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  • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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  • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
  • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
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  • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
  • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
  • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
  • C21D8/0226—Hot rolling
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  • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
  • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
  • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
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  • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
  • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
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  • 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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  • 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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  • 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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  • 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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  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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  • 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
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  • 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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  • 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
  • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
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  • 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
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  • C21D2211/00—Microstructure comprising significant phases
  • C21D2211/005—Ferrite

Definitions

• the present invention relates to a duplex stainless steel and a method for producing the duplex stainless steel.
• a duplex stainless steel having a dual phase structure consisting of the ferrite phase and the austenite phase is known to have excellent corrosion resistance.
• a duplex stainless steel is particularly superior in corrosion resistance against pitting and/or crevice corrosion (hereinafter referred to as "pitting resistance"), which is taken as a problem in an aqueous solution containing chlorides.
• a duplex stainless steel is therefore widely used in a wet environment containing chlorides, such as seawater. In a wet environment containing chlorides, a duplex stainless steel is used, for example, in a flow line pipe, an umbilical tube, and a heat exchanger.
• duplex stainless steel is therefore required to have more excellent pitting resistance.
• a variety of technologies have been proposed.
• Patent Literature 1 discloses a duplex stainless steel containing, in mass%, Ni: 3 to 8%, Cr: 20 to 35%, Mo: 0.01 to 4.0%, and N: 0.05 to 0.60% and further containing one or more types of element selected from Re: 2.0% or less, Ga: 2.0% or less, and Ge: 2.0% or less.
• the fact that the duplex stainless steel contains Re, Ga, or Ge increases the critical potential at which pitting occurs (pitting potential) to enhance the pitting resistance and crevice corrosion resistance.
• Patent Literature 2 discloses a method for producing a duplex stainless steel pipe by performing hot working or hot working and further solid solution heat treatment on a duplex stainless steel material containing, in mass%, Cr: 20 to 35%, Ni: 3 to 10%, Mo: 0 to 6%, W: 0 to 6%, Cu: 0 to 3%, and N: 0.15 to 0.60% to produce a steel pipe for cold working and then performing cold rolling on the steel pipe.
• Patent Literature 2 describes that the method described above provides a duplex stainless steel pipe that can be used, for example, in an oil well and a gas well, shows excellent corrosion resistance also in a carbon dioxide gas corrosion environment or a stress corrosion environment, and has high strength.
• Patent Literature 3 discloses a duplex stainless steel containing, in mass%, Cr: 20 to 30%, Ni: 1 to 11%, Cu: 0.05 to 3.0%, Nd: 0.005 to 0.5%, and N: 0.1 to 0.5% and/or Mo: 0.5 to 6% and W: 1 to 10%.
• the hot workability of the duplex stainless steel is enhanced because the duplex stainless steel contains Nd.
• Patent Literature 4 discloses a super duplex stainless steel containing, in weight%, Cr: 21.0% to 38.0%, Ni: 3.0% to 12.0%, Mo: 1.5% to 6.5%, W: 0 to 6.5%, N: 0.2% to 0.7%, and Ba: 0.0001 to 0.6% and having a pitting resistance equivalent index PREW that satisfies 40 ⁇ PREW ⁇ 67.
• Patent Literature 4 describes that the thus configured super duplex stainless steel is superior in corrosion resistance, embrittlement resistance, castability, and hot workability with formation of intermetal phases, such as the brittle sigma ( ⁇ ) phase and the chi ( ⁇ ) phase, suppressed.
• An objective of the present disclosure is to provide a duplex stainless steel having excellent pitting resistance and a method for producing the duplex stainless steel.
• a duplex stainless steel according to the present disclosure has a chemical composition consisting of, in mass%, Cr: more than 27.00% to 29.00%, Mo: 2.50 to 3.50%, Ni: 5.00 to 8.00%, W: 4.00 to 6.00%, Cu: 0.01 to less than 0.10%, N: more than 0.400% to 0.600%, C: 0.030% or less, Si: 1.00% or less, Mn: 1.00% or less, sol.Al: 0.040% or less, V: 0.50% or less, O: 0.010% or less, P: 0.030% or less, S: 0.020% or less, Ca: 0 to 0.0040%, Mg: 0 to 0.0040%, and B: 0 to 0.0040% with the balance being Fe and impurities and satisfying Formula (1), and a microstructure consisting of 35 to 65 volume% of ferrite phase with the balance being an austenite phase.
