CN117568705A - Heat-resistant steel for high-temperature turbine rotor forging and preparation method thereof - Google Patents
Heat-resistant steel for high-temperature turbine rotor forging and preparation method thereof Download PDFInfo
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- CN117568705A CN117568705A CN202210945050.1A CN202210945050A CN117568705A CN 117568705 A CN117568705 A CN 117568705A CN 202210945050 A CN202210945050 A CN 202210945050A CN 117568705 A CN117568705 A CN 117568705A
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 43
- 239000010959 steel Substances 0.000 title claims abstract description 43
- 238000005242 forging Methods 0.000 title claims abstract description 34
- 238000002360 preparation method Methods 0.000 title abstract description 8
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 9
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 9
- 239000012535 impurity Substances 0.000 claims abstract description 8
- 229910052727 yttrium Inorganic materials 0.000 claims abstract description 8
- 229910052729 chemical element Inorganic materials 0.000 claims abstract description 7
- 238000005496 tempering Methods 0.000 claims description 21
- 238000010438 heat treatment Methods 0.000 claims description 14
- 238000010791 quenching Methods 0.000 claims description 14
- 230000000171 quenching effect Effects 0.000 claims description 14
- 238000000034 method Methods 0.000 claims description 10
- 238000003723 Smelting Methods 0.000 claims description 7
- 238000001816 cooling Methods 0.000 claims description 7
- 238000007670 refining Methods 0.000 claims description 7
- 238000007711 solidification Methods 0.000 claims description 7
- 230000008023 solidification Effects 0.000 claims description 7
- 238000011282 treatment Methods 0.000 claims description 7
- 238000009849 vacuum degassing Methods 0.000 claims description 7
- 239000002994 raw material Substances 0.000 claims description 3
- 238000004519 manufacturing process Methods 0.000 claims description 2
- 239000000463 material Substances 0.000 abstract description 23
- 230000003647 oxidation Effects 0.000 abstract description 15
- 238000007254 oxidation reaction Methods 0.000 abstract description 15
- 239000010949 copper Substances 0.000 description 9
- 230000007774 longterm Effects 0.000 description 4
- 238000003754 machining Methods 0.000 description 4
- 230000008569 process Effects 0.000 description 4
- 238000005728 strengthening Methods 0.000 description 4
- 238000005266 casting Methods 0.000 description 3
- 229910052802 copper Inorganic materials 0.000 description 3
- 239000007789 gas Substances 0.000 description 3
- 229910052748 manganese Inorganic materials 0.000 description 3
- 239000000126 substance Substances 0.000 description 3
- 230000004584 weight gain Effects 0.000 description 3
- 235000019786 weight gain Nutrition 0.000 description 3
- CURLTUGMZLYLDI-UHFFFAOYSA-N Carbon dioxide Chemical compound O=C=O CURLTUGMZLYLDI-UHFFFAOYSA-N 0.000 description 2
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 2
- 230000008901 benefit Effects 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000012986 modification Methods 0.000 description 2
- 230000004048 modification Effects 0.000 description 2
- 229910052750 molybdenum Inorganic materials 0.000 description 2
- 229910052758 niobium Inorganic materials 0.000 description 2
- 238000010248 power generation Methods 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 238000006467 substitution reaction Methods 0.000 description 2
- 229910000859 α-Fe Inorganic materials 0.000 description 2
- 230000009286 beneficial effect Effects 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 229910002092 carbon dioxide Inorganic materials 0.000 description 1
- 239000001569 carbon dioxide Substances 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 239000003245 coal Substances 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 230000003009 desulfurizing effect Effects 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 238000009661 fatigue test Methods 0.000 description 1
- 239000012530 fluid Substances 0.000 description 1
- 239000002737 fuel gas Substances 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 239000003921 oil Substances 0.000 description 1
- 230000002085 persistent effect Effects 0.000 description 1
- 229910052761 rare earth metal Inorganic materials 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J5/00—Methods for forging, hammering, or pressing; Special equipment or accessories therefor
- B21J5/002—Hybrid process, e.g. forging following casting
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/007—Heat treatment of ferrous alloys containing Co
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/0068—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for particular articles not mentioned below
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
