefore, if the diffusion movement distance of C atoms and N atoms is 10 nm or more wider than the average distance between dislocations 12 and 14, C atoms and N atoms can be fixed to the dislocation core.
  • the upper limit of the heat treatment temperature in the low temperature heat treatment is 450 ° C.
  • the low-temperature heat treatment suppresses the decrease in the tensile yield strength or the compressive yield strength due to the Bauschinger effect, and reduces the anisotropy of the yield strength in the pipe axis direction and the pipe circumferential direction of the duplex stainless steel pipe 1.
  • the dislocation 14 is generated in the slip system 13 different from the slip system 11 during the cold working by the straightening process, and the activity of the dislocation 12 is inhibited. Furthermore, C and N are fixed in the vicinity of the dislocation core by the low temperature heat treatment, and the activities of the dislocation 12 and the dislocation 14 are hindered. Based on the above knowledge, the duplex stainless steel pipe 1 of this embodiment was completed. Hereinafter, the duplex stainless steel pipe 1 of the present embodiment will be described in detail.
  • the duplex stainless steel pipe 1 is composed of a duplex structure of austenite and ferrite.
  • the duplex stainless steel pipe 1 has the following chemical composition.
  • “%” of the content of each element represents “mass%”.
  • C 0.008 to 0.03%
  • Carbon (C) stabilizes the austenite phase and increases the strength. Further, C forms carbides at the time of temperature rise in the heat treatment. Thereby, a fine structure is obtained.
  • the C content exceeds 0.03%, carbides are excessively precipitated due to the heat effect during heat treatment and welding, and the corrosion resistance and workability of the steel are reduced. Therefore, the C content is 0.03% or less.
  • the upper limit may be less than 0.03%, 0.02%, or 0.018%.
  • the lower limit may be 0.010% or 0.014%.
  • Si 0 to 1% Silicon (Si) deoxidizes steel. Further, Si forms an intermetallic compound at the time of temperature rise in the heat treatment. Thereby, a fine structure is obtained.
  • the Si content exceeds 1%, an intermetallic compound is excessively precipitated due to the heat effect during heat treatment or welding, and the corrosion resistance and workability of the steel are deteriorated. Therefore, the Si content is 1% or less.
  • the upper limit may be less than 1%, 0.8%, or 0.7%.
  • the lower limit is 0%.
  • Si may be contained for the formation of an intermetallic compound or for deoxidation, and the lower limit thereof may be 0.05%, 0.1%, or 0.2% as necessary.
  • Mn 0.1-2%
  • Manganese (Mn) deoxidizes steel in the same manner as Si. Further, Mn combines with S in the steel to form a sulfur, and fixes S. Therefore, the hot workability of steel is increased. If the Mn content is less than 0.1%, it is difficult to obtain the above effect. Therefore, the Mn content is 0.1% or more. On the other hand, when the Mn content exceeds 2%, the hot workability and corrosion resistance of the steel are lowered. Therefore, the Mn content is 2% or less.
  • the lower limit of the Mn content may be more than 0.1%, 0.2%, or 0.3%.
  • the upper limit of the Mn content may be less than 2%, 1.7%, or 1.5%.
  • Chromium (Cr) maintains the corrosion resistance of the steel and increases the strength. If the Cr content is less than 20%, the above effect is difficult to obtain. Therefore, the Cr content is 20% or more. On the other hand, if the Cr content exceeds 35%, a ⁇ phase is easily generated, and the corrosion resistance and toughness of the steel are reduced. Therefore, the Cr content is 35% or less.
  • the lower limit of the Cr content may be over 20%, 22%, or 23%. Further, the upper limit of the Cr content may be less than 35%, 30%, or 28%.
  • Ni 3-10% Nickel (Ni) stabilizes the austenite phase and forms a two-phase structure of ferrite and austenite.
  • Ni content 3-10%
  • Ni Nickel (Ni) stabilizes the austenite phase and forms a two-phase structure of ferrite and austenite.
  • Ni content 3-10%
  • Ni nickel
  • the Ni content is 3% or more.