• an area fraction of Cu precipitated in the ferrite phase is 0.5% or less.
• a method for producing a duplex stainless steel according to the present disclosure includes a preparation step, a hot working step, a cooling step, and a solution heat treatment step.
• a preparation step a starting material having the chemical composition described above is prepared.
• the hot working step the starting material is subjected to hot working at 850°C or more.
• the cooling step the starting material subjected to the hot working is cooled at a rate of 5°C/sec or more.
• the solution heat treatment step the cooled starting material is subjected to a solution heat treatment at 1070°C or more.
• the duplex stainless steel according to the present disclosure has excellent pitting resistance.
• the method for producing the duplex stainless steel according to the present disclosure allows production of the duplex stainless steel described above.
• the present inventors have investigated and studied an approach for enhancing the pitting resistance of a duplex stainless steel. As a result, the following findings have been achieved.
• Cr, Mo, and Cu are known to be effective in improvement of the pitting resistance of a duplex stainless steel.
• Cr, Mo, and Cu, Cr and Mo are believed to have a mechanism that enhances the pitting resistance of a duplex stainless steel as follows: Cr serves as a primary component of a passive film as an oxide on the surface of a duplex stainless steel. The passive film prevents contact between corrosion factors and the surface of the duplex stainless steel. As a result, the duplex stainless steel on the surface of which the passive film has been formed has enhanced pitting resistance. Mo is contained in the passive film and further enhances the pitting resistance of the passive film.
• Cu is believed to have a mechanism that enhances the pitting resistance of a duplex stainless steel as follows: It is believed that there are the following two steps that cause pitting to occur. The first step is occurrence of pitting (initial stage). The next step is propagation of the pitting (propagation stage). It has been believed that Cu is effective in suppressing the propagation of pitting. Particularly in an acidic solution, an active site where the duplex stainless steel melts at high speed is formed on the surface of the duplex stainless steel. Cu coats the active site to suppress the melting of the duplex stainless steel. It has been believed that the thus functioning Cu suppresses the propagation of the pitting that occurs on a duplex stainless steel.
• Table 1 is a table showing the chemical compositions of test specimens labeled with test numbers 2 and 5 and the pitting potential, which is an index of the pitting resistance, of the test specimens in Examples described later.
• the chemical compositions listed in two rows in Table 1 are those of steels of B and E, correspond to the test numbers 2 and 5, and are extracted from Table 3, which will be described later.
• the chemical compositions in Table 1 are expressed in mass%, and the balance is Fe and impurities.
• the pitting potentials listed in Table 1 are those labeled with the corresponding test numbers and are extracted from Table 4, which will be described later.
• the test specimen labeled with the test number 2 has a higher Cu content than the Cu content in the test specimen labeled with the test number 5. Further, the test specimen labeled with the test number 2 has higher Cr and Mo contents than the Cr and Mo contents in the test specimen labeled with the test number 5. It can therefore be expected based on the findings in the related art that the test specimen labeled with the test number 2, which has higher Cr, Mo, and Cu contents, has more excellent pitting resistance than the test specimen labeled with the test number 5.
• the pitting potential, which is an index of the pitting resistance, of the test specimen labeled with the test number 2 is, however, 71 mVvs.SCE, which is smaller than the pitting potential of 346 mVvs.SCE of the test specimen labeled with the test number 5.
• the pitting resistance of the test specimen labeled with the test number 2 which is expected based on the findings in the related art to have more excellent pitting resistance than the test specimen labeled with the test number 5, is instead smaller than the pitting resistance of the test specimen labeled with the test number 5.
• the present inventors have focused on the microstructures of the test specimens labeled with the test numbers 2 and 5 and have investigated the microstructures in more detail. As a result, the investigation clearly showed that the test specimen labeled with the test number 2 has a greater area fraction of Cu precipitated in the ferrite phase (called Cu area fraction in ferrite phase) than the test specimen labeled with the test number 5.
• Table 2 is a table showing the chemical compositions of test specimens labeled with the test numbers 3 and 6, the Cu area fractions thereof in the ferrite phase, and the pitting potential thereof, which is an index of the pitting resistance, in Examples described later.
• the chemical compositions listed in two rows in Table 2 are those of steel of C, correspond to the test numbers 3 and 6, and are extracted from Table 3, which will be described later.