-
- 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
- C22C38/005—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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
-
- 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
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
- F01D—NON-POSITIVE DISPLACEMENT MACHINES OR ENGINES, e.g. STEAM TURBINES
- F01D5/00—Blades; Blade-carrying members; Heating, heat-insulating, cooling or antivibration means on the blades or the members
- F01D5/12—Blades
- F01D5/28—Selecting particular materials; Particular measures relating thereto; Measures against erosion or corrosion
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- General Engineering & Computer Science (AREA)
- Turbine Rotor Nozzle Sealing (AREA)
Abstract
The invention provides heat-resistant steel for a high-temperature turbine rotor forging, which comprises the following chemical elements in percentage by mass: c:0.11-0.17%, si:0.02-0.095%, mn:0.22-0.5%, cr:10.6-11.8%, co:2.5-2.9%, mo:0.01-0.18%, W:2.55-3.4%, V:0.12-0.39%, nb:0.03-0.07%, ni:0.12-0.29%, cu:0.3-0.7%, B:0.019-0.035%, N:0.012-0.035%, Y:0-0.5%, and the balance of Fe and unavoidable impurities. The invention also provides a preparation method of the heat-resistant steel and application of the heat-resistant steel in turbine machinery. Compared with the prior art, the forging prepared from the material has excellent high-temperature endurance strength, low-cycle fatigue performance and oxidation resistance, and can completely meet the use requirement of a high-temperature turbine rotor with the working temperature of 650 ℃ and below. The forging preparation method is simple to operate and easy to implement and produce.
Description
Technical Field
The invention relates to the technical field of metal materials, in particular to heat-resistant steel for a high-temperature turbine rotor forging and a preparation method thereof.
Background
The turbine machine is a machine for converting energy in fluid working medium into mechanical work, and the working medium of the turbine machine can be steam, fuel gas, air and other gases, or water, oil and other liquids. Generally, for a turbomachine in which a working medium is gas, the higher the temperature and pressure of the working medium gas, the higher the energy conversion efficiency of the turbomachine, but at the same time, the higher requirements are put on the performance of parts of the turbomachine, particularly parts in which the working temperature is high.
In particular, for thermal power generation, steam turbines are key components for converting steam thermal energy into mechanical work. The increase of the steam temperature and pressure can improve the power generation efficiency, reduce the coal consumption and reduce the CO 2 、NO X 、SO X And the like, has obvious economic and social benefits. In the last decades, the steam parameters of turbines have been increased from subcritical, supercritical to supercritical parameters at the 620 ℃ and 630 ℃ level, and are currently being developed towards higher temperature level turbine sets. The steam temperature of the steam turbine is improved, the working environment of high-temperature parts is further deteriorated, and higher requirements are put on the high-temperature strength and high-temperature oxidation resistance of the material. In addition, with the proposal of concepts such as multi-energy complementation and the like, new energy power supply is gradually increased, and thermal power becomes an important backing and peak shaving power supply, so that greater requirements are put forward on the flexibility of operation of the thermal power turbine, and the fatigue performance of key parts of the turbine, particularly the low-cycle fatigue performance of a rotor forging, is an important factor for influencing the flexibility and the safety of a unit.
At present, the forging prepared from the existing material cannot have good high-temperature strength, low-cycle fatigue performance and oxidation resistance, so that further research is needed.
Disclosure of Invention
In view of the above-mentioned drawbacks, an object of the present invention is to provide a heat-resistant steel for high-temperature turbine rotor forgings, which has excellent high-temperature strength, low-cycle fatigue property and oxidation resistance, and can meet the use requirements of turbine mechanical forgings with working temperatures of 650 ℃ and below.
The invention provides heat-resistant steel for a high-temperature turbine rotor forging, which comprises the following chemical elements in percentage by mass: c:0.11-0.17%, si:0.02-0.095%, mn:0.22-0.5%, cr:10.6-11.8%, co:2.5-2.9%, mo:0.01-0.18%, W:2.55-3.4%, V:0.12-0.39%, nb:0.03-0.07%, ni:0.12-0.29%, cu:0.3-0.7%, B:0.019-0.035%, N:0.012-0.035%, Y:0-0.5%, and the balance of Fe and unavoidable impurities.
