Classifications

• • 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
• • 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
  • C21D6/02—Hardening by precipitation
• • 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
  • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
  • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
• • 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
  • C21D8/02—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
• • 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
  • C21D8/02—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
  • C21D8/0236—Cold rolling
• • 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
  • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
• • 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
• • 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
  • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
• • 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
  • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
• • 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
• • 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
  • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
• • 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
• • 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
• • 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
• • 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
  • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
• • 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
  • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
• • 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

Definitions

• the present invention relates to a stainless steel, more specifically to an austenitic stainless steel.
• Some components for plant facilities such as a heating furnace pipe of a thermal boiler, an oil-refining and petrochemical plant, or other facilities, are used under a high-temperature corrosive environment, the temperature of which is as high as 600 to 700°C, and a corrosive fluid containing sulfide and/or chloride is contained in the environment.
• a corrosive fluid containing sulfide and/or chloride is contained in the environment.
• air, moisture, and sulfide scale react to form polythionic acid on a surface of a component.
• the polythionic acid induces stress corrosion cracking in a grain boundary (hereafter, referred to as polythionic acid SCC). Accordingly, components used in the high-temperature corrosive environment described above are required to have an excellent polythionic acid SCC resistance.
• Patent Literature 1 Japanese Patent Application Publication No. 2003-166039 (Patent Literature 1) and International Application Publication No. WO2009/044802 (Patent Literature 2).
• the polythionic acid SCC occurs due to Cr precipitating in a form of an M 23 C 6 carbide in a grain boundary and a resultant Cr depleted zone formed in the proximity of the grain boundary. Therefore, according to Patent Literature 1 and Patent Literature 2, the polythionic acid SCC resistance is increased by reducing an amount of C to inhibit the formation of the M 23 C 6 carbide.
• an heat resistant austenitic steel disclosed in Patent Literature 1 contains, in mass%, C: 0.005 to less than 0.03%, Si: 0.05 to 0.4%, Mn: 0.5 to 2%, P: 0.01 to 0.04%, S: 0.0005 to 0.005%, Cr: 18 to 20%, Ni: 7 to 11%, Nb: 0.2 to 0.5%, V: 0.2 to 0.5%, Cu: 2 to 4%, N: 0.10 to 0.30%, and B: 0.0005 to 0.0080%, with the balance being Fe and unavoidable impurities.
• a total of contents of Nb and V is 0.6% or more, and a solubility of Nb in the steel is 0.15% or more.
• N/14 ⁇ Nb/93 + V/51 and Cr - 16C - 0.5Nb - V ⁇ 17.5 are satisfied.
• the polythionic acid SCC resistance is increased by reducing the amount of C and regulating a relation between Cr, and C, Nb, and V.
• An austenitic stainless steel disclosed in Patent Literature 2 contains in mass%, C: less than 0.04%, Si: 1.5% or less, Mn: 2% or less, Cr: 15 to 25%, Ni: 6 to 30%, N: 0.02 to 0.35%, and Sol.Al: 0.03% or less, and further contains one or more elements selected from the group consisting of Nb: 0.5% or less, Ti: 0.4% or less, V: 0.4% or less, Ta: 0.2% or less, Hf: 0.2% or less, and Zr: 0.2% or less, with the balance being Fe and impurities.
• the impurities include P: 0.04% or less, S: 0.03% or less, Sn: 0.1% or less, As: 0.01% or less, Zn: 0.01% or less, Pb: 0.01% or less, and Sb: 0.01% or less.
• F1 S + ⁇ (P + Sn) / 2 ⁇ + ⁇ (As + Zn + Pb + Sb) / 5 ⁇ ⁇ 0.075 and 0.05 ⁇ Nb + Ta + Zr + Hf + 2Ti + (V/10) ⁇ 1.7 - 9 ⁇ F1 are satisfied.
• the polythionic acid SCC resistance is increased by setting the amount of C at less than 0.05%.
• grain boundary embrittling elements in the steel such as P, S, and Sn are reduced by reducing C immobilizing elements such as Nb and Ti, thereby enhancing embrittlement cracking resistance in a weld heat affected zone (HAZ).
• Components used in the high-temperature corrosive environment described above have recently been required to have high creep ductilities.
• a plant facility may undergo a regular inspection with its equipment deactivated.
• the regular inspection involves examination of what components are in need of replacement.
• a high creep ductility allows checking how much a component deforms to be used as a criterion for replacing the component in the regular inspection.
• Patent Literature 1 and Patent Literature 2 aim at improving the polythionic acid SCC resistance but do not aim at enhancing the creep ductility.
• the steels proposed in these Patent Literatures each have a reduced amount of C in order to increase the polythionic acid SCC resistance. In this instance, there are cases where a high creep ductility cannot be obtained.