• the chemical compositions in Table 2 are expressed in mass%, and the balance is Fe and impurities.
• the Cu area fractions thereof in the ferrite phase listed in Table 2 are those labeled with the corresponding test numbers and are extracted from Table 4, which will be described later.
• the pitting potentials listed in Table 2 are those labeled with the corresponding test numbers and are extracted from Table 4, which will be described later.
• the test specimen labeled with the test number 3 and the test specimen labeled with the test number 6 had the same chemical composition.
• the test specimen labeled with the test number 6 had a smaller Cu area fraction in the ferrite phase than the Cu area fraction in the ferrite phase of the test specimen labeled with the test number 3.
• the pitting potential of the test specimen labeled with the test number 6 was 204 mVvs.SCE, which was greater than the pitting potential of -12 mVvs.SCE of the test specimen labeled with the test number 3.
• test specimen labeled with the test number 6 had more excellent pitting resistance than the test specimen labeled with the test number 3 as a result of a decrease in the amount of precipitation of Cu in the ferrite phase in the test specimen labeled with the test number 6.
• a duplex stainless steel according to the present embodiment attained based on the findings described above has a chemical composition consisting of, in mass%, Cr: more than 27.00% to 29.00%, Mo: 2.50 to 3.50%, Ni: 5.00 to 8.00%, W: 4.00 to 6.00%, Cu: 0.01 to less than 0.10%, N: more than 0.400% to 0.600%, C: 0.030% or less, Si: 1.00% or less, Mn: 1.00% or less, sol.Al: 0.040% or less, V: 0.50% or less, O: 0.010% or less, P: 0.030% or less, S: 0.020% or less, Ca: 0 to 0.0040%, Mg: 0 to 0.0040%, and B: 0 to 0.0040% with the balance being Fe and impurities and satisfying Formula (1), and a microstructure consisting of 35 to 65 volume% of ferrite phase with the balance being the austenite phase.
• the area fraction of Cu precipitated in the ferrite phase is 0.5% or less.
• the duplex stainless steel according to the present embodiment has the chemical composition described above and the microstructure described above, and the area fraction of Cu in the ferrite phase is 0.5% or less. As a result, the duplex stainless steel according to the present embodiment has excellent pitting resistance.
• the chemical composition described above preferably contains, in mass%, one or more types of element selected from the group consisting of Ca: 0.0001 to 0.0040%, Mg: 0.0001 to 0.0040%, and B: 0.0001 to 0.0040%.
• the duplex stainless steel according to the present embodiment has enhanced hot workability.
• a method for producing a duplex stainless steel according to the present embodiment includes a preparation step, a hot working step, a cooling step, and a solution heat treatment step.
• a preparation step a starting material having the chemical composition described above is prepared.
• the hot working step the starting material is subjected to hot working at 850°C or more.
• the cooling step the starting material subjected to the hot working is cooled at a rate of 5°C/sec or more.
• the solution heat treatment step the cooled starting material is subjected to a solution heat treatment at 1070°C or more.
• the duplex stainless steel produced by the production method according to the present embodiment has the chemical composition described above and the microstructure described above, and the area fraction of Cu in the ferrite phase is 0.5% or less. As a result, the duplex stainless steel produced by the production method according to the present embodiment has excellent pitting resistance.
• duplex stainless steel according to the present embodiment will be described below in detail.
• the chemical composition of the duplex stainless steel according to the present embodiment contains the following elements.
• the symbol % associated with an element means mass% unless otherwise specified.
• Chromium (Cr) forms a passive film as an oxide on the surface of the duplex stainless steel.
• the passive film prevents contact between corrosion factors and the surface of the duplex stainless steel. As a result, occurrence of pitting on the duplex stainless steel is suppressed.
• Cr is an element necessary for achievement of the ferrite structure in the duplex stainless steel. Achievement of a sufficient ferrite structure provides stable pitting resistance. Too low a Cr content provides no effects described above. On the other hand, too high a Cr content lowers the hot workability of the duplex stainless steel.
• the Cr content therefore ranges from more than 27.00% to 29.00%.
• the lower limit of the Cr content is preferably 27.50%, more preferably 28.00%.
• the upper limit of the Cr content is preferably 28.50%.
• Molybdenum (Mo) is contained in the passive film and further enhances the corrosion resistance of the passive film. As a result, the pitting resistance of the duplex stainless steel is enhanced. Too low a Mo content provides no effect described above. On the other hand, too high a Mo content lowers the workability of, for example, the assembly of a steel pipe made of the duplex stainless steel.
