EP4148157A1 - Alliages haute résistance de haute température pour unités thermoélectriques et technique de traitement associée - Google Patents

Alliages haute résistance de haute température pour unités thermoélectriques et technique de traitement associée Download PDF

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EP4148157A1
EP4148157A1 EP21800520.5A EP21800520A EP4148157A1 EP 4148157 A1 EP4148157 A1 EP 4148157A1 EP 21800520 A EP21800520 A EP 21800520A EP 4148157 A1 EP4148157 A1 EP 4148157A1
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temperature
alloy
less
generating unit
room temperature
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German (de)
English (en)
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Jingbo Yan
Yuefeng Gu
Yong Yuan
Zheng Yang
Xingxing Zhang
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Xian Thermal Power Research Institute Co Ltd
Huaneng Power International Inc
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Xian Thermal Power Research Institute Co Ltd
Huaneng Power International Inc
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D21/00—Casting non-ferrous metals or metallic compounds so far as their metallurgical properties are of importance for the casting procedure; Selection of compositions therefor
    • B22D21/02—Casting exceedingly oxidisable non-ferrous metals, e.g. in inert atmosphere
    • B22D21/025—Casting heavy metals with high melting point, i.e. 1000 - 1600 degrees C, e.g. Co 1490 degrees C, Ni 1450 degrees C, Mn 1240 degrees C, Cu 1083 degrees C
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D27/00—Treating the metal in the mould while it is molten or ductile ; Pressure or vacuum 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
    • 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
    • C21D1/26—Methods of annealing
    • 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
    • C21D1/78—Combined heat-treatments not provided for above
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working
    • 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
    • C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/0081—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for slabs; for billets
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting
    • C22C1/023—Alloys based on nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C19/00—Alloys based on nickel or cobalt
    • C22C19/03—Alloys based on nickel or cobalt based on nickel
    • C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
    • C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
    • C22C19/056—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 10% but less than 20%
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C30/00—Alloys containing less than 50% by weight of each constituent
    • 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
    • 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
    • C22C38/44—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
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/10—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of nickel or cobalt or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
    • C21C7/10—Handling in a vacuum

Definitions

  • the disclosure relates to the field of materials and material preparation, and more particularly relates to a high-strength superalloy for a thermal generating unit and a process of preparing the same, wherein the resulting high-strength superalloy may satisfy requirements of thick-wall parts such as the main steam pipeline and the header tank of an advanced 700°C ultra-supercritical (A-USC) thermal generating unit with respect to workability and service performance.
  • A-USC advanced 700°C ultra-supercritical
  • the large-diameter, thick-wall pipes of under-600°C thermal generating units mainly use ferritic heat-resisting steels (Cr: 9 wt.%-12 wt.%) and heat-resistance austenitic steels.
  • Typical ferritic heat-resisting steels include TP91, NF616, E911, and HCM12A, etc., which have excellent durability and corrosion-resistance properties and are thus extensively applied in large-diameter, thick-wall pipes of under-600°C units.
  • TP91 steel has been extensively used in subcritical and supercritical thermal generating units, from which massive service performance data have been accumulated.
  • ferritic heat-resisting steels can hardly meet serviceability requirements of higher temperature parameters of large-diameter, thick-wall pipes.
  • the coarse-grained (TP304H, TP347H), fine-grained (Super304H, TP347HFG), and high-chromium (HR3C, NF709, SAVE25) heat resistant austenitic steels are better in durability, anti-oxidization, and corrosion-resistance.
  • the heat resistant austenitic steels also have issues such as low heat transfer efficiency, high thermal expansion coefficient, and expensiveness. Particularly when the main steam temperature reaches 700°C or above, the strength of heat-resistant austenitic steels cannot satisfy requirements of large-diameter, thick-wall pipes with respect to material serviceability.
  • iron-nickel-based superalloys including HR6W and HR35; Sandvik has developed Sanicro25 iron-nickel-based alloy; CAS IMR (Institute of Metal Research, Chinese Academy of Sciences) and CISRI (China Iron & Steel Research Institute Group) have developed wrought iron-nickel-based superalloys such as GH2984 and GH110, etc., respectively.
  • CAS IMR Institute of Metal Research, Chinese Academy of Sciences
  • CISRI China Iron & Steel Research Institute Group
  • the iron-nickel-based superalloys have a low hot strength, a poor structure stability, and a poor corrosion-resistance property despite their cost advantages.
  • to achieve a desired structure and performance they still need deforming processing, resulting in preparation and processing complexity and further incurring a relatively high overall manufacture cost, which renders it difficult for performance improvement.