• An objective of the present invention is to provide an austenitic stainless steel excellent in the polythionic acid SCC resistance and excellent in the creep ductility.
• An austenitic stainless steel according to the present invention includes a chemical composition consisting of, in mass%, C: 0.030% or less, Si: 0.10 to 1.00%, Mn: 0.20 to 2.00%, P: 0.040% or less, S: 0.010% or less, Cr: 16.0 to 25.0%, Ni: 10.0 to 30.0%, Mo: 0.1 to 5.0%, Nb: 0.20 to 1.00%, N: 0.050 to 0.300%, sol.Al: 0.0005 to 0.100%, B: 0.0010 to 0.0080%, Cu: 0 to 5.0%, W: 0 to 5.0%, Co: 0 to 1.0%, V: 0 to 1.00%, Ta: 0 to 0.2%, Hf: 0 to 0.20%, Ca: 0 to 0.010%, Mg: 0 to 0.010%, and rare earth metals: 0 to 0.10%, with the balance being Fe and impurities, and satisfying Formula (1): B + 0.004 ⁇ 0.9 ⁇ C + 0.017 Mo 2 ⁇
• the austenitic stainless steel according to the present invention is excellent in the polythionic acid SCC resistance and excellent in the creep ductility.
• the present inventors conducted investigations and studies on steels that are excellent not only in the polythionic acid SCC resistance but also in the creep ductility.
• the present inventors conducted further studies about an austenitic stainless steel which can establish compatibility between an excellent polythionic acid SCC resistance and an excellent creep ductility.
• B boron
• B is considered to be able to increase the grain boundary strength through segregating in crystal grain boundaries under the high-temperature corrosive environment at 600 to 700°C described above.
• the present inventors thus considered that the compatibility between the excellent polythionic acid SCC resistance and the excellent creep ductility can be established with an austenitic stainless steel consisting of, in mass%, C: 0.030% or less, Si: 0.10 to 1.00%, Mn: 0.20 to 2.00%, P: 0.040% or less, S: 0.010% or less, Cr: 16.0 to 25.0%, Ni: 10.0 to 30.0%, Mo: 0.1 to 5.0%, Nb: 0.20 to 1.00%, N: 0.050 to 0.300%, sol.Al: 0.0005 to 0.100%, B: 0.0010 to 0.0080%, Cu: 0 to 5.0%, W: 0 to 5.0%, Co: 0 to 1.0%, V: 0 to 1.00%, Ta: 0 to 0.2%, Hf: 0 to 0.20%, Ca: 0 to 0.010%, Mg: 0 to 0.010%, and rare earth metals: 0 to 0.10%, with the balance being Fe and impurities.
• the present embodiment involves both setting the content of C at 0.030% or less to increase the polythionic acid SCC resistance, and making 0.20 to 1.00% of Nb contained to immobilize C on Nb, so as to reduce the dissolved C.
• Nb combines with C through solution treatment or short-time aging, precipitating in a form of MX carbo-nitride.
• the MX carbo-nitride is of a metastable phase.
• an MX carbo-nitride of Nb transforms into a Z phase (CrNbN), a stable phase, and an M 23 C 6 carbide.
• B segregating in grain boundaries is replaced with C being part of the M 23 C 6 carbide, so as to be absorbed into the M 23 C 6 carbide. Therefore, an amount of B segregating in the grain boundaries is reduced, resulting in a decrease in the grain boundary strength. Consequently, obtaining a sufficient creep ductility fails.
• the present inventors conducted further studies on a method for restricting the reduction in the amount of segregating B in grain boundaries in use under the high-temperature corrosive environment at 600 to 700°C. As a result, it was found that the following mechanism can be conceived.
• Mo restricts the formation of the M 23 C 6 carbide itself.
• Mo may be replaced with M being part of M 23 C 6 carbide, being dissolved into the M 23 C 6 carbide.
• the M 23 C 6 carbide with Mo dissolved therein is defined herein as "Mo-dissolved M 23 C 6 carbide”.
• the Mo-dissolved M 23 C 6 carbide resists allowing B to be dissolved therein.
• the present inventors conducted further studies on a chemical composition that can form Mo-dissolved M 23 C 6 carbide to restrict reduction in an amount of segregating B in grain boundaries even when MX carbo-nitride containing Nb transforms into a Z phase and an M 23 C 6 carbide in use under a high-temperature corrosive environment at 600 to 700°C. As a result, it was found that restricting the reduction in the amount of segregating B by the formation of the Mo-dissolved M 23 C 6 carbide has a close relation with B, C, and Mo in the chemical composition described above.
• the present inventors further conducted studies, and it was found as a result that, in a case where the above austenitic stainless steel contains Cu, an optional element, containing Cu at 5.0% or less makes it possible to obtain an excellent creep strength as well as to keep a creep ductility, but setting an upper limit of a content of Cu at 1.9% or less makes it possible to further enhance the creep strength as well as to keep a higher creep ductility.
• the reason is considered as follows. In use under a high-temperature corrosive environment, Cu precipitates in grains, forming Cu phases. The Cu phases enhance creep strength but can degrade creep ductility. Accordingly, for an austenitic stainless steel including the above chemical composition and satisfying Formula (1), it is more preferable that the content of Cu is 1.9% or less. When the content of Cu is 1.9% or less, it is possible to keep an excellent creep ductility more effectively.
• a content of Mo is set at 0.5% or more.
• Mo further segregates in grain boundaries and forms its intermetallic compounds in use under a high-temperature corrosive environment at 600 to 700°C. This grain-boundary segregation and intermetallic compounds further enhance the grain boundary strength.
• a lower limit of the content of Mo is preferably 0.5%.