• the Mo content therefore ranges from 2.50 to 3.50%.
• the lower limit of the Mo content is preferably 2.80%, more preferably 3.00%.
• the upper limit of the Mo content is preferably 3.30%.
• Nickel (Ni) is an austenite stabilizing element and is an element necessary for achievement of the ferrite/austenite dual phase structure. Too low a Ni content provides no effect described above. On the other hand, too high a Ni content causes imbalance between the ferrite phase and the austenite phase. In this case, the duplex stainless steel is not stably produced.
• the Ni content therefore ranges from 5.00 to 8.00%.
• the lower limit of the Ni content is preferably 5.50%, more preferably 6.00%.
• the upper limit of the Ni content is preferably 7.50%.
• Tungsten (W) is contained in the passive film and further enhances the corrosion resistance of the passive film, as in the case of Mo. As a result, occurrence of the pitting on the duplex stainless steel is suppressed. Too low a W content provides no effect described above. On the other hand, too high a W content is likely to cause the ⁇ phase to precipitate easily, resulting in a decrease in toughness.
• the W content therefore ranges from 4.00 to 6.00%.
• the lower limit of the W content is preferably 4.50%.
• the upper limit of the W content is preferably 5.50%.
• Copper (Cu) is an element effective in suppressing the propagation of the pitting (propagation stage). Too low a Cu content provides no effect described above. On the other hand, among Cr, Mo, and Cu, Cu lowers the pitting resistance at the occurrence of pitting (initial stage).
• the duplex stainless steel according to the present embodiment therefore has a lowered Cu content as compared with the Cu content in a duplex stainless steel of the related art. As a result, the precipitation of Cu in the ferrite phase is suppressed, and occurrence of pitting on the duplex stainless steel (initial stage) is suppressed. Too high a Cu content causes too large an area fraction of Cu in the ferrite phase. In this case, the pitting resistance of the duplex stainless steel lowers.
• the Cu content therefore ranges from 0.01 to less than 0.10%.
• the upper limit of the Cu content is preferably 0.07%, more preferably 0.05%.
• N more than 0.400% to 0.600%
• N Nitrogen
• the N content therefore ranges from more than 0.400% to 0.600%.
• the lower limit of the N content is preferably 0.420%.
• the upper limit of the N content is preferably 0.500%.
• Carbon (C) is inevitably contained. That is, the C content is more than 0%. C forms a Cr carbide in the crystal grain boundary, and the Cr carbide increases the corrosion susceptibility in the grain boundary.
• the C content is therefore 0.030% or less.
• the upper limit of the C content is preferably 0.025%, more preferably 0.020%.
• the C content is preferably minimized. Extreme reduction in the C content, however, greatly increases the production cost.
• the lower limit of the C content is therefore preferably 0.001%, and more preferably 0.005% in consideration of industrial production.
• Si deoxidizes steel.
• the Si content is more than 0%.
• too high a Si content lowers the hot workability of the duplex stainless steel.
• the Si content is therefore 1.00% or less.
• the upper limit of the Si content is preferably 0.80%, and more preferably 0.70%.
• the lower limit of the Si content is not limited to a specific value and is, for example, 0.20%.
• Manganese (Mn) deoxidizes steel.
• the Mn content is more than 0%.
• too high a Mn content lowers the hot workability of the duplex stainless steel.
• the Mn content is therefore 1.00% or less.
• the upper limit of the Mn content is preferably 0.80%, and more preferably 0.70%.
• the lower limit of the Mn content is not limited to a specific value and is, for example, 0.20%.
• the Al content is more than 0%.
• too high an Al content lowers the hot workability of the duplex stainless steel.
• the Al content is therefore 0.040% or less.
• the upper limit of the Al content is preferably 0.030%, and more preferably 0.025%.
• the lower limit of the Al content is not limited to a specific value and is, for example, 0.005%.
• the Al content refers to the acid-soluble Al (sol.Al) content.
• V 0.50% or less
• Vanadium (V) is inevitably contained. That is, the V content is more than 0%. Too high a V content excessively increases the amount of the ferrite phase, resulting in decreases in toughness and corrosion resistance of the duplex stainless steel in some cases.
• the V content is therefore 0.50% or less.
