WO2014091756A1 - 継目無鋼管の熱処理設備列および高強度ステンレス鋼管の製造方法 - Google Patents
継目無鋼管の熱処理設備列および高強度ステンレス鋼管の製造方法 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
- 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
- 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
- C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
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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
- C21D9/0062—Heat-treating apparatus with a cooling or quenching zone
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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
- 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
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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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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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
- C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
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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
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium 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
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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
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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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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- 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
Definitions
- the present invention provides a high strength stainless steel tube (high strength stainless steel tube) for imparting stable product quality to a high Cr-based seamless steel pipe (quenching and tempering treatment).
- the present invention relates to a method for manufacturing orpipe) and a heat treatment equipment line for high-strength stainless steel pipes.
- heat treatment of steel pipe includes heat treatment such as quenching, tempering, annealing, solution treatment (solution heat treatment) and the like. These heat treatments are selectively performed according to purposes such as required performance (required performance) from customers and product quality (homogenization).
- Patent Document 1 discloses a heat treatment facility in which a quenching heating furnace (heating for quenching), a quenching device (equipment for quenching), and a tempering heating furnace (tempering furnace) are effectively arranged for the purpose of efficiency and compactness.
- a column is proposed.
- the martensite transformation temperature (Mf point) is around room temperature (about room temperature) or below room temperature (25 °C).
- the cooling stop temperature after quenching (cooling ⁇ ⁇ stop temperature) is constant due to room temperature changes and restrictions on the process of continuous operation.
- the volume fraction of residual austenite before tempering fluctuates. For this reason, there has been a problem that the mechanical properties such as strength and toughness after heat treatment become unstable and the mechanical properties vary from product to product.
- the present invention solves the above-mentioned problems and provides a series of heat treatment equipment for seamless steel pipes and a method for producing high-strength stainless steel pipes, in which product quality after heat treatment is stably obtained. It is.
- the high-strength stainless steel pipe is, by mass, C: 0.005 to 0.05%, Si: 0.05 to 1.0%, Mn: 0.2 to 1.8%, P: 0 0.03% or less, S: 0.005% or less, Cr: 14 to 20%, Ni: 1.5 to 10%, Mo: 1 to 5%, N: 0.15% or less, O: 0.006%
- the high-strength stainless steel pipe has the following composition, the balance being Fe and inevitable impurities.
- the high-strength stainless steel pipe is reheated to 850 to 1000 ° C. in the quenching furnace and then air-cooled in the quenching equipment. ) Cooling to 50 ° C. or less at the above cooling rate, followed by cooling to 20 ° C. or less with the low-temperature cooling equipment, and then heating to a temperature of 450 to 700 ° C. in the tempering furnace (1 The manufacturing method of the high intensity
- An on-line heat treatment equipment row of seamless steel pipes in which a quenching heating furnace, a quenching equipment, and a tempering heating furnace are arranged in the lower process of the rolling line, and interposed between the quenching equipment and the tempering heating furnace.
- a heat treatment equipment row for manufacturing the high-strength stainless steel pipe characterized in that a low-temperature cooling equipment capable of cooling the heat-treated steel pipe to 20 ° C. or lower is disposed at one end or a part of the heat treatment conveyance line.
- the low-temperature cooling facility is a facility capable of cooling the heat-treated steel pipe to a temperature of 10 ° C. or lower, and cools the heat-treated steel pipe to a temperature of 10 ° C. or lower before tempering.
- the quenching and cooling stop temperature is constant at 20 ° C. or less, preferably 10 ° C. or less. For this reason, even when producing a high-strength stainless steel pipe containing 14% or more of Cr and containing alloy elements such as Ni and Mo, the volume fraction of retained austenite before tempering treatment is constant, and stable product quality is achieved. can get.
- a steel pipe is heated and maintained at a predetermined temperature in a quenching heating furnace, then cooled by water quenching, air blast cooling, air cooling, etc., and then at a predetermined temperature. Heat, hold and temper.
- the cooling stop temperature after quenching is, for example, 100 ° C. or lower, room temperature, or the like as described in Patent Document 2.