  • a high-strength superalloy for use in a thermal generating unit and a method of preparing the same are provided.
  • a high-strength superalloy for use in a thermal generating unit comprising, by weigh percent constituents: Carbon (C) between 0.05 and 0.08, Chromium (Cr) between 14 and 17, Manganese (Mn) less than or equal to 0.5, Silicon (Si) less than or equal to 0.5, Tungsten (W) between 1.0 to 2.5, Molybdenum (Mo) between 0.3 and 2.0, Titanium (Ti) between 2.0 and 2.5, Aluminum (Al) between 1.0 and 1.5, Boron (B): less than or equal to 0.003, Zirconium (Zr) less than or equal to 0.03, Iron (Fe) between 37 and 48, balance Ni.
  • a process of preparing a high-strength superalloy for use in a thermal generating unit comprising steps of:
  • ta duration of the refining in step (1) ranges from 0.5 hours to 1 hour.
  • step (1) specifically comprises: melting the chromium, nickel, tungsten, silicon, manganese, molybdenum and iron when the vacuum degree reaches between 0.3Pa and 0.5Pa, followed by adding coke for deoxidization, the mass of the coke added not exceeding 25% ⁇ 50% of the mass of carbon, then adding a Ni-Mg alloy for second deoxidization, followed by adding aluminum, titanium, boron, zirconium and carbon, and then stirring for 5 ⁇ 10 minutes (min) and discharging liquid alloy for casting, the casting temperature being not lower than 1600°C, and after the liquid alloy is solidified, subjecting the solidified alloy to homogenization treatment, followed by air cooling to room temperature.
  • step (1) a metal mold is used for casting; and a surface of the liquid alloy is covered with an aluminum exothermic compound upon solidifying.
  • the homogenization treating specifically comprises: heating from room temperature to 1050°C ⁇ 1120°C at a heating rate ranging from 10°C/min to 30°C/min, and dwelling at the temperature for 24 hours.
  • step (1) the solidified alloy dwells at a temperature ranging from 900°C to 980°C for 1.0 to 1.5 hours, followed by homogenization treating.
  • step (2) after each pass of cogging, the ingot is charged back into the furnace to keep temperature, wherein a dwell time T at the temperature and an out-of-furnace time t satisfy 5t ⁇ T ⁇ 10t.
  • step (3) after each pass of hot rolling, the ingot is charged back into the furnace to keep temperature, wherein a dwell time T at the temperature and an out-of-furnace time t satisfy 5t ⁇ T ⁇ 10t.
  • step (4) specifically comprises: first heating to 1100°C ⁇ 1125°C for solution treating for 3 to 5 hours and then air cooling to room temperature, followed by reheating from the room temperature to 630°C ⁇ 680°C at a heating rate of 10°C /min to 30°C /min and dwelling at the temperature for 7 to 10 hours, and then air cooling to room temperature, and finally reheating from the room temperature to 740°C to 800°C at a heating rate of 10°C /min to 30°C /min, dwelling at the temperature for 1 to 3 hours, and then air cooling to room temperature.
  • the disclosure offers the following benefits: the alloy provided by the disclosure has a high Fe content but lower contents of precious metals such as W and Nb, thereby having a reduced raw material cost. Meanwhile, the alloy preparing process abandons the conventional triple melting process for superalloys, but adopts a scheme of directly cogging after arc melting, which reduces the preparation composition of the alloy.
  • the smelting process involves second oxidization, reducing the metal liquid solidification rate with an exothermal compound after casting, and then carrying out multiple passes of large-deformation-amount treatment to the alloy, wherein the cogging and rolling temperatures are controlled to 200°C ⁇ 250°C and 150°C ⁇ 200°C above the ⁇ ' precipitation temperature, respectively, and their single-pass deformation amounts are not less than 30% and 35%, respectively, which ensures enough energy storage for strains during delivery of the alloy.
  • the resulting hot-treated alloy has an excellent high-temperature strength property, a yield strength of not lower than 540MPa and a ductility rate higher than 12% at 700°C.
  • the disclosure provides a high-strength superalloy for a thermal generating unit, comprising, by weigh percent constituents: Carbon (C) between 0.05 and 0.08, Chromium (Cr) between 14 and 17, Manganese (Mn) less than or equal to 0.5, Silicon (Si) less than or equal to 0.5, Tungsten (W) between 1.0 to 2.5, Molybdenum (Mo) between 0.3 and 2.0, Titanium (Ti) between 2.0 and 2.5, Aluminum (Al) between 1.0 and 1.5, Boron (B): less than or equal to 0.003, Zirconium (Zr) less than or equal to 0.03, Iron (Fe) between 37 and 48, balance Ni.