  • Ni since Ni is expensive, when the Ni content exceeds 10%, the manufacturing cost increases. Therefore, the Ni content is 10% or less.
  • the lower limit of the Ni content may be more than 3%, 5%, or 6%.
  • the upper limit of the Ni content may be less than 10%, 9%, or 8%.
  • Mo 0-4% Molybdenum (Mo) increases the pitting corrosion resistance and crevice corrosion resistance of steel. Mo further increases the strength of the steel by solid solution strengthening. Therefore, Mo is contained as necessary. If Mo is contained even a little, the above effect can be obtained to some extent. However, if the Mo content exceeds 4%, the ⁇ phase tends to precipitate, and the toughness of the steel decreases. Therefore, the Mo content is 4% or less. When the above effect is further required, the upper limit may be less than 4%, 3.8%, or 3.5%. There is no need to define the lower limit of Mo, and the lower limit is 0%. In order to obtain the above effect remarkably, Mo may be contained, and the lower limit may be set to 0.5%, more than 0.5%, 2%, or 3% as necessary.
  • W 0-6% Tungsten (W), like Mo, increases the pitting corrosion resistance and crevice corrosion resistance of steel. W further increases the strength of the steel by solid solution strengthening. Therefore, W is contained as necessary. If W is contained even a little, the above effect can be obtained to some extent. However, if the W content exceeds 6%, the ⁇ phase tends to precipitate, and the toughness of the steel decreases. Therefore, the W content is 6% or less. When the above effect is further required, the upper limit may be less than 6%, 5%, or 4%. There is no need to specify the lower limit of W, and the lower limit is 0%. In order to obtain the above effect remarkably, W may be contained, and the lower limit may be set to 0.5%, more than 0.5%, 1% or 2% as necessary.
  • duplex stainless steel of this embodiment does not need to contain both Mo and W, and may contain at least one or more of Mo and W.
  • Cu 0 to 3% Copper (Cu) increases the corrosion resistance and intergranular corrosion resistance of steel. Therefore, Cu is contained as necessary. If Cu is contained even a little, the above effect can be obtained to some extent. However, when the Cu content exceeds 3%, the effect is saturated, and further, the hot workability and toughness of the steel are reduced. Therefore, the Cu content is 3% or less. When the above effect is further required, the upper limit may be less than 3%, 2%, or 1%. There is no need to define the lower limit of Cu, and the lower limit is 0%. In order to obtain the above effect remarkably, Cu may be contained, and the lower limit may be set to 0.1%, more than 0.1%, or 0.3% as necessary.
  • N 0.15-0.35%
  • Nitrogen (N) increases the stability of austenite and increases the strength of the steel. N further enhances the pitting corrosion resistance and crevice corrosion resistance of the duplex stainless steel. If the N content is less than 0.15%, the above effect is difficult to obtain. Therefore, the N content is 0.15% or more. On the other hand, if the N content exceeds 0.35%, the toughness and hot workability of the steel deteriorate. Therefore, the N content is 0.35% or less.
  • the lower limit of the N content may be more than 0.15%, more than 0.17%, or 0.20%. Further, the upper limit of the N content may be less than 0.35%, 0.33%, or 0.30%.
  • the balance of the duplex stainless steel pipe 1 of this embodiment is iron and impurities.
  • Impurities are ores and scraps used as a raw material for stainless steel, or elements mixed in from the environment of the manufacturing process.
  • the contents of P, S and O are limited as follows.
  • P 0.04% or less Phosphorus (P) is an impurity that is inevitably mixed during refining of steel, and is an element that lowers the hot workability, corrosion resistance, and toughness of steel. Therefore, the P content is 0.04% or less, preferably less than 0.04%, 0.034% or less, or 0.030% or less.
  • S 0.03% or less Sulfur (S) is an impurity inevitably mixed during refining of steel, and is an element that lowers the hot workability of steel. S further forms sulfides. Since sulfide is a starting point of pitting corrosion, it reduces the pitting corrosion resistance of steel. Therefore, the S content is 0.03% or less, preferably less than 0.003%, 0.001% or less, or 0.0007% or less.