- the martensite transformation end temperature (Mf point) may be 20 ° C. or less, and the volume fraction of retained austenite varies depending on the cooling stop temperature, and tempering. Later product quality was the cause of variation.
- the present inventors examined a facility for making the cooling stop temperature constant at room temperature or lower.
- the steel pipe to be heat-treated is always kept at a constant temperature (20 ° C. or less, preferably 10 ° C. or less) using water as a cooling medium between the quenching equipment 2 and the tempering furnace 5.
- the heat treatment equipment row in which the low-temperature cooling equipment 4 capable of cooling is arranged has been invented.
- the low-temperature cooling equipment 4 provided at the downstream end of the heat treatment conveyance line 3 may be provided in the middle of the heat treatment conveyance line (heat treatment carrier line) 3 or upstream of the heat treatment conveyance line 3. It may be provided at the side end.
- the water used as the refrigerant circulates between the low-temperature cooling facility 4 and a refrigerant cooling device (not shown) while its temperature is continuously measured.
- the circulating water is always maintained at a constant temperature by being cooled by the refrigerant cooling device.
- “always constant” means that the temperature of the refrigerant when entering the low-temperature cooling facility 4 from the refrigerant cooling device is always constant.
- Constant means a range of desired temperature ⁇ 3.0 ° C.
- % representing the content of a component means “% by mass”.
- C 0.005 to 0.05%
- the C content is preferably 0.005% or more. If the amount of C exceeds 0.05%, the amount of Cr carbide produced becomes excessive, and the amount of solid solution Cr that effectively acts on corrosion resistance may decrease. In order to prevent this, in the present invention, it is preferable to limit the C content to a range of 0.005 to 0.05%. Further, from the viewpoint of corrosion resistance, it is preferable that the amount of C is as small as possible. Further, from the viewpoint of ensuring strength, it is preferable that the amount of C is large. Considering these balances, the more preferable amount of C is 0.005 to 0.03%.
- Si 0.05 to 1.0%
- Si is an element that acts as a deoxidizing agent.
- the Si amount is preferably 0.05% or more.
- the Si content is preferably limited to a range of 0.05 to 1.0%.
- a more preferable Si amount is 0.10 to 0.3%.
- Mn 0.2 to 1.8%
- Mn is an element that increases the strength.
- the Mn content is preferably 0.2% or more. If the amount of Mn exceeds 1.8%, the toughness may be adversely affected. For this reason, the amount of Mn is preferably limited to 0.2 to 1.8%. A more preferable amount of Mn is 0.2 to 0.8%.
- P 0.03% or less
- P is an element that degrades both corrosion resistance and sulfide stress corrosion cracking resistance. In the present invention, it is preferable to reduce the amount of P as much as possible. However, an extreme reduction in the amount of P causes an increase in manufacturing cost.
- the amount of P is preferably 0.03% or less from the viewpoint that it can be industrially implemented at a relatively low cost and does not deteriorate both corrosion resistance and sulfide stress corrosion cracking resistance. A more preferable amount of P is 0.02% or less.
- S 0.005% or less S is an element that significantly deteriorates hot workability in a pipe manufacturing process. It is preferable to reduce the amount of S as much as possible. If the amount of S is reduced to 0.005% or less, steel pipes can be manufactured by a normal process. Therefore, the amount of S is preferably limited to 0.005% or less. A more preferable amount of S is 0.002% or less.
- Cr 14-20% Cr is an element that improves the corrosion resistance by forming a protective surface film on the surface of the steel pipe, and in particular, is an element that contributes to the improvement of the CO 2 corrosion resistance and sulfide stress corrosion cracking resistance.
- the Cr content is preferably 14% or more. When the Cr content exceeds 20%, the volume fraction of austenite and ferrite becomes excessive, and the desired high strength cannot be maintained, and the toughness and hot workability also deteriorate. A more preferable Cr content is 15 to 18%.
- Ni 1.5-10%
- Ni has the effect of strengthening the protective coating and enhancing the resistance to CO 2 corrosion, pitting corrosion resistance and resistance to sulfide stress corrosion cracking. Furthermore, Ni is an element that increases the strength of steel by solid solution strengthening. Such an effect is recognized by containing 1.5% or more of Ni. However, if the amount of Ni exceeds 10%, desired high strength cannot be obtained, and hot workability may be deteriorated. A more preferable amount of Ni is 3 to 8%.