• a lower limit of the content of Mo is preferably 0.8%, more preferably 1.0%, more preferably 2.0%.
• An austenitic stainless steel according to the present invention that is made based on the findings described above includes a chemical composition consisting of, in mass%, C: 0.030% or less, Si: 0.10 to 1.00%, Mn: 0.20 to 2.00%, P: 0.040% or less, S: 0.010% or less, Cr: 16.0 to 25.0%, Ni: 10.0 to 30.0%, Mo: 0.1 to 5.0%, Nb: 0.20 to 1.00%, N: 0.050 to 0.300%, sol.Al: 0.0005 to 0.1000%, B: 0.0010 to 0.0080%, Cu: 0 to 5.0%, W: 0 to 5.0%, Co: 0 to 1.0%, V: 0 to 1.00%, Ta: 0 to 0.2%, Hf: 0 to 0.20%, Ca: 0 to 0.010%, Mg: 0 to 0.010%, and rare earth metals: 0 to 0.10%, with the balance being Fe and impurities, and satisfying Formula (1): B + 0.004 ⁇ 0.9
• the chemical composition may contain one or more elements selected from the group consisting of, in mass%, Cu: 0.1 to 5.0%, W: 0.1 to 5.0%, and Co: 0.1 to 1.0%.
• the chemical composition may contain one or more elements selected from the group consisting of, in mass%, V: 0.1 to 1.00%, Ta: 0.01 to 0.2%, and Hf: 0.01 to 0.20%.
• the chemical composition may contain one or more elements selected from the group consisting of, in mass%, Ca: 0.0005 to 0.010%, Mg: 0.0005 to 0.010%, and rare earth metals: 0.001 to 0.10%.
• the chemical composition may contain, in mass%, Cu: 0 to 1.9%.
• the chemical composition may contain, in mass%, Mo: 0.5 to 5.0%.
• the austenitic stainless steel according to the present embodiment has a chemical composition containing the following elements.
• Carbon (C) is contained unavoidably.
• C When the austenitic stainless steel according to the present embodiment is in use under the high-temperature corrosive environment at 600 to 700°C, C produces M 23 C 6 carbide in grain boundaries, degrading polythionic acid SCC resistance. Accordingly, a content of C is 0.030% or less.
• An upper limit of the content of C is preferably 0.020%, more preferably 0.015%.
• the content of C is preferably as low as possible.
• a lower limit value of the content of C is preferably 0.0001%.
• Si deoxidizes steel.
• Si enhances oxidation resistance and steam oxidation resistance of steel.
• An excessively low content of Si fails to provide the effects described above.
• an excessively high content of Si causes a sigma phase ( ⁇ phase) to precipitate in steel, degrading toughness of the steel.
• a content of Si is 0.10 to 1.00%.
• An upper limit of the content of Si is preferably 0.75%, more preferably 0.50%.
• Mn Manganese deoxidizes steel. In addition, Mn stabilizes austenite, enhancing the creep strength. An excessively low content of Mn fails to provide the effects described above. Meanwhile, an excessively high content of Mn degrades creep strength of steel. Accordingly, a content of Mn is 0.20 to 2.00%. A lower limit of the content of Mn is preferably 0.40%, more preferably 0.50%. An upper limit of the content of Mn is preferably 1.70%, more preferably 1.50%.
• Phosphorus (P) is an impurity. P decreases hot workability and toughness of steel. Accordingly, a content of P is 0.040% or less. An upper limit of the content of P is preferably 0.035%, more preferably 0.032%. The content of P is preferably as low as possible. However, since P is contained unavoidably, at least 0.0001% of P can be contained in industrial production. Accordingly, a lower limit value of the content of P is preferably 0.0001%.
• S Sulfur
• S is an impurity. S degrades hot workability and creep ductility of steel. Accordingly, a content of S is 0.010% or less.
• An upper limit of the content of S is preferably 0.005%.
• the content of S is preferably as low as possible. However, since S is contained unavoidably, at least 0.0001% of S can be contained in industrial production. Accordingly, a lower limit value of the content of S is preferably 0.0001%.
• Chromium (Cr) enhances polythionic acid SCC resistance of steel.
• Cr enhances oxidation resistance, steam oxidation resistance, high-temperature corrosion resistance, and the like of steel.
• An excessively low content of Cr fails to provide the effects described above.
• an excessively high Cr content degrades creep strength and toughness of steel. Accordingly, a content of Cr is 16.0 to 25.0%.
• a lower limit of the content of Cr is preferably 16.5%, more preferably 17.0%.
• An upper limit of the content of Cr is preferably 24.0%, more preferably 23.0%.
• An excessively low content of Ni fails to provide the effect described above.
• an excessively high content of Ni results in saturation of the effect described above and in addition, increases production costs.
• a content of Ni is 10.0 to 30.0%.
• a lower limit of the content of Ni is preferably 11.0%, more preferably 13.0%.
• An upper limit of the content of Ni is preferably 25.0%, more preferably 22.0%.
• Molybdenum (Mo) restricts formation of M 23 C 6 carbide in grain boundaries in use under a high-temperature corrosive environment at 600 to 700°C.
• Mo restricts dissolution of B into M 23 C 6 carbide when MX carbo-nitride of Nb transforms into the M 23 C 6 carbide, restricting reduction of an amount of segregating B in grain boundaries under the high-temperature corrosive environment. This allows a sufficient creep ductility to be obtained in the high-temperature corrosive environment.
• An excessively low content of Mo fails to provide the effects described above. In contrast, an excessively high content of Mo degrades stability of austenite. Accordingly, a content of Mo is 0.1 to 5.0%. A lower limit of the content of Mo is preferably 0.2%, more preferably 0.3%.