• the upper limit of the V content is preferably 0.40%, and more preferably 0.30%.
• the lower limit of the V content is not limited to a specific value and is, for example, 0.05%.
• Oxygen (O) is an impurity. That is, the O content is more than 0%. O lowers the hot workability of the duplex stainless steel. The O content is therefore 0.010% or less.
• the upper limit of the O content is preferably 0.007%, and more preferably 0.005%.
• the O content is preferably minimized. Extreme reduction in the O content, however, greatly increases the production cost.
• the lower limit of the O content is therefore preferably 0.0001%, and more preferably 0.0005% in consideration of industrial production.
• Phosphorus (P) is an impurity. That is, the P content is more than 0%. P lowers the pitting resistance and toughness of the duplex stainless steel. The P content is therefore 0.030% or less.
• the upper limit of the P content is preferably 0.025%, and more preferably 0.020%.
• the P content is preferably minimized. Extreme reduction in the P content, however, greatly increases the production cost.
• the lower limit of the P content is therefore preferably 0.001 %, and more preferably 0.005% in consideration of industrial production.
• S is an impurity. That is, the S content is more than 0%. S lowers the hot workability of the duplex stainless steel.
• the S content is therefore 0.020% or less.
• the upper limit of the S content is preferably 0.010%, more preferably 0.005%, and still more preferably 0.003%.
• the S content is preferably minimized. Extreme reduction in the S content, however, greatly increases the production cost.
• the lower limit of the S content is therefore preferably 0.0001%, and more preferably 0.0005% in consideration of industrial production.
• the balance of the chemical composition of the duplex stainless steel according to the present embodiment is Fe and impurities.
• the impurities in the chemical composition mean contaminants, for example, from ore as a raw material, scraps, or the production environment in industrial production of the duplex stainless steel that are acceptable to the extent that the contaminants do not adversely affect the duplex stainless steel according to the present embodiment.
• Ca Calcium
• the Ca content is therefore 0 to 0.0040%.
• the lower limit of the Ca content is preferably 0.0001%, more preferably 0.0005%, and still more preferably 0.0010%.
• the upper limit of the Ca content is preferably 0.0030%.
• Magnesium (Mg) is an optional element and may not be contained. That is, the Mg content may be 0%. When contained, Mg enhances the hot workability of the duplex stainless steel, as does Ca. When Mg is contained even by a trace amount, the effect described above is provided to some extent. On the other hand, too high a Mg content produces a coarse oxide, which lowers the hot workability of the duplex stainless steel.
• the Mg content is therefore 0 to 0.0040%.
• the lower limit of the Mg content is preferably 0.0001%, more preferably 0.0005%, and still more preferably 0.0010%.
• the upper limit of the Ca content is preferably 0.0030%.
• B Boron
• B is an optional element and may not be contained. That is, the B content may be 0%. When contained, B enhances the hot workability of the duplex stainless steel, as do Ca and Mg. When B is contained even by a trace amount, the effect described above is provided to some extent. On the other hand, too high a B content lowers the toughness of the duplex stainless steel.
• the B content is therefore 0 to 0.0040%.
• the lower limit of the B content is preferably 0.0001%, more preferably 0.0005%, and still more preferably 0.0010%.
• the upper limit of the Ca content is preferably 0.0030%.
• the chemical composition of the duplex stainless steel according to the present embodiment satisfies the contents of the elements described above and further satisfies the following Formula (1): Cr + 4.0 ⁇ Mo + 2.0 ⁇ W + 20 ⁇ N ⁇ 5 ⁇ ln Cu ⁇ 65.2 where, content in mass% of each of the elements is substituted into the corresponding symbol of the element in Formula (1).
• F1 Cr+4.0 ⁇ Mo+2.0 ⁇ W+20 ⁇ N-5 ⁇ ln(Cu).
• F1 is an index representing the pitting resistance. When F1 is less than 65.2, the pitting resistance of the duplex stainless steel lowers. The following formula is therefore satisfied: F1 ⁇ 65.2.
• the lower limit of F1 is preferably 68.0, more preferably 69.0, and still more preferably 70.0.
• the upper limit of F1 is not limited to a specific value and is, for example, 90.0.
• the microstructure of the duplex stainless steel according to the present embodiment consists of ferrite and austenite. Specifically, the microstructure of the duplex stainless steel according to the present embodiment consists of 35 to 65 volume% of ferrite phase with the balance being the austenite phase.