  • Oxygen (O) is an impurity that is inevitably mixed during the refining of steel, and is an element that reduces the hot workability of steel. Therefore, the O content is 0.010% or less, preferably less than 0.010%, 0.009% or less, or 0.008% or less.
  • molten metal is manufactured by melting duplex stainless steel.
  • an electric furnace an Ar—O 2 mixed gas bottom blowing decarburization furnace (AOD furnace), a vacuum decarburization furnace (VOD furnace), or the like can be used.
  • AOD furnace Ar—O 2 mixed gas bottom blowing decarburization furnace
  • VOD furnace vacuum decarburization furnace
  • Cast material is manufactured using molten metal.
  • the cast material is, for example, an ingot, a slab, or a bloom. Specifically, an ingot is manufactured by an ingot-making method. Or a slab and a bloom are manufactured by a continuous casting method.
  • ⁇ Cast billets are hot processed to produce round billets. Hot working is, for example, hot rolling or hot forging.
  • the manufactured round billet is hot-worked to manufacture the raw tube 30.
  • the raw tube 30 is manufactured from a round billet by an extrusion pipe manufacturing method typified by the Eugene Sejurune method.
  • the raw tube 30 is manufactured from the round billet by the Mannesmann tube manufacturing method.
  • Cold working includes cold drawing and cold rolling represented by pilger rolling. In the present embodiment, either cold drawing or cold rolling may be employed.
  • Cold drawing gives a large tensile strain to the duplex stainless steel tube 1 in the tube axis direction as compared with cold rolling.
  • Cold rolling gives large strain not only in the tube axis direction of the raw tube 30 but also in the tube circumferential direction. Therefore, cold rolling gives a large compressive strain in the tube circumferential direction of the raw tube 30 as compared with cold drawing.
  • a preferable cross-sectional reduction rate during cold working is 5.0% or more.
  • the cross-sectional reduction rate is defined by Equation 6.
  • Cross-sectional reduction rate (cross-sectional area of the raw pipe 30 before cold working ⁇ cross-sectional area of the raw pipe 30 after cold working) / cross-sectional area of the raw pipe 30 before cold working ⁇ 100 (6)
  • the tensile yield strength YS LT is 689.1 to 1000.5 MPa.
  • a preferable lower limit of the cross-section reduction rate is 7.0%. If the cross-section reduction rate is too high, the roundness of the duplex stainless steel pipe 1 is lowered. Therefore, the upper limit of the preferable cross-section reduction rate of cold drawing is 20.0%, and the upper limit of the preferable cross-section reduction rate of cold rolling is 40.0%.
  • Other processing may be performed between hot processing and cold processing.
  • a solution heat treatment is performed on the hot-worked raw tube 30.
  • Descaling is performed on the raw tube 30 after the solution heat treatment to remove the scale.
  • Cold working is performed on the unscaled element tube 30.
  • cold working may be performed a plurality of times.
  • a solution heat treatment may be performed as a softening heat treatment between the cold working and the next cold working.
  • the subsequent steps are performed on the raw tube 30 after the final cold working.
  • the straight tube 30 after cold working is subjected to straightening and low-temperature heat treatment by an inclined roll type straightening machine 200.
  • Either straightening or low-temperature heat treatment may be performed first. That is, straightening may be performed after cold working, and then low-temperature heat treatment may be performed. Low temperature heat treatment may be performed after cold working, and then straightening may be performed. Further, the straightening process may be performed a plurality of times, or the low-temperature heat treatment may be performed a plurality of times. For example, cold working, first straightening, low-temperature heat treatment, and second straightening may be performed in this order. Cold processing, first low-temperature heat treatment, straightening processing, and second low-temperature heat treatment may be performed in this order. Details of the straightening process and the low-temperature heat treatment will be described below.
  • FIG. 10 is a schematic diagram of the straightening machine 200.