• a lower limit of the content of Mo is more preferably 0.5%, still more preferably 0.8%, still more preferably 1.0%, still more preferably 1.5%, still more preferably 2.0%.
• a content of Mo of 1.5% or more also enhances creep strength.
• An upper limit of the content of Mo is preferably 4.5%, more preferably 4.0%.
• a content of Mo of 1.5% or more also enhances creep strength.
• Niobium (Nb) combines with C in use under a high-temperature corrosive environment at 600 to 700°C to form MX carbo-nitride, reducing an amount of dissolved C in steel. This enhances polythionic acid SCC resistance of the steel.
• the formed MX carbo-nitride of Nb also enhances creep strength.
• An excessively low content of Nb fails to provide the effects described above.
• an excessively high content of Nb causes ⁇ ferrite to be produced, degrading long-term creep strength, toughness, and weldability of steel.
• a content of Nb is 0.20 to 1.00%.
• a lower limit of the content of Nb is preferably 0.25%.
• An upper limit of the content of Nb is preferably 0.90%, more preferably 0.80%.
• N Nitrogen
• N is dissolved in a matrix (parent phase) to stabilize austenite, enhancing creep strength.
• N forms its fine carbo-nitride in grains, enhancing creep strength of steel. That is, N contributes to the creep strength through both solid-solution strengthening and precipitation strengthening.
• An excessively low content of N fails to provide the effects described above.
• an excessively high content of N causes Cr nitride to be formed in grain boundaries, degrading polythionic acid SCC resistance in a welding heat affected zone (HAZ).
• HZ welding heat affected zone
• an excessively high content of N also degrades workability of steel.
• a content of N is 0.050 to 0.300%.
• a lower limit of the content of N is preferably 0.070%.
• An upper limit of the content of N is preferably 0.250%, more preferably 0.200%.
• a content of Al is 0.0005 to 0.100%.
• a lower limit of the content of Al is preferably 0.001%, more preferably 0.002%.
• An upper limit of the content of Al is preferably 0.050%, more preferably 0.030%.
• the content of Al means a content of acid-soluble Al (sol.Al).
• B Boron (B) segregates in grain boundaries in use under a high-temperature corrosive environment at 600 to 700°C, enhancing grain boundary strength. As a result, creep ductility can be enhanced. An excessively low content of B fails to provide the effects described above. In contrast, an excessively high content of B degrades weldability and hot workability at high temperature. Accordingly, a content of B is 0.0010 to 0.0080%. A lower limit of the content of B is preferably 0.0015%, more preferably 0.0020%. An upper limit of the content of B is preferably less than 0.0060%, more preferably 0.0050%.
• the balance of the chemical composition of the austenitic stainless steel according to the present embodiment is Fe and impurities.
• the impurities mean elements that are mixed from ores and scraps used as raw material, a producing environment, or the like when the austenitic stainless steel is produced in an industrial manner, and are allowed to be mixed within ranges within which the impurities have no adverse effect on the austenitic stainless steel of the present embodiment.
• the austenitic stainless steel according to the present embodiment may further contain, in lieu of a part of Fe, one or more elements selected from the group consisting of Cu, W, and Co. These elements all enhance creep strength of steel.
• Copper (Cu) is an optional element and need not be contained.
• Cu precipitates in use under a high-temperature corrosive environment at 600 to 700°C in a form of Cu phases in grains, exerting precipitation strengthening to enhance creep strength of steel.
• an excessively high content of Cu degrades hot workability and weldability of steel.
• a content of Cu is 0 to 5.0%.
• a lower limit of the content of Cu is preferably 0.1%, more preferably 2.0%, more preferably 2.5%.
• An upper limit of the content of Cu is preferably 4.5%, more preferably 4.0%.
• the content of Cu is preferably 0 to 1.9%, and a more preferable upper limit of the content of Cu is 1.8%.
• Tungsten (W) is an optional element and may not be contained. When contained, W is dissolved in a matrix (parent phase), enhancing creep strength of steel. However, an excessively high content of W degrades stability of austenite, degrading creep strength and toughness of steel. Accordingly, a content of W is 0 to 5.0%. A lower limit of the content of W is preferably 0.1%, more preferably 0.2%. An upper limit of the content of W is preferably 4.5%, more preferably 4.0%.
• Co Co
• Co Cobalt
• a content of Co is 0 to 1.0%.
• a lower limit of the content of Co is preferably 0.1%, more preferably 0.2%.
• the austenitic stainless steel according to the present embodiment may further contain, in lieu of a part of Fe, one or more elements selected from the group consisting of V, Ta, and Hf. These elements all enhance polythionic acid SCC resistance and creep strength of steel.
• Vanadium (V) is an optional element and need not be contained. When contained, V combines with C to form its carbo-nitride in use under a high-temperature corrosive environment at 600 to 700°C, so as to reduce dissolved C, enhancing polythionic acid SCC resistance of steel. The formed V carbo-nitride also enhances creep strength. However, an excessively high content of V causes ⁇ ferrite to be produced, degrading creep strength, toughness, and weldability of steel. Accordingly, a content of V is 0 to 1.00%. In order to enhance the polythionic acid SCC resistance and the creep strength more effectively, a lower limit of the content of V is preferably 0.10%. An upper limit of the content of V is preferably 0.90%, more preferably 0.80%.