- Mo 1-5% Mo is, Cl - is an element that increases resistance to by pitting.
- Mo amount it is preferable to make Mo amount into 1% or more. If the amount of Mo exceeds 5%, austenite and ferrite become excessive, the desired high strength cannot be maintained, and toughness and hot workability may be deteriorated. On the other hand, if the Mo amount exceeds 5%, intermetallics may precipitate, and the toughness and resistance to sulfide stress corrosion cracking may be deteriorated.
- a more preferable amount of Mo is 2 to 4%.
- N 0.15% or less N is an element that remarkably improves pitting corrosion resistance.
- the amount of N exceeds 0.15%, various nitrides are formed, and the toughness may deteriorate due to the formation of the nitrides.
- the N content is preferably 0.15% or less.
- a more preferable N amount is 0.1% or less.
- O 0.006% or less
- O exists as an oxide in steel and adversely affects various properties. In order to improve the characteristics, it is preferable to reduce the amount of O as much as possible. In particular, when the amount of O exceeds 0.006%, hot workability, corrosion resistance, sulfide stress corrosion cracking resistance, and toughness are significantly reduced. Therefore, in the present invention, it is preferable to limit the amount of O to 0.006% or less.
- Al 0.002 to 0.05%, Cu: 3.5% or less, Nb: 0.5% or less, V: 0.5% or less, Ti: 1 selected from 0.3% or less, Zr: 0.2% or less, W: 3% or less, B: 0.01% or less, Ca: 0.01% or less, REM: 0.1% or less More than seeds can be contained.
- Al is an element having a strong deoxidizing action.
- the Al content is preferably 0.002% or more. If the Al content exceeds 0.05%, the toughness may be adversely affected. For this reason, when Al is contained, the Al content is preferably limited to a range of 0.002 to 0.05%. A more preferable amount of Al is 0.03% or less.
- Al may be included as an inevitable impurity in an amount of less than 0.002%. If the amount of Al is limited to less than about 0.002%, there is an advantage that the low temperature toughness is remarkably improved.
- Cu is an element that strengthens the protective coating, suppresses the penetration of hydrogen into the steel, and improves the resistance to sulfide stress corrosion cracking. The effect becomes remarkable when the amount of Cu is 0.5% or more. On the other hand, if the amount of Cu exceeds 3.5%, CuS grain boundary precipitation is caused and hot workability is lowered. For this reason, it is preferable to limit the amount of Cu to 3.5% or less. A more preferable amount of Cu is 1.0 to 3.0%.
- Nb, V, Ti, Zr, W, and B are all elements that increase the strength, and are used as necessary.
- V, Ti, Zr, W, and B are also elements that improve stress-corrosion-cracking-resistance.
- Such effects include Nb amount of 0.03% or more, V amount of 0.02% or more, Ti amount of 0.03% or more, Zr amount of 0.03% or more, W amount of 0.2% or more, or It becomes remarkable when the amount of B is 0.0005% or more.
- the Nb amount exceeds 0.5%
- the V amount exceeds 0.5%
- the Ti amount exceeds 0.3%
- the Zr amount exceeds 0.2%
- the W amount exceeds 3%
- or the B amount is 0.00.
- the Nb amount is 0.5% or less
- the V amount is 0.5% or less
- the Ti amount is 0.3% or less
- the Zr amount is 0.2% or less
- the W amount is 3% or less
- the B amount is 0. It is preferable to limit it to 0.01% or less.
- Ca has the action of fixing S as CaS and spheroidizing sulfide inclusions. This action reduces the lattice strain of the matrix surrounding the inclusions and reduces the hydrogen trapping ability of the inclusions. Such an effect becomes remarkable when the Ca content is 0.0005% or more. Moreover, when Ca content exceeds 0.01%, the increase in CaO will be caused and corrosion resistance will fall. For this reason, it is preferable to limit Ca amount to a range of 0.01% or less.