Preferably, the heat-resistant steel comprises the following chemical elements in percentage by mass: c:0.12-0.15%, si:0.02-0.045%, mn:0.25-0.35%, cr:10.9-11.1%, co:2.65-2.85%, mo:0.01-0.09%, W:3.05-3.35%, V:0.31-0.37%, nb:0.04-0.06%, ni:0.12-0.24%, cu:0.45-0.65%, B:0.019-0.027%, N:0.0155-0.029%, Y:0-0.5%, and the balance of Fe and unavoidable impurities.
Preferably, the mass percentage of the Y is 0.26-0.34%.
The invention also provides a preparation method of the heat-resistant steel, which comprises the following steps: raw materials are weighed according to element proportion and mixed, and then are poured into an electrode rod after smelting, ladle refining and vacuum degassing, the electrode rod is subjected to electroslag remelting treatment and cooling solidification to form a steel ingot, and the steel ingot is forged into a turbine rotor type blank and is subjected to heat treatment.
Preferably, the heat treatment includes one quenching and two tempering processes.
Preferably, the quenching temperature is 1100-1150 ℃, the first tempering temperature is 580-660 ℃, and the second tempering temperature is 670-730 ℃.
The invention also provides the application of the heat-resistant steel in turbomachinery.
Preferably, the turbomachine is a steam turbine.
Compared with the prior art, the invention has the following beneficial effects:
the C element ensures the hardenability of the steel, promotes the martensitic transformation, is an important element for carbide formation, and can improve the strength of the steel; however, excessive C element can reduce the toughness of the material, and is unfavorable for low cycle fatigue performance. Therefore, the C content is 0.11 to 0.17%, more preferably 0.12 to 0.15%.
Si and Mn are deoxidizers and desulfurizing agents in molten steel, si can improve the oxidation resistance of the material, and Mn can improve the hardenability and strength of the steel; however, si and Mn decrease the plasticity and toughness of the material, and therefore, si content is 0.02 to 0.095%, mn content is 0.22 to 0.50%, more preferably Si content is 0.02 to 0.045%, mn content is 0.25 to 0.35%.
Cr is an important element for providing oxidation resistance of steel and is also an important element for forming carbide; however, when Cr content is too high, delta ferrite is easy to generate, Z phase is easy to generate after long-term service, and the long-term high-temperature strength of the material is reduced. Thus, the Cr content is 10.6 to 11.8%, more preferably 10.9 to 11.1%.
Co is an important solid solution strengthening element, and can inhibit the formation of delta ferrite; however, excessive Co content can promote coarsening of carbide and reduce low cycle fatigue performance of the material. Therefore, the Co content is 2.5-2.9%, more preferably 2.65-2.85%.
Mo and W are two important solid solution strengthening elements, and play an important role in the high-temperature strength of the material; however, excessive addition of Mo content can form large primary carbide, so that the low cycle fatigue performance of the material is reduced, and excessive W content can reduce the manufacturability of the material, and segregation is easy in the manufacturing process. Therefore, the Mo content is 0.01-0.18%, the W content is 2.55-3.4%, more preferably the Mo content is 0.01-0.09%, and the W content is 3.05-3.35%.
V and Nb are important forming elements of fine and dispersed carbonitrides in steel, and increase the high-temperature strength of the material; however, if the V content is too high, the toughness of the material is reduced, and if the Nb content is too high, coarse primary NbC phases are easily formed, and the low cycle fatigue performance of the material is reduced. Accordingly, the V content is 0.12 to 0.39%, the Nb content is 0.03 to 0.07%, more preferably the V content is 0.31 to 0.37%, and the Nb content is 0.04 to 0.06%.
Ni can increase the hardenability of the material, and has important influence on the toughness of the material; however, too high Ni content reduces the high temperature long-term strength of the material. Thus, the Ni content is 0.12 to 0.29%, more preferably 0.12 to 0.24%.