• the volume ratio of the ferrite phase hereinafter also referred to as ferrite fraction
• stress corrosion cracking is more likely to occur depending on the environment in which the duplex stainless steel is used.
• the volume ratio of the ferrite phase is more than 65%, the toughness of the duplex stainless steel is more likely to lower. Therefore, the microstructure of the duplex stainless steel according to the present embodiment consists of 35 to 65 volume% of ferrite phase with the balance being the austenite phase.
• the ferrite fraction of the duplex stainless steel can be determined by the following method: A test specimen for microstructure observation is collected from the duplex stainless steel. When the duplex stainless steel is used to form a steel plate, a cross section of the steel plate that is the cross section perpendicular to the plate width direction of the steel plate (hereinafter referred to as observation surface) is polished. When the duplex stainless steel is used to form a steel pipe, a cross section of the steel pipe that is the cross section (observation surface) containing the axial direction and the wall thickness direction of the steel pipe is polished.
• a cross section of the steel bar or the wire rod that is the cross section (observation surface) containing the axial direction of the steel bar or the wire rod is polished.
• the polished observation surface is then etched by using a liquid that is the mixture of aqua regia and glycerin.
• Ten visual fields of the etched observation surface are observed under an optical microscope.
• the area of each of the visual fields is, for example, 2000 ⁇ m 2 (at magnification of 500).
• the ferrite and the other phases can be distinguished from each other based on contrast.
• the ferrite is therefore identified based on the contrast in each observation.
• the area fraction of the identified ferrite is measured by using a point counting method compliant with JIS G0555 (2003).
• the measured area fraction is assumed to be equal to the volume fraction, which is then defined as a ferrite fraction (volume%).
• the area fraction of Cu precipitated in the ferrite phase of the duplex stainless steel according to the present embodiment is 0.5% or less. It is believed as described above that Cu contained in the duplex stainless steel suppresses the propagation of the pitting on the duplex stainless steel.
• the duplex stainless steel according to the present embodiment therefore contains Cu by an amount ranging from 0.01 to less than 0.10%.
• metal Cu precipitates in the ferrite phase in some cases It has clearly been shown as described above that Cu precipitated in the ferrite phase lowers the passive film's effect of suppressing occurrence of pitting. That is, metal Cu precipitated in the ferrite phase lowers the pitting resistance of the duplex stainless steel.
• the duplex stainless steel according to the present embodiment has a reduced Cu area fraction in the ferrite phase to 0.5% or less. The occurrence of pitting on the duplex stainless steel is thus suppressed.
• the Cu area fraction in the ferrite phase is preferably minimized.
• the upper limit of the Cu area fraction in the ferrite phase is preferably 0.3%, and more preferably 0.1%.
• the lower limit of the Cu area fraction in the ferrite phase is 0.0%.
• the Cu area fraction in the ferrite phase means the area fraction of Cu precipitated in the ferrite phase out of the microstructure of the duplex stainless steel with respect to the ferrite phase.
• the Cu area fraction in the ferrite phase can be measured by the following method: A thin film specimen for observation under a transmission electron microscope (TEM) is prepared by an FIB-micro-sampling method. To prepare the thin film specimen, a focused ion beam processing apparatus (MI4050 manufactured by Hitachi High-Tech Science Corporation) is used. A thin film specimen for TEM observation is prepared from an arbitrary portion of the duplex stainless steel. To prepare the thin film specimen, a mesh made of Mo and a carbon deposit film as a surface protection film are used.
• a field emission transmission electron microscope (JEM-2100F manufactured by JEOL Ltd.) is used for the TEM observation.
• the TEM observation is performed at an observation magnification of 10000.
• the ferrite phase and the austenite phase in a visual field differ from each other in terms of contrast.
• the crystal grain boundary is then identified based on the contrast.
• the phase of a region surrounded by each crystal grain boundary is identified by X-ray diffraction (XRD).
• XRD X-ray diffraction
• EDS energy dispersive X-ray spectrometry
• the area of Cu precipitated in the identified ferrite phase is determined by image analysis. The sum of the areas of Cu precipitated in the ferrite phase is divided by the sum of areas of the ferrite phase. The Cu area fraction (%) in the ferrite phase is thus measured.
• the duplex stainless steel according to the present embodiment satisfies both the chemical composition including Formula (1) and the microstructure including the in-ferrite-phase Cu area fraction described above.