- REM improves the stress corrosion cracking resistance in the environment of high temperature aqueous chloride solution. Such an effect becomes remarkable when the amount of REM is 0.001% or more. On the other hand, even if REM is excessively contained, the effect is saturated. Therefore, the upper limit of the REM amount is preferably 0.1%. A more preferable amount of REM is 0.001 to 0.01%.
- REM as used in the field of this invention is lanthanoid from yttrium (Y) of atomic number 39 and lanthanum (La) of atomic number 57 to lutetium (Lu) of 71.
- the stainless steel according to the present invention preferably contains one or more of the above-mentioned REMs.
- the amount of REM is the total content of one or more selected from the plurality of REMs described above.
- the balance other than the above components is Fe and inevitable impurities.
- molten steel having the above composition is melted by a generally known melting method such as a converter, an electric furnace (electric furnace), a vacuum melting furnace (vacuum melting furnace), and continuously cast. It is preferable to use a steel pipe material such as billet by a generally known method such as a continuous casting method or a slab-milling method. These steel pipe materials are then heated and hot rolled using the normal Mannesmann-plug mill method or Mannesmann-mandrel mill method. Pipes are made into seamless steel pipes of the desired dimensions. After the pipe making, the seamless steel pipe is preferably cooled to room temperature at a cooling rate equal to or higher than air cooling. Note that the seamless steel pipe may be manufactured by hot extrusion by a press method. In addition, the said hot rolling and hot extrusion correspond to the process in the rolling line of FIG.
- the seamless steel pipe is reheated to 850 to 1100 ° C. Then, it cools to 50 degrees C or less with the quenching equipment 2 with the cooling rate more than air cooling. Subsequently, in the heat treatment equipment row shown in FIG. 1, the seamless steel pipe cooled by the quenching equipment 2 passes through the heat treatment conveyance line 3 (the temperature of the seamless steel pipe exceeds 50 ° C. due to cooling by the quenching equipment 2. As long as it can be cooled to 50 ° C. or less by passing through the heat treatment conveyance line 3). Subsequently, the seamless steel pipe is cooled to 20 ° C.
- the low-temperature cooling equipment 4 provided at the downstream end of the heat treatment conveyance line 3.
- the seamless steel pipe cooled by the low-temperature cooling equipment 4 is tempered in a tempering heating furnace 5, and the tempered seamless steel pipe is further sent to a downstream conveying line.
- the position where the low-temperature cooling equipment 4 is provided may be one end or a part of the heat treatment transfer line 3 interposed between the quenching equipment 2 and the tempering heating furnace 5.
- the steel structure of the seamless steel pipe can be made into a fine and high toughness martensite structure.
- the steel structure may also contain suitable amounts of other phases, such as ferrite phase and residual austenite phase.
- the total content of other phases is preferably 20 vol% or less.
- a martensite + ferrite structure may be used. In that case, the retained austenite is preferably 10 vol% or less.
- the quenching heating temperature in the quenching heating furnace 1 is less than 850 ° C., sufficient martensite portion does not enter and the strength tends to decrease. On the other hand, if the quenching heating temperature exceeds 1100 ° C., the structure becomes coarse and the toughness decreases. For this reason, the heating temperature in the quenching heating furnace 1 is preferably 850 to 1100 ° C.
- the cooling stop temperature after quenching (temperature of the seamless steel pipe cooled by the low-temperature cooling equipment 4) is room temperature, the volume fraction of retained austenite may fluctuate due to the change in room temperature, which causes variations in mechanical properties It becomes. For this reason, it is preferable that the said cooling stop temperature is 20 degrees C or less. More preferably, it is 10 degrees C or less.
- the cooling stop temperature can always be kept constant at room temperature or lower. For this reason, the dispersion
- the seamless steel pipe that has been subjected to quenching treatment is preferably subjected to a tempering treatment in a tempering heating furnace 5 that is heated to a temperature of 450 to 700 ° C. and cooled at a cooling rate equal to or higher than air cooling.
- the steel structure is a structure composed of a tempered martensite phase, or a structure composed of a tempered martensite phase, a small amount of ferrite phase and a small amount of retained austenite phase, or a tempered martensite.
- the structure consists of a phase, a ferrite phase, and a small amount of retained austenite phase.