  • the straightening machine 200 used in the present embodiment is an inclined roll type.
  • the straightening machine 200 shown in FIG. 10 has a plurality of stands ST1 to ST4.
  • a plurality of stands ST1 to ST4 are arranged in a line.
  • Each of the stands ST1 to ST4 includes a pair or one inclined roll 22. Specifically, the last stand ST4 is provided with one inclined roll 22, and the other stands ST1 to ST3 are provided with a pair of inclined rolls 22 arranged vertically.
  • Each inclined roll 22 includes a roll shaft 221 and a roll surface 222.
  • Roll axis 221 is inclined obliquely with respect to pass line PL.
  • the roll shafts 221 of the pair of inclined rolls 22 of the stands ST1 to ST3 intersect each other. Since the roll shafts 221 of the inclined rolls 22 disposed above and below are inclined with respect to the pass line PL and intersect each other, the tube 30 can be rotated in the pipe circumferential direction.
  • the roll surface 222 is concave.
  • the center P0 of the gap between the inclined rolls 22 of the stand ST2 is arranged so as to be shifted from the pass line PL. Therefore, the stand ST1 and the stand ST2 bend the raw tube 30, and the stand ST2 and the stand ST3 bend the raw tube 30 back. Thereby, the straightening machine 200 corrects the bending of the raw tube 30.
  • FIG. 11 is a front view of the inclined roll 22 and the raw tube 30 in a stand STi having a pair of inclined rolls 22.
  • the base tube 30 is crushed by the pair of inclined rolls 22.
  • RC (DA-DB) / DA ⁇ 100 (8)
  • Each stand STi compresses the raw pipe 30 rotating in the circumferential direction with a crush amount AC set for each stand, and gives distortion to the raw pipe 30.
  • the dislocation 14 generated in the raw tube 30 due to the reduction acts in a slip system 13 different from the dislocation 12 generated during cold working. Therefore, the dislocations 14 generated by the straightening process collide with the dislocations 12 generated during the cold working and cut each other. As a result, the dislocations 12 and 14 are difficult to move. Therefore, the straightening process prevents the compressive stress intensity YS LC in the tube axis direction from being reduced by the Bauschinger effect.
  • the rolling by the inclined roll 22 is effective.
  • the maximum crash rate RC among the crash rates RC of each stand STi is defined as the maximum crash rate.
  • the reduction by the maximum crash rate can give the largest strain to the raw tube 30. Therefore, it is estimated that the maximum crash rate is effective in reducing the anisotropy of the yield strength in the tube axis direction.
  • a preferred maximum crash rate is 2.0 to 15.0%.
  • a more preferable lower limit of the maximum crash rate is 4.0%, and a more preferable upper limit of the maximum crash rate is 12.0%.
  • the straightening machine 200 includes seven inclined rolls 22, and includes four stands ST1 to ST4.
  • the number of inclined rolls 22 is not limited to seven, and the number of stands is not limited to four.
  • the number of inclined rolls 22 may be ten, or may be other than that.
  • the last stand is provided with one inclined roll 22, and the other stands are provided with a pair of inclined rolls 22.
  • each stand includes a pair of inclined rolls 22.
  • the raw tube 30 is charged into a heat treatment furnace. Then, the raw tube 30 is soaked at a heat treatment temperature of 350 to 450 ° C. By soaking in the above-described temperature range, C and N in the raw tube 30 diffuse and are easily fixed in the vicinity of the dislocation core. As a result, the dislocation 12 and the dislocation 14 become difficult to move, and the anisotropy of the yield strength in the tube axis direction and the tube circumferential direction is reduced.
  • the preferable soaking time is 5 minutes or more. In this case, C and N in the duplex stainless steel are sufficiently diffused. The upper limit of preferable soaking time is 60 minutes. In addition, since the heat treatment temperature of the low-temperature heat treatment is low, the raw tube 30 after the heat treatment is unlikely to be bent.
  • the duplex stainless steel pipe 1 satisfying the formulas 1 to 4 is manufactured.