• Tantalum (Ta) is an optional element and need not be contained.
• Ta When contained, Ta combines with C to form its carbo-nitride in use under a high-temperature corrosive environment at 600 to 700°C, so as to reduce dissolved C, enhancing polythionic acid SCC resistance of steel.
• the formed Ta carbo-nitride also enhances creep strength.
• an excessively high content of Ta causes ⁇ ferrite to be produced, degrading creep strength, toughness, and weldability of steel. Accordingly, a content of Ta is 0 to 0.2%.
• a lower limit of the content of Ta is preferably 0.01%, more preferably 0.02%.
• Hafnium (Hf) is an optional element and need not be contained. When contained, Hf combines with C to form its carbo-nitride in use under a high-temperature corrosive environment at 600 to 700°C, so as to reduce dissolved C, enhancing polythionic acid SCC resistance of steel. The formed Hf carbo-nitride also enhances creep strength. However, an excessively high content of Hf causes ⁇ ferrite to be produced, degrading creep strength, toughness, and weldability of steel. Accordingly, a content of Hf is 0 to 0.20%. A lower limit of the content of Hf is preferably 0.01%, more preferably 0.02%.
• the austenitic stainless steel according to the present embodiment may further contain, in lieu of a part of Fe, one or more elements selected from the group consisting of Ca, Mg, and rare earth metals. These elements all enhance hot workability and creep ductility of steel.
• Ca is an optional element and need not be contained. When contained, Ca immobilizes O (oxygen) and S (sulfur) in forms of its inclusions, enhancing hot workability and creep ductility of steel. However, an excessively high content of Ca degrades hot workability and creep ductility of steel. Accordingly, a content of Ca is 0 to 0.010%. A lower limit of the content of Ca is preferably 0.0005%, more preferably 0.001%. An upper limit of the content of Ca is preferably 0.008%, more preferably 0.006%.
• Mg Magnesium
• Mg is an optional element and need not be contained. When contained, Mg immobilizes O (oxygen) and S (sulfur) in forms of its inclusions, enhancing hot workability and creep ductility of steel. However, an excessively high content of Mg degrades hot workability and long-term creep ductility of steel. Accordingly, a content of Mg is 0 to 0.010%. A lower limit of the content of Mg is preferably 0.0005%, more preferably 0.001%. An upper limit of the content of Mg is preferably 0.008%, more preferably 0.006%.
• Rare earth metals 0 to 0.10%
• Rare earth metals are optional elements and need not be contained. When contained, REMs immobilize O (oxygen) and S (sulfur) in forms of its inclusions, enhancing hot workability and creep ductility of steel. However, an excessively high content of REMs degrades hot workability and long-term creep ductility of steel. Accordingly, a content of REMs is 0 to 0.01%. A lower limit of the content of REMs is preferably 0.001%, more preferably 0.002%. An upper limit of the content of REMs is preferably 0.08%, more preferably 0.06%.
• REMs herein contain at least one element of Sc, Y, and lanthanoid (La, with atomic number 57, to Lu, with atomic number 71), and the content of REMs means a total content of these elements.
• the present embodiment involves both setting the content of C at 0.030% or less to increase the polythionic acid SCC resistance, and making 0.20 to 1.00% of Nb contained to produce MX carbo-nitride of Nb in use under a high-temperature corrosive environment at 600 to 700°C, reducing an amount of dissolved C.
• the MX carbo-nitride of Nb transforms into a Z phase and an M 23 C 6 carbide in use under the above high-temperature use environment because the MX carbo-nitride of Nb is a metastable phase. B segregating in grain boundaries is dissolved in the M 23 C 6 carbide, and an amount of segregating B in the grain boundaries is reduced. As a result, the creep ductility deteriorates.
• F1 is an index indicating a ratio of an Mo-dissolved M 23 C 6 carbide to a plurality of kinds of M 23 C 6 carbides formed in steel in use under a high-temperature corrosive environment. If F1 is zero or more, the ratio of the Mo-dissolved M 23 C 6 carbide is high even when the plurality of kinds of M 23 C 6 carbides are formed in the steel in use under the high-temperature corrosive environment. Therefore, B segregating in grain boundaries is hard to be dissolved in the M 23 C 6 carbides, and therefore an amount of B segregating in the grain boundaries is kept.
• F1 is zero (0.00000) or more.
• F1 is preferably 0.00100 or more, more preferably 0.00200 or more, more preferably 0.00400 or more, more preferably 0.00500 or more, more preferably 0.00800 or more, most preferably 0.01000 or more.
• the upper limit of the content of Cu is 1.9% or less as described above.
• the content of Cu is preferably 0% to 1.9%.
• the content of Cu is 1.9% or less, a Cu phase is subjected to precipitation strengthening, which makes it possible to keep the excellent creep ductility with the excellent creep strength obtained.
• a lower limit of the content of Mo is preferably 0.5%.
• Mo additionally segregates in grain boundaries and forms intermetallic compounds. This grain-boundary segregation and intermetallic compounds further enhance the grain boundary strength. As a result, the creep ductility is further enhanced.
• the lower limit of the content of Mo is preferably 1.0%. Note that, when the lower limit of the content of Mo is 1.0% or more, an F1 value is preferably 0.00500 or more, more preferably 0.00800 or more, more preferably 0.01000 or more.