Cu can form a copper-rich phase in dispersion distribution, so that the high-temperature strength and the low-cycle fatigue performance of the material are improved; however, too high a Cu content, coarsening of the copper-rich phase reduces the strengthening effect and reduces the plasticity of the material. Therefore, the Cu content is 0.3 to 0.7%, more preferably 0.45 to 0.65%.
B can inhibit the growth of carbide in grain boundary, improve the high-temperature long-term strength of the material, N is an important forming element of fine dispersed carbonitride in steel, and can improve the strength and low-cycle fatigue performance of the material; however, too high B and N contents form coarse BN phases, which lower the low cycle fatigue properties. Accordingly, the B content is 0.019 to 0.035%, the N content is 0.012 to 0.035%, more preferably the B content is 0.019 to 0.027%, and the N content is 0.0155 to 0.029%.
Y is a rare earth element, and the oxidation resistance, strength and low cycle fatigue performance of the material can be further improved by adding trace Y element; however, the addition of the Y content is excessive, and the strengthening effect is weakened. Therefore, the Y content is 0 to 0.5%, more preferably 0.26 to 0.34%.
Compared with the prior art, the forging prepared from the material has excellent high-temperature endurance strength, low-cycle fatigue performance and oxidation resistance, and can completely meet the use requirement of a high-temperature turbine rotor with the working temperature of 650 ℃ and below. The forging preparation method is simple to operate and easy to implement and produce.
Drawings
FIG. 1 is a graph comparing the oxidation weight gain at 650℃with the oxidation weight gain of 13Cr9Mo2Co1NiVNbNB at 620℃for four examples of this invention.
Detailed Description
The following describes the embodiments of the present invention in further detail with reference to the accompanying drawings. These embodiments are merely illustrative of the present invention and are not intended to be limiting.
The following specific examples are presented to illustrate the present invention, and those skilled in the art will readily appreciate the additional advantages and capabilities of the present invention as disclosed herein. The invention may be practiced or carried out in other embodiments and details within the scope and range of equivalents of the specific embodiments and ranges of equivalents, without departing from the spirit of the invention.
The invention provides heat-resistant steel for a high-temperature turbine rotor forging, which comprises the following chemical elements in percentage by mass: c:0.11-0.17%, si:0.02-0.095%, mn:0.22-0.5%, cr:10.6-11.8%, co:2.5-2.9%, mo:0.01-0.18%, W:2.55-3.4%, V:0.12-0.39%, nb:0.03-0.07%, ni:0.12-0.29%, cu:0.3-0.7%, B:0.019-0.035%, N:0.012-0.035%, Y:0-0.5%, and the balance of Fe and unavoidable impurities.
Preferably, the heat-resistant steel comprises the following chemical elements in percentage by mass: c:0.12-0.15%, si:0.02-0.045%, mn:0.25-0.35%, cr:10.9-11.1%, co:2.65-2.85%, mo:0.01-0.09%, W:3.05-3.35%, V:0.31-0.37%, nb:0.04-0.06%, ni:0.12-0.24%, cu:0.45-0.65%, B:0.019-0.027%, N:0.0155-0.029%, Y:0-0.5%, and the balance of Fe and unavoidable impurities.
Further, the preferable mass percentage of Y is 0.26-0.34%.
Based on the total mass of the heat-resistant steel, the main component of the impurities is less than or equal to 0.015 percent, and the S is less than or equal to 0.01 percent.
The invention also provides a preparation method for preparing the turbine rotor forging, which comprises the following steps: raw materials are weighed according to element proportion and mixed, and then are poured into an electrode rod after arc furnace smelting, ladle refining and vacuum degassing, the electrode rod is subjected to electroslag remelting treatment and cooling solidification to form a steel ingot, and the steel ingot is forged into a turbine rotor type blank and is subjected to heat treatment. The heat treatment comprises a primary quenching and a secondary tempering process. Wherein the quenching temperature is 1100-1150 ℃, the first tempering temperature is 580-660 ℃, and the second tempering temperature is 670-730 ℃.