• the duplex stainless steel according to the present embodiment therefore has excellent pitting resistance.
• the yield strength of the duplex stainless steel according to the present embodiment is not limited to a specific value.
• the yield strength is 750 MPa or less, however, the cold working can be omitted in the production process. In this case, the production cost can be reduced.
• the yield strength is therefore preferably 750 MPa or less.
• the yield strength is more preferably 720 MPa or less.
• the lower limit of the yield strength is not limited to a specific value and is, for example, 300 MPa.
• the yield strength in the present specification means 0.2% proof stress determined by a method compliant with JIS Z2241 (2011).
• the shape of the duplex stainless steel according to the present embodiment is not limited to a specific shape.
• the duplex stainless steel may be used in a form of, for example, a steel pipe, a steel plate, a steel bar, or a wire rod.
• the duplex stainless steel according to the present embodiment can be produced, for example, by the following method:
• the production method includes a preparation step, a hot working step, a cooling step, and a solution heat treatment step.
• a starting material having the chemical composition described above is prepared.
• the starting material may be a cast piece produced by a continuous casting process (including round continuous casting) or a slab produced from the cast piece.
• the starting material may be a slab produced by performing hot working on an ingot produced by an ingot-making process.
• the prepared starting material is placed in a heating furnace or a soaking pit and heated at a temperature ranging, for example, from 1150 to 1300°C.
• the heated starting material is subsequently subjected to hot working.
• the hot working may be hot forging, hot extrusion using, for example, the Ugine-Sejournet process or the Ehrhardt push bench process, or hot rolling.
• the hot working may be performed once or multiple times.
• the heated starting material is subjected to hot working at 850°C or more. More specifically, the surface temperature of the steel material at the end of the hot working is 850°C or more.
• the surface temperature of the steel material at the end of the hot working is less than 850°C, a large amount of Cu precipitates in the ferrite phase. As a result, even a solution treatment, which will be described later, cannot sufficiently reduce the Cu area fraction in the ferrite phase in some cases. In this case, the pitting resistance of the duplex stainless steel lowers.
• the surface temperature of the steel material at the end of the hot working is therefore 850°C or more. In a case where the hot working is performed multiple times, the surface temperature of the steel material at the end of the last hot working is 850°C or more.
• Precipitation of Cu in the ferrite phase can thus be suppressed at the end of the hot working.
• the upper limit of the surface temperature of the steel material at the end of the hot working is not limited to a specific value and is, for example, 1300°C.
• the end of the hot working is the point of time within three seconds after the hot working ends.
• the starting material after the hot working is subsequently cooled at a rate of 5°C/sec or more.
• Cu starts precipitating in the ferrite phase at around 850°C. Therefore, if the cooling rate after the hot working is too slow, a large amount of Cu precipitates in the ferrite phase. As a result, even a solution treatment, which will be described later, cannot sufficiently reduce the Cu area fraction in the ferrite phase in some cases. In this case, the pitting resistance of the duplex stainless steel lowers.
• the cooling rate after the hot working is therefore 5°C/sec or more.
• the hot working refers to "after the last hot working.” That is, in the present embodiment, the starting material after the last hot working is cooled at the rate of 5°C/sec or more.
• the upper limit of the cooling rate is not limited to a specific value.
• the cooling method is, for example, air cooling, water cooling, or oil cooling.
• the cooled starting material is subsequently subjected to a solution heat treatment at 1070°C or more.
• the solution heat treatment causes the Cu precipitated in the ferrite phase to dissolve.
• Performing the solution heat treatment at 1070°C or more on the starting material in which the precipitation of Cu in the ferrite phase at the end of the hot working and after the cooling is sufficiently suppressed allows the Cu area fraction in the ferrite phase to be 0.5% or less.
• the upper limit of the solution heat treatment temperature is not limited to a specific value and is, for example, 1150°C.
• the treatment period of the solution heat treatment is not limited to a specific value.
• the treatment period of the solution heat treatment ranges, for example, from 1 to 30 minutes.
• the duplex stainless steel according to the present embodiment can be produced by carrying out the steps described above. In the present embodiment, it is preferable to perform no cold working because cold working increases the production cost.
• Alloys having the chemical compositions shown in Table 3 were melted in a 50 kg vacuum furnace, the obtained ingots were heated at 1200°C, and the heated ingots were subjected to hot forging and hot rolling into steel plates having a thickness of 10 mm.