  • a process of preparing the alloy mainly comprises three steps: alloy smelting, deforming, and heat treating, specifically:
  • coke is added for deoxidization after the Cr, Ni, W, Si, Mn, Mo and Fe are completely molten, wherein the mass of coke added is not greater than 25% ⁇ 50% of the mass of carbon in the alloy composition; after the deoxidization, Ni-Mg alloy is added for second deoxidization, and finally, easily burnable elements including Al, Ti, B, Zr, and C are added and stirred for 5min to 10min, and then the melt is discharged, wherein the casting temperature upon discharge is not lower than 1600°C.
  • a metal mold is used for casting; and the liquid alloy surface is covered with an aluminum exothermic compound during solidification, so as to lower solidification rate and facilitate feeding of the metal liquid.
  • the heating rate should be controlled within a range from 10°C to 30°C/min, wherein the ingot should dwell at 900°C ⁇ 980°C for 1.0h to 1.5h before being heated to the homogenization treatment temperature; and then the ingot is heated to 1050°C ⁇ 1120°C at the heating rate between 10°C/min and 30°C/min.
  • the hot-treated alloy has an excellent high-temperature strength property, with a yield strength not less than 540MPa and a ductility higher than 12% at 700°C.
  • This example provides a high-strength superalloy for use in a thermal generating unit, comprising, by weigh percent constituents: Carbon (C) 0.06, Chromium (Cr) 16, Manganese (Mn) 0.2, Silicon (Si) 0.15, Tungsten (W) 1.6, Molybdenum (Mo) 1.2, Titanium (Ti) 2.2, Aluminum (Al) 1.4, Boron (B) 0.002, Zirconium (Zr) 0.02, Iron (Fe) 37, balance Ni.
  • a magnesium oxide basic lining was applied for smelting the alloy, the furnace was rinsed with pure nickel before smelting, and the raw materials of the alloy were subjected to shot blasting treatment before addition.
  • the alloy was smelted with an induction arc furnace, with the vacuum degree being controlled at 0.35Pa.
  • the elements including Cr, Ni, and W were completely molten and then refined for 40min, and before adding Al, Ti, B, Zr, and C, highly pure argon was introduced for protection.
  • the ingot was heated to 1020°C at a rate of 10°C/min and dwelled at the temperature for 1.0h; then, the temperature rose up to 1160°C, followed by homogenization treatment for 24h, and then air cooled to room temperature.
  • the oxide scale was turn-milled, the alloy was cogged at a temperature 220°C above a ⁇ ' precipitation temperature, the deformation amount of each pass being 30% and the final deformation amount in total being 70%.
  • the alloy was subjected to hot rolling at a temperature 160°C above the ⁇ ' precipitation temperature, with the deformation amount of each pass being 35% and the final deformation amount in total being 80%.
  • the rollers were heated to 500°C above, and after each pass of cogging and rolling, the alloy was charged back to the furnace to keep the temperature for 30min.
  • the rolled alloy was reheated to 1120°C for solution treatment for 4h and then air cooled to room temperature, followed by reheating to 650°C and holding at the temperature for 8h, and then air cooled to room temperature; finally, the alloy was reheated to 760°C and dwelled at the temperature for 2h, followed by air cooling, wherein the heating rate during the procedures of homogenization treatment, solution treatment, and aging treatment was 10°C/min, and the ingot should dwell at 950°C for 1.0h before being heated to the homogenization treatment temperature.
  • Figs. 1 and 2 are images of the ingot and the forged alloy slab according to example 1, where no noticeable cracks are found in their surface, which indicates that the alloy smelting and processing solution is reasonable.
  • the alloy performance testing result indicates that the alloy has a yield strength of 582MPa and a ductility of 14.2% at 700°C, showing that the alloy has an excellent high-temperature strength property.
  • This example provides a high-strength superalloy for use in a thermal generating unit, comprising, by weigh percent constituents: Carbon (C) 0.07, Chromium (Cr) 15, Manganese (Mn) 0.2, Silicon (Si) 0.15, Tungsten (W) 2.2, Molybdenum (Mo) 0.4, Titanium (Ti) 2.2, Aluminum (Al) 1.4, Boron (B) 0.002, Zirconium (Zr) 0.02, Iron (Fe) 47, balance Ni.
  • a magnesium oxide basic lining was applied for smelting the alloy, the furnace was rinsed with pure nickel before smelting, and the raw materials of the alloy were subjected to shot blasting treatment before addition.
  • the alloy was smelted with an induction arc furnace, with the vacuum degree being controlled at 0.35Pa.
  • the elements including Cr, Ni, and W were completely molten and then refined for 40min, and before adding Al, Ti, B, Zr, and C, highly pure argon was introduced for protection.