- a steel pipe material having the composition shown in Table 1 was piped by hot working, and air-cooled after the pipe making to obtain a seamless steel pipe having an outer diameter of 83.8 mm and a wall thickness of 12.7 mm.
- the obtained seamless steel pipes were each heated to the temperatures shown in Table 2 and then cooled to room temperature by air cooling or water cooling (conventional example, comparative example), and after the quenching treatment, using the low-temperature cooling equipment of the present invention, 10 And a process of cooling to ° C. (examples of the present invention).
- the temperature of the seamless steel pipe before entering the low-temperature cooling facility was as shown in Table 2 (quenching cooling stop temperature in Table 2). Thereafter, tempering treatment was performed at the temperatures shown in Table 2, respectively.
- Test pieces were taken from each steel pipe after tempering, and the retained austenite fraction and tensile properties were investigated. The results are shown in Table 2.
- the retained austenite fraction was converted from the diffracted X-ray integrated intensity measured using the X-ray diffraction method.
- variation the same evaluation was performed using ten samples of each steel pipe No. The variation was determined as the difference between the maximum YS and the minimum YS.
- the inventive example has a smaller variation in yield strength than the comparative example, and the problem of variation in yield strength is remarkably improved.
- the Ms point is 345 ° C., which is significantly higher than room temperature. For this reason, when steel A was used, there was little variation in tensile properties even with the conventional heat treatment method.
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Abstract
Description
Cは、マルテンサイト系ステンレス鋼の耐食性、強度に関係する重要な元素である。本発明ではC量を0.005%以上にすることが好ましい。C量が0.05%を超えると、Cr炭化物の生成量が過大となり、耐食性に有効に作用する固溶Cr量が減少する場合がある。これを防止する目的から、本発明では、C量を0.005~0.05%の範囲に限定することが好ましい。また、耐食性の観点からはC量はできるだけ少ないほうが好ましい。また、強度を確保する観点からはC量が多いほうが好ましい。これらのバランスを考えて、より好ましいC量は0.005~0.03%である。
Siは、脱酸剤(deoxidizing agent)として作用する元素である。本発明ではSi量を0.05%以上にすることが好ましい。また、Si量が1.0%を超えると、耐CO2腐食性が低下し、さらには熱間加工性(hot workability)も低下する場合がある。このため、Si量は0.05~1.0%の範囲に限定することが好ましい。なお、より好ましいSi量は0.10~0.3%である。
Mnは、強度を増加させる元素である。本発明における所望の強度を確保するためにMn量を0.2%以上含有することが好ましい。Mn量が1.8%を超えると靭性に悪影響を及ぼす場合がある。このため、Mn量は0.2~1.8%に限定することが好ましい。なお、より好ましいMn量は0.2~0.8%である。