• the present producing method includes a preparation process of preparing a starting material, a hot working process of performing hot working on the starting material to produce a steel material, a cold working process of, as necessary, performing cold working on the steel material subjected to the hot working, and a solution treatment process of, as necessary, performing solution treatment on the steel material.
• the producing method will be described below.
• a molten steel having the above chemical composition and satisfying Formula (1) is produced.
• the molten steel is produced using, for example, an electric furnace, an AOD (Argon Oxygen Decarburization) furnace, or a VOD (Vacuum Oxygen Decarburization) furnace.
• the produced molten steel is subjected to a well-known degassing treatment.
• a starting material is produced from the molten steel subjected to the degassing treatment.
• Examples of the producing method for the starting material include a continuous casting process.
• a continuous casting material (the starting material) is produced.
• the continuous casting material is, for example, a slab, a bloom, a billet, and the like.
• the molten steel may be subjected to an ingot-making process into an ingot.
• the prepared starting material (a continuous casting material or an ingot) is subjected to hot working to be produced into an austenitic stainless steel material.
• the starting material is subjected to the hot rolling to be produced into a steel plate, a steel bar, or a wire rod.
• the starting material is subjected to hot-extrusion process, hot piercing-rolling, or the like to be produced into an austenitic stainless steel pipe.
• a specific method of the hot working is not specially limited, and performing hot working conforming to a shape of a finished product will suffice.
• a finish working temperature of the hot working is, for example, 1050°C or more.
• the finish working temperature used herein means a temperature of the steel material immediately after completion of final hot working.
• Cold working may be performed, as necessary, on the austenitic stainless steel material subjected to the hot working.
• the austenitic stainless steel material is a steel bar, a wire rod, or a steel pipe
• the cold working is, for example, cold drawing or cold rolling.
• the austenitic stainless steel material is a steel plate, the cold working is cold rolling or the like.
• solution treatment may be performed as necessary.
• a solution treatment step involves uniformizing a structure and dissolving a carbo-nitride.
• a preferable solution treatment temperature is as follows.
• Preferable solution treatment temperature 1000 to 1250°C
• solution treatment temperature is 1000°C or more, a carbo-nitride of Nb is dissolved sufficiently, further increasing the creep strength.
• solution treatment temperature is 1250°C or less, excessive dissolution of C can be restricted, further increasing the polythionic acid SCC resistance.
• a retention duration in the solution treatment at the above solution treatment temperature is, for example but not specially limited to, 2 minutes to 60 minutes.
• a finish working temperature of the hot working is preferably set at 1000°C or more.
• the finish hot working temperature is 1000°C or more, the carbo-nitride of Nb is dissolved sufficiently, which makes it possible to establish compatibility between an excellent polythionic acid SCC resistance and an excellent creep ductility in use under a high-temperature corrosive environment at 600 to 700°C, and the carbo-nitride of Nb is formed in use under a high temperature environment, which allows a sufficient creep strength to be obtained.
• a shape of the austenitic stainless steel of the present embodiment is not specially limited.
• the austenitic stainless steel of the present embodiment may be a steel plate, a steel pipe, a steel bar or a wire rod, or a shape steel.
• the molten steels were used to produce ingots each having an outer diameter of 120 mm and weighing 30 kg.
• the ingots were subjected to hot forging to be formed into steel plates each having a thickness of 40 mm.
• the steel plates were further subjected to the hot rolling into steel plates each having a thickness of 15 mm.
• Final working temperatures of the hot rolling was 1050°C or more for all test numbers.
• the steel plates subjected to the hot rolling were further subjected to the cold rolling to be produced into steel plates each having a thickness of 10.5 mm, a width of 50 mm, and a length of 100 mm.
• the steel plates subjected to the cold rolling were each subjected to the solution treatment.
• the solution treatment temperature was 1150°C, and a solution treatment duration was 10 minutes.
• the steel plates subjected to the solution treatment were subjected to water cooling. Through the above steps, austenitic stainless steel materials were produced.
• t thickness of a produced austenitic stainless steel plate defined as t (mm)
• a sample taken from a position at t/4 depth from a surface of the steel plate was used to perform well-known component analysis methods (the infrared absorptiometric method after combustion for C and S, the thermal desorption spectroscopy for N, and the ICP spectrometry for other alloying elements).
• component analysis methods the infrared absorptiometric method after combustion for C and S, the thermal desorption spectroscopy for N, and the ICP spectrometry for other alloying elements.