  • the order of straightening and low-temperature heat treatment is not particularly limited. However, preferably, straightening is performed after cold working, and low-temperature heat treatment is performed after straightening. In this case, C and N stick to not only the dislocations 12 generated by the cold working but also the dislocations 14 generated by the straightening process, and the Cottrell effect is obtained. Therefore, the anisotropy of the yield strength in the tube axis direction and the tube circumferential direction is likely to be further reduced.
  • a plurality of duplex stainless steel pipes 1 were manufactured under different manufacturing conditions. The anisotropy of the yield strength of the manufactured duplex stainless steel pipe 1 was investigated.
  • Ingots were manufactured by melting steel A and steel B having the chemical composition shown in Table 1.
  • Steel A and steel B were both within the range of the preferred chemical composition of this embodiment.
  • P content of steel A and steel B was 0.04% or less
  • S content was 0.03% or less
  • O content was 0.010% or less.
  • the produced ingot was hot-extruded to produce a plurality of cold-working blanks 30.
  • the manufacturing process shown in Table 2 was performed on the cold-working blank 30 to produce the duplex stainless steel pipes 1 to 16.
  • the type of billet used (steel A and steel B) is described in the steel column.
  • the outer diameter (60.0 mm and 178.0 mm) of the manufactured duplex stainless steel pipe 1 is described.
  • AsP / D means as cold drawn.
  • P / D means cold drawing.
  • CR means cold rolling.
  • STR means straightening.
  • the heat treatment means a low temperature heat treatment.
  • the cross-section reduction rate of cold drawing was 8%, and the cross-section reduction rate of cold rolling was 16%.
  • the cross-sectional reduction rate (%) was obtained by the above-described six equations.
  • the heat treatment temperature (° C.) of the low temperature heat treatment performed during the manufacturing process is described.
  • the number of inclined rolls of the straightening machine 200 used for straightening is described.
  • the maximum crash rate (%) at the time of straightening is described.
  • a duplex stainless steel pipe 1 was manufactured by performing only cold drawing on the base pipe 30 of the mark 1. That is, the duplex stainless steel pipe 1 of the mark 1 was an as-cold drawn (As Cold Drawn) material. In the mark 2, the duplex stainless steel pipe 1 was manufactured by performing only cold rolling on the raw pipe 30.
  • straightening processing was performed twice on the raw tube 30. Specifically, after the cold drawing was performed on the raw tube 30, the first straightening process (first STR) was performed. The maximum crash rate during the first straightening process was 4.0%. After the first straightening process, low-temperature heat treatment was performed. A second straightening process (second STR) was performed on the element tube 30 after the heat treatment. The maximum crash rate during the second straightening process was 6.0%.
  • Compressive specimens and tensile specimens were collected from the manufactured duplex stainless steel pipe 1 of each mark. Specifically, a tensile test piece and a compression test piece extending in the tube axis direction of each mark were collected, and a tensile test piece and a compression test piece extending in the tube circumferential direction of each mark were collected.
  • test specimens conformed to ASTM (American Society for Testing and Materials) -E8 and ASTM-E9. Both the outer diameter of the compression test piece and the standard test piece of the compression test piece was 6.35 mm, and the distance between the gauge points was 12.7 mm. For each mark, if a standard specimen could not be collected, a proportional specimen was collected.
  • a compression test and a tensile test were performed in a normal temperature (25 ° C.) atmosphere to obtain a compression yield strength and a tensile yield strength.
  • the tensile yield strength YS LT (MPa) in the tube axis direction was obtained using a tensile test piece extending in the tube axis direction.
  • the tensile yield strength YS CT (MPa) in the pipe circumferential direction was obtained using a tensile test piece extending in the pipe circumferential direction.
  • a compressive yield strength YS LC (MPa) in the tube axis direction was obtained using a compression test piece extending in the tube axis direction.
  • the compression yield strength YS CC (MPa) in the pipe circumferential direction was obtained using a compression test piece extending in the pipe circumferential direction. Each yield strength was defined as a 0.2% yield strength in a tensile test and a compression test. Table 2 shows the obtained yield strengths (YS LT , YS CT , YS LC and YS CC ).