The invention provides chemical components of 4 example forgings and comparative example 13Cr9Mo2Co1NiVNbNB (disclosed by Chinese patent No. CN 103074550B), wherein the chemical components are calculated by mass percent, and the balance is Fe. See table 1.
Table 1 forging chemical composition analysis results (wt.%)
Example 1
Mixing 0.115% of C,0.086% of Si,0.24% of Mn,11.43% of Cr,2.76% of Co,0.025% of Mo,3.29% of W,0.22% of V,0.06% of Nb,0.27% of Ni,0.63% of Cu,0.021% of B,0.0319% of N,0.45% of Y and the balance of Fe in percentage by mass, smelting in an arc furnace, ladle refining and vacuum degassing, and casting into an electrode rod, wherein the electrode rod is subjected to electroslag remelting treatment and cooling solidification to form a steel ingot; the steel ingot is manufactured into a 25-ton thermal power steam turbine rotor forging through a series of procedures of forging, heat treatment, machining and the like, and the maximum diameter reaches 1.1 m.
Wherein, the heat treatment comprises a primary quenching and a secondary tempering, the quenching temperature is 1110 ℃, the primary tempering temperature is 600 ℃, and the secondary tempering temperature is 690 ℃.
Example 2
Mixing 0.132% of C,0.044% of Si,0.32% of Mn,11.05% of Cr,2.84% of Co,0.078% of Mo,3.11% of W,0.33% of V,0.04% of Nb,0.14% of Ni,0.52% of Cu,0.024% of B,0.0161% of N,0.27% of Y and the balance of Fe in percentage by mass, smelting in an arc furnace, ladle refining and vacuum degassing, and casting into an electrode rod, wherein the electrode rod is subjected to electroslag remelting treatment and cooling solidification to form a steel ingot; the steel ingot is manufactured into a 1 ton supercritical carbon dioxide rotor forging through a series of procedures such as forging, heat treatment, machining and the like, and the outer diameter of the steel ingot is 0.4 meter.
Wherein, the heat treatment comprises a primary quenching and a secondary tempering, the quenching temperature is 1140 ℃, the primary tempering temperature is 620 ℃, and the secondary tempering temperature is 710 ℃.
Example 3
According to mass percent, 0.145 percent of C,0.025 percent of Si,0.43 percent of Mn,10.73 percent of Cr,2.57 percent of Co,0.153 percent of Mo,2.81 percent of W,0.29 percent of V,0.05 percent of Nb,0.21 percent of Ni,0.39 percent of Cu,0.033 percent of B,0.0239 percent of N,0.33 percent of Y and the balance of Fe are mixed in proportion, and then are subjected to arc furnace smelting, ladle refining and vacuum degassing, and then are poured into electrode bars, and the electrode bars are subjected to electroslag remelting treatment and cooling solidification to form steel ingots; the steel ingot is manufactured into a 2-ton industrial turbine rotor forging through a series of procedures of forging, heat treatment, machining and the like, and the outer diameter of the steel ingot is 0.6 meter.
Wherein, the heat treatment comprises a primary quenching process and a secondary tempering process, the quenching temperature is 1120 ℃, the primary tempering temperature is 610 ℃, and the secondary tempering temperature is 700 ℃.
Example 4
Mixing 0.16% of C,0.035% of Si,0.28% of Mn,10.92% of Cr,2.88% of Co,0.045% of Mo,3.18% of W,0.37% of V,0.053% of Nb,0.18% of Ni,0.46% of Cu,0.027% of B,0.0138% of N and the balance of Fe in percentage by mass, smelting by an arc furnace, refining by a ladle, vacuum degassing, casting into an electrode rod, and carrying out electroslag remelting treatment, cooling and solidification on the electrode rod to form a steel ingot; the steel ingot is manufactured into a 2.4 ton air turbine rotor forging through a series of procedures such as forging, heat treatment, machining and the like, and the outer diameter of the steel ingot is 0.8 meter.
Wherein, the heat treatment comprises a primary quenching and a secondary tempering, the quenching temperature is 1130 ℃, the primary tempering temperature is 590 ℃, and the secondary tempering temperature is 720 ℃.