• the temperatures at the end of rolling shown in Table 4 are the surface temperatures of the steel plates at the end of the hot rolling.
• the post-rolling cooling rates shown in Table 4 are the cooling rates after the hot rolling.
• the steel plates were subjected to a solution treatment at the solution temperatures (°C) shown in Table 4 into test specimens labeled with the test numbers.
• the ferrite fraction (volume%) of each of the test specimens labeled with the test numbers was measured by using the method described above. Table 4 shows the results of the measurement. The balance of the microstructure of each of the test specimens labeled with the test numbers was the austenite phase.
• the in-ferrite-phase Cu area fraction (%) of each of the test specimens labeled with the test numbers was measured by using the method described above.
• Table 4 shows the results of the measurement.
• the pitting potential of each of the test specimens labeled with the test numbers after the solution treatment was measured.
• the test specimens were each first machined into a test specimen having a diameter of 15 mm and a thickness of 2 mm.
• the obtained test specimens were each used to measure the pitting potential in 25% NaClaq. at 80°C.
• the conditions other than the test temperature and the NaCl concentration were compliant with JIS G0577 (2014).
• Table 4 shows the results of the measurement of pitting potential Vc' 100 of the test specimens labeled with the test numbers.
• the 0.2% proof stress of the test specimens labeled with the respective test numbers was determined by using a method compliant with JIS Z2241 (2011). Table 4 shows the results of the determination.
• test specimens labeled with test numbers 5 to 8 had appropriate chemical compositions and were produced under appropriate conditions.
• the test specimens labeled with the test numbers 5 to 8 therefore were the duplex stainless steel having a ferrite fraction ranging from 35 to 65 volume% with the balance being the austenite phase, and the Cu area fraction in the ferrite phase was 0.5% or less.
• the pitting potential (mVvs.SCE) of each of the steel plates labeled with the test numbers 5 to 8 was 100 or more, which represented excellent pitting resistance.
• the test specimen labeled with test number 1 has too high a Cu content. Further, F1 of the test specimen labeled with the test number 1 was 59.8, which did not satisfy Formula (1). The Cu area fraction in the ferrite phase of the test specimen labeled with the test number 1 was therefore 0.8%. As a result, the pitting potential (mVvs.SCE) of the test specimen labeled with the test number 1 was -60, which did not represent excellent pitting resistance.
• the test specimen labeled with test number 2 has too high a Cu content.
• the Cu area fraction in the ferrite phase of the test specimen labeled with the test number 2 was therefore 0.6%.
• the pitting potential (mVvs.SCE) of the test specimen labeled with the test number 2 was 71, which did not represent excellent pitting resistance.
• the solution temperature of the test specimen labeled with test number 3 was 1050°C, which was too low.
• the Cu area fraction in the ferrite phase of the test specimen labeled with the test number 3 was therefore 0.7%.
• the pitting potential (mVvs.SCE) of the test specimen labeled with the test number 3 was -12, which did not represent excellent pitting resistance.
• the test specimen labeled with test number 9 had too low a W content.
• the pitting potential (mVvs.SCE) of the test specimen labeled with the test number 9 was 70, which did not represent excellent pitting resistance.
• the test specimen labeled with test number 10 had too low a Mo content.
• the pitting potential (mVvs.SCE) of the test specimen labeled with the test number 10 was 76, which did not represent excellent pitting resistance.
• the test specimen labeled with test number 11 had too low a Cr content.
• the pitting potential (mVvs.SCE) of the test specimen labeled with the test number 11 was 81, which did not represent excellent pitting resistance.
• the temperature of the test specimen labeled with test number 12 at the end of the hot rolling was 840°C, which was too low.
• the Cu area fraction in the ferrite phase of the test specimen labeled with the test number 12 was therefore 1.1%.
• the pitting potential (mVvs.SCE) of the test specimen labeled with the test number 12 was -150, which did not represent excellent pitting resistance.
• the cooling rate at which the test specimen labeled with test number 13 was cooled at the end of the hot rolling was 3°C/sec, which was too slow.
• the Cu area fraction in the ferrite phase of the test specimen labeled with the test number 13 was therefore 1.6%.
• the pitting potential (mVvs.SCE) of the test specimen labeled with the test number 13 was -71, which did not represent excellent pitting resistance.

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