• the steel plates of the respective test numbers were subjected to a 5000-hour aging treatment at 600°C on the assumption that they are used under the high temperature environment. From these aging-treated materials, plate-shaped test specimens were taken, the test specimens each having a thickness of 2 mm, a width of 10 mm, and a length of 75 mm.
• An evaluation test for polythionic acid SCC resistance was conducted conforming to "Stress corrosion cracking test in chloride solution for stainless steels" in JIS G 0576(2001). Specifically, each test specimen was bended around a punch having an inside radius of 5 mm to have a U-bend shape.
• test specimen with the U-bend shape was immersed in Wackenroder solution (solution made by blowing a large quantity of H 2 S gas into H 2 SO 3 saturated aqueous solution that is made by blowing SO 2 gas into distilled water) at normal temperature for 100 hours.
• Wackenroder solution solution made by blowing a large quantity of H 2 S gas into H 2 SO 3 saturated aqueous solution that is made by blowing SO 2 gas into distilled water
• the immersed test specimen was subjected to microscopic observation at 500x magnification to check for a crack.
• test specimen When no crack was found in a test specimen, the test specimen was determined to be excellent in polythionic acid SCC resistance (marked as "E” (Excellent) in a column “POLYTHIONIC ACID SCC RESISTANCE” in Table 2). When any crack was found in a test specimen, the test specimen was determined to be low in polythionic acid SCC resistance (marked as "NA” (Not Accepted) in the column “POLYTHIONIC ACID SCC RESISTANCE” in Table 2).
• a creep rupture test specimen conforming to JIS Z2271(2010) was fabricated from the steel plate.
• a cross section of the creep rupture test specimen perpendicular to its axial direction was in a round shape, and the creep rupture test specimen had an outer diameter of 6 mm and a parallel portion measuring 30 mm. The parallel portion was parallel to a rolling direction of the steel plate.
• the fabricated creep rupture test specimen was used to conduct a creep rupture test conforming to JIS Z2271(2010). Specifically, the creep rupture test specimen was heated at 750°C and then subjected to the creep rupture test. A test stress was set at 45 MPa, and a creep rupture time (hour) and a percentage reduction of area after creep rupture (%) were determined.
• the test specimen when a creep rupture time of a test specimen was 5000 to 10000 h or less, the test specimen was determined to be excellent in creep strength (marked as "G” (Good) in a column “CREEP STRENGTH” in Table 2). When a creep rupture time of a test specimen was more than 10000 hours, the test specimen was determined to be markedly excellent in creep strength (marked as “E” (Excellent) in the column “CREEP STRENGTH” in Table 2). When a creep rupture time of a test specimen was less than 5000 hours, the test specimen was determined to be low in creep strength (marked as "NA” (Not Accepted) in the column “CREEP STRENGTH” in Table 2). When a test specimen was marked as "G” or “E” in creep rupture time, it was determined that a sufficient creep strength was obtained with the test specimen.
• the test specimen As to the creep ductility, when a percentage reduction of area after creep rupture of a test specimen was 20.0% to 30.0% or less, the test specimen was determined to be good in creep ductility (marked as "P" (Passing) in a column “CREEP DUCTILITY” in Table 2). When a percentage reduction of area after creep rupture of a test specimen was more than 30.0% to 50.0% or less, the test specimen was determined to be excellent in creep ductility (marked as "G” (Good) in the column “CREEP DUCTILITY” in Table 2).
• test specimen When a percentage reduction of area after creep rupture of a test specimen was more than 50.0%, the test specimen was determined to be markedly excellent in creep ductility (marked as “E” (Excellent) in the column “CREEP DUCTILITY” in Table 2). When a percentage reduction of area after creep rupture of a test specimen was less than 20.0%, the test specimen was determined to be low in creep ductility (marked as "NA” (Not Accepted) in the column “CREEP DUCTILITY” in Table 2). When a test specimen was marked as "P”, “G”, or “E” in percentage reduction of area after creep rupture, it was determined that a sufficient creep ductility was obtained with the test specimen.
• the contents of elements in the chemical compositions of the steels of the test numbers 1 to 16 were appropriate, and F1 of the steels satisfied Formula (1). Therefore, the steel plates of these test numbers provided excellent polythionic acid SCC resistances.
• the rupture times of the steel plates were 5000 hours or more, and excellent creep strengths were obtained.
• their percentage reductions of area after creep rupture were 20.0% or more, and excellent creep ductilities were obtained.
• test numbers 2 to 4, 6 to 12, and 15, since they contained Cu or contained Mo in a large quantity since they contained Cu or contained Mo in a large quantity, their rupture times in the creep rupture test was longer than those of test numbers 1, 5, 13, 14, and 16, 10000 hours or more, and superior creep strengths were obtained.
• test numbers 3 and 4 which contained Cu at 1.9% or less and contained Mo at 0.5% or more
• test numbers 5 to 7, 11, and 12 which did not contain Cu but contained Mo at 1.0% or more
• sufficient creep strengths were obtained, and at the same time, superior creep ductilities were obtained.
• test number 23 As to a test number 23, it contained no Nb. As a result, its polythionic acid SCC resistance was low. In addition, its rupture time was less than 5000 hours, and a creep strength of its steel was low.