Table 2 shows the room temperature mechanical properties (including yield strength R) of the forgings of examples 1-4 of the invention p0.2 Tensile strength R m Elongation after break a, reduction of area Z). As can be seen from a combination of Table 2 and CN103074550B, the forgings provided in examples 1-4 of the present invention had room temperature strength and plasticity without 13Cr9Mo2Co1 NiVNbNB.
Table 2 mechanical properties of forgings at room temperature
Table 3 shows the high temperature durability of the forgings of examples 1-4 of the present invention at 650℃ for 10 ten thousand hours extrapolated based on durability test data. As is clear from Table 3, the high-temperature durability of examples 1 to 4 of the present invention at 650℃for 10 ten thousand hours all reached 115MPa or more, and the present invention has excellent high-temperature durability.
TABLE 3 persistent Properties of the inventive examples
Table 4 shows the results of the low cycle fatigue test of the forgings of examples 1 to 4 of the present invention at room temperature and 650. DegreeCit is clear from Table 4 that examples 1 to 4 of the present invention have excellent low cycle fatigue properties at both the room temperature and 650. DegreeCt.
TABLE 4 Low cycle fatigue Properties (cycle)
As shown in FIG. 1, the forgings of examples 1-4 were subjected to steam oxidation tests at 650 ℃ for different oxidation times (100 h, 500h, 1000h and 2000 h), and under the same oxidation time conditions, the oxidation weight gain of the forgings of examples 1-4 was lower than that of 13Cr9Mo2Co1NiVNbNB in a 620 ℃ steam environment. From this, it can be seen that the forgings of examples 1 to 4 of the present invention have excellent steam oxidation resistance at 650 ℃.
The foregoing is merely a preferred embodiment of the present invention, and it should be noted that modifications and substitutions can be made by those skilled in the art without departing from the technical principles of the present invention, and these modifications and substitutions should also be considered as being within the scope of the present invention.
Claims (8)
1. The heat-resistant steel for the high-temperature turbine rotor forging is characterized by comprising the following chemical elements in percentage by mass: c:0.11-0.17%, si:0.02-0.095%, mn:0.22-0.5%, cr:10.6-11.8%, co:2.5-2.9%, mo:0.01-0.18%, W:2.55-3.4%, V:0.12-0.39%, nb:0.03-0.07%, ni:0.12-0.29%, cu:0.3-0.7%, B:0.019-0.035%, N:0.012-0.035%, Y:0-0.5%, and the balance of Fe and unavoidable impurities.
2. The heat resistant steel according to claim 1, characterized in that it comprises the following chemical elements in mass percent: c:0.12-0.15%, si:0.02-0.045%, mn:0.25-0.35%, cr:10.9-11.1%, co:2.65-2.85%, mo:0.01-0.09%, W:3.05-3.35%, V:0.31-0.37%, nb:0.04-0.06%, ni:0.12-0.24%, cu:0.45-0.65%, B:0.019-0.027%, N:0.0155-0.029%, Y:0-0.5%, and the balance of Fe and unavoidable impurities.
3. Heat resistant steel according to claim 1 or 2, characterized in that the mass percentage of Y is 0.26-0.34%.
4. A method for producing a heat resistant steel according to any one of claims 1 to 3, comprising the steps of: raw materials are weighed according to element proportion and mixed, and then are poured into an electrode rod after smelting, ladle refining and vacuum degassing, the electrode rod is subjected to electroslag remelting treatment and cooling solidification to form a steel ingot, and the steel ingot is forged into a turbine rotor type blank and is subjected to heat treatment.
5. The method according to claim 4, wherein the heat treatment comprises one quenching and two tempering steps.
6. The method according to claim 5, wherein the quenching temperature is 1100 ℃ to 1150 ℃, the first tempering temperature is 580 ℃ to 660 ℃, and the second tempering temperature is 670 ℃ to 730 ℃.
7. Use of the heat resistant steel according to any one of claims 1-3 in turbomachinery.
8. The use of claim 7, wherein the turbomachine is a steam turbine.
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