Pは、耐食性(corrosion resistance)および耐硫化物応力腐食割れ性(sulfide stress corrosion cracking resistance)をともに劣化させる元素である。本発明ではP量を可及的に低減することが好ましい。しかし、極端なP量の低減は製造コストの上昇を招く。工業的に比較的安価に実施可能でかつ耐食性および耐硫化物応力腐食割れ性をともに劣化させない観点からP量は、0.03%以下であることが好ましい。なお、より好ましいP量は0.02%以下である。
Sは、鋼管製造工程(pipe manufacturing process)において熱間加工性を著しく劣化させる元素である。S量を可及的に低減することが好ましい。S量を0.005%以下に低減すれば通常工程による鋼管製造が可能となることから、S量は0.005%以下に限定することが好ましい。なお、より好ましいS量は0.002%以下である。
Crは、鋼管表面に保護被膜(protective surface film)を形成して耐食性を向上させる元素であり、特に耐CO2腐食性、耐硫化物応力腐食割れ性の向上に寄与する元素である。耐食性の観点からは、Cr量を14%以上にすることが好ましい。Cr量が20%を超えると、オーステナイト(austenite)やフェライト(ferrite)の体積分率が過大となり、所望の高強度が保てないうえ、靭性および、熱間加工性も劣化する。なお、より好ましいCr量は15~18%である。
Niは、保護被膜を強固にして、耐CO2腐食性、耐孔食性(pitting corrosion resistance)および耐硫化物応力腐食割れ性を高める作用を有する。さらに、Niは固溶強化により鋼の強度を増加させる元素である。このような効果はNiを1.5%以上含有することで認められる。しかし、Ni量が10%を超えると所望の高強度が得られなくなり、熱間加工性も劣化する場合がある。なお、より好ましいNi量は3~8%である。
Moは、Cl-による孔食に対する抵抗性を増加させる元素である。本発明ではMo量を1%以上にすることが好ましい。Mo量が5%を超えるとオーステナイトやフェライトが過大となり、所望の高強度が保てないうえ、靭性および、熱間加工性も劣化する場合がある。また、Mo量が5%を超えると、金属間化合物(intermetallics)が析出し、靭性および、耐硫化物応力腐食割れ性が劣化する場合がある。なお、より好ましいMo量は2~4%である。
Nは、耐孔食性を著しく向上させる元素である。N量が0.15%を超えると、種々の窒化物(nitride)が形成され、この窒化物の形成により靭性が劣化する場合がある。このため、N量は0.15%以下が好ましい。より好ましいN量は0.1%以下である。
Oは、鋼中では酸化物(oxide)として存在し、各種特性に悪影響を及ぼす。特性向上のためには、できるだけO量を低減することが好ましい。特に、O量が0.006%を超えると、熱間加工性、耐食性、耐硫化物応力腐食割れ性および靭性が著しく低下する。このため、本発明ではO量を0.006%以下に限定することが好ましいとした。
2 焼入れ設備
3 熱処理搬送ライン(兼冷却床(double as cooling bed))
4 低温冷却設備
5 焼戻し加熱炉
Claims (6)
- 圧延ラインの下工程に焼入れ加熱炉、焼入れ設備、および焼戻し加熱炉を配置する継目無鋼管のオンライン熱処理設備列において、前記焼入れ設備と前記焼戻し加熱炉の間に被熱処理鋼管を20℃以下に冷却可能な低温冷却設備を配置し、焼戻し処理前に被熱処理鋼管を20℃以下に冷却することを特徴とする高強度ステンレス鋼管の製造方法。
- 前記高強度ステンレス鋼管が、質量%で、C:0.005~0.05%、Si:0.05~1.0%、Mn:0.2~1.8%、P:0.03%以下、S:0.005%以下、Cr:14~20%、Ni:1.5~10%、Mo:1~5%、N:0.15%以下、O: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る組成を有し、
該高強度ステンレス鋼管を、前記焼入れ加熱炉で850~1000℃に再加熱した後、前記焼入れ設備で空冷以上の冷却速度で50℃以下まで冷却し、続いて、前記低温冷却設備で20℃以下まで冷却した後、前記焼戻し加熱炉で450~700℃の温度に加熱することを特徴とする請求項1に記載の高強度ステンレス鋼管の製造方法。 - 前記組成に加えて、質量%で、Al:0.002~0.05%、Cu:3.5%以下、Nb:0.5%以下、V:0.5%以下、Ti:0.3%以下、Zr:0.2%以下、W:3%以下、B:0.01%以下、Ca:0.01%以下、REM:0.1%以下のうちから選ばれた1種以上を含有することを特徴とする請求項2に記載の高強度ステンレス鋼管の製造方法。
- 圧延ラインの下工程に焼入れ加熱炉、焼入れ設備、および焼戻し加熱炉を配置する継目無鋼管のオンライン熱処理設備列であって、前記焼入れ設備と前記焼戻し加熱炉の間に介設された熱処理搬送ラインの一端または一部に被熱処理鋼管を20℃以下に冷却可能な低温冷却設備を配置したことを特徴とする前記高強度ステンレス鋼管を製造するための熱処理設備列。
- 前記低温冷却設備が被熱処理鋼管を10℃以下の温度まで冷却可能な設備であり、焼戻し処理前に被熱処理鋼管を10℃以下の温度まで冷却することを特徴とする請求項1~3に記載の高強度ステンレス鋼管の製造方法。
- 前記低温冷却設備が、被熱処理鋼管を10℃以下の温度まで冷却可能な設備であることを特徴とする請求項4に記載の前記高強度ステンレス鋼管を製造するための熱処理設備列。
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