Landscapes

• Chemical & Material Sciences (AREA)
• Engineering & Computer Science (AREA)
• Materials Engineering (AREA)
• Mechanical Engineering (AREA)
• Metallurgy (AREA)
• Organic Chemistry (AREA)
• Physics & Mathematics (AREA)
• Thermal Sciences (AREA)
• Crystallography & Structural Chemistry (AREA)
• Heat Treatment Of Steel (AREA)

Applications Claiming Priority (2)

Publications (2)

Family

ID=61300959

Family Applications (1)

Country Status (8)

Cited By (1)

Families Citing this family (13)

Family Cites Families (18)

• 2017
  • 2017-08-30 JP JP2018537347A patent/JP6904359B2/ja active Active
  • 2017-08-30 WO PCT/JP2017/031157 patent/WO2018043565A1/fr unknown
  • 2017-08-30 KR KR1020197008697A patent/KR102223549B1/ko active IP Right Grant
  • 2017-08-30 SG SG11201901278XA patent/SG11201901278XA/en unknown
  • 2017-08-30 EP EP17846569.6A patent/EP3508602A4/fr active Pending
  • 2017-08-30 US US16/328,755 patent/US20190194787A1/en active Pending
  • 2017-08-30 CN CN201780052637.7A patent/CN109642291B/zh active Active
  • 2017-08-30 CA CA3035162A patent/CA3035162C/fr active Active

Also Published As

Similar Documents

Legal Events