  • F1 to F4 shown in the following formulas 1 to 4 were obtained for each mark.
  • F1 YS LC / YS LT (1)
  • F2 YS CC / YS CT (2)
  • F3 YS CC / YS LT (3)
  • F4 YS CT / YS LT (4)
  • the obtained F1 to F4 are shown in Table 2.
  • the duplex stainless steel pipe 1 marked 1 to 5 at least one of F1 to F4 did not satisfy the formulas 1 to 4. Specifically, the F1 value of the mark 1 was less than 0.90.
  • the blank tube 30 of the mark 1 was extended in the axial direction by cold drawing. Accordingly, it is presumed that the compressive yield strength YS LC in the tube axis direction is excessively smaller than the tensile yield strength YS LT in the tube axis direction due to the Bauschinger effect.
  • the F1 value and F4 value of Mark 2 were less than 0.90, and the F2 value exceeded 1.11.
  • the cold tube 30 of the mark 2 was only cold rolled.
  • the raw tube 30 during the cold rolling is subjected to tensile deformation in the axial direction and compression deformation in the circumferential direction.
  • the compressive deformation in the circumferential direction of the raw tube 30 in cold rolling is larger than that in the case of cold drawing.
  • the compressive yield strength YS LC in the tube axis direction becomes excessively smaller than the tensile yield strength YS LT
  • the tensile yield strength YS CT in the tube circumferential direction is excessive than the compressive yield strength YS CC. It became small. Therefore, it is estimated that Formula 1, Formula 2, and Formula 4 were not satisfied.
  • the F2 value and the F4 value did not satisfy the formulas 2 and 4.
  • the compressive yield strength YS LC in the tube axis direction was improved.
  • the anisotropy of the tensile yield strength and the compressive yield strength in the pipe circumferential direction was not improved, and as a result, it is estimated that Formulas 2 and 4 were not satisfied.
  • the duplex stainless steel pipe according to the present invention has a small anisotropy in yield strength, it can be used even when a different stress distribution is applied depending on the use environment. Therefore, it can be widely used as an oil well pipe. In particular, it can be used for tubing and casings.

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US14/402,882 US10184160B2 (en) 2012-08-31 2013-08-22 Dual phase stainless steel pipe and manufacturing method thereof
JP2013542276A JP5500324B1 (ja) 2012-08-31 2013-08-22 二相ステンレス鋼管及びその製造方法
ES13833720.9T ES2623731T3 (es) 2012-08-31 2013-08-22 Tubo de acero inoxidable dúplex y método de fabricación del mismo
AU2013310286A AU2013310286B2 (en) 2012-08-31 2013-08-22 Dual phase stainless steel pipe and manufacturing method thereof
CN201380034033.1A CN104395491A (zh) 2012-08-31 2013-08-22 双相不锈钢管及其制造方法
IN9674DEN2014 IN2014DN09674A (GUID-C5D7CC26-194C-43D0-91A1-9AE8C70A9BFF.html) 2012-08-31 2013-08-22
EP13833720.9A EP2853614B1 (en) 2012-08-31 2013-08-22 Duplex stainless steel tube and method for producing same
BR112014032621-5A BR112014032621B1 (pt) 2012-08-31 2013-08-22 tubo de aço inoxidável duplex e seu método de produção

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WO2021157251A1 (ja) * 2020-02-05 2021-08-12 Ｊｆｅスチール株式会社 ステンレス継目無鋼管およびその製造方法
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IN2014DN09674A (GUID-C5D7CC26-194C-43D0-91A1-9AE8C70A9BFF.html) 2015-07-31
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AU2013310286A1 (en) 2014-12-04
ES2623731T3 (es) 2017-07-12
JP5500324B1 (ja) 2014-05-21
EP2853614A4 (en) 2016-03-30
BR112014032621B1 (pt) 2021-02-17
CN108842047A (zh) 2018-11-20
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