  • coke was added for deoxidization, wherein the mass of coke added does not exceed 40% of the carbon content in the alloy composition; upon completion of deoxidization, the Ni-Mg alloy was added for second deoxidization; finally, easily burnable elements including Al, Ti, B, Zr, and C were added; the melt was stirred for 5min and then discharged for casting, wherein the casting temperature was 1650°C.
  • a metal mold was used for the casting; after casting, the liquid alloy surface was covered with a sodium nitrate + aluminum oxide exothermic compound so as to reduce the solidification rate and facilitate feeding of the metal liquid.
  • the proportion between sodium nitrate and aluminum oxide exothermic compound was known to those skilled in the art.
  • the ingot was heated to 1020°C at a rate of 10°C /min and dwelled at the temperature for 1.0h; then, the temperature rose up to 1160°C, followed by homogenization treatment for 24h, and then air cooled to room temperature.
  • the oxide scale was turn-milled, the alloy was cogged at a temperature 240°C above a ⁇ ' precipitation temperature, the deformation amount of each pass being 30% and the final deformation amount in total being 70%.
  • the alloy was subjected to hot rolling at a temperature 180°C above the ⁇ ' precipitation temperature, with the deformation amount of each pass being 35% and the final deformation amount in total being 80%.
  • the rollers were heated to 500°C above, and after each pass of cogging and rolling, the alloy was charged back to the furnace to keep the temperature for 30min.
  • the rolled alloy was reheated to 1120°C for solution treatment for 4h and then air cooled to room temperature, followed by reheating to 650°C and holding at the temperature for 8h, and then air cooled to room temperature; finally, the alloy was reheated to 760°C and held at the temperature for 2h, followed by air cooling, wherein the heating rate during the procedures of homogenization treatment, solution treatment, and aging treatment was 10°C /min, and the ingot should dwell at 950°C for 1.0h before being heated to the homogenization treatment temperature.
  • Figs. 3 and 4 are images of the alloy subjected to the first pass of rolling and the rolled alloy, respectively, where no noticeable cracks are found in their surface, which indicates that the alloy processing solution is reasonable.
  • the alloy performance testing result indicates that the alloy has a yield strength of 543MPa and a ductility of 16.1% at 700°C, showing that the alloy has an excellent high-temperature strength property.
  • the high-temperature superalloy comprises, by weigh percent constituents: Carbon (C) between 0.05 and 0.08, Chromium (Cr) between 14 and 17, Manganese (Mn) less than or equal to 0.5, Silicon (Si) less than or equal to 0.5, Tungsten (W) between 1.0 to 2.5, Molybdenum (Mo) between 0.3 and 2.0, Titanium (Ti) between 2.0 and 2.5, Aluminum (Al) between 1.0 and 1.5, Boron (B): less than or equal to 0.003, Zirconium (Zr) less than or equal to 0.03, Iron (Fe) between 37 and 48, balance Ni.
  • the pre-prepared alloy constituents are smelted in an electric arc furnace under a vacuum degree not higher than 0.3Pa; the alloy was cogged with a deformation amount up to 70% at a temperature 200°C ⁇ 250°C above the Ni 3 Al ( ⁇ ') precipitation temperature, and hot rolled with a deformation amount up to 80% at a temperature 150°C ⁇ 200°C above the ⁇ ' precipitation temperature.
  • the alloy preparing process according to the disclosure has a low manufacture cost, and the alloy prepared according to the method has an excellent high-temperature mechanical property at 650°C above.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
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  • Heat Treatment Of Steel (AREA)
  • Manufacture And Refinement Of Metals (AREA)
EP21800520.5A 2020-05-08 2021-05-08 Alliages haute résistance de haute température pour unités thermoélectriques et technique de traitement associée Pending EP4148157A1 (fr)

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Application Number Priority Date Filing Date Title
CN202010383732.9A CN111394638B (zh) 2020-05-08 2020-05-08 一种火电机组用高强高温合金及其加工工艺
PCT/CN2021/092505 WO2021223760A1 (fr) 2020-05-08 2021-05-08 Alliages haute résistance de haute température pour unités thermoélectriques et technique de traitement associée

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CN112359261B (zh) * 2020-11-10 2021-12-14 华能国际电力股份有限公司 一种高铝耐蚀高温合金的大口径厚壁管材制备加工工艺
CN112453101B (zh) * 2020-11-10 2023-03-10 华能国际电力股份有限公司 一种铁基高温合金的大口径厚壁管材成型制备工艺
CN114150169A (zh) * 2021-11-26 2022-03-08 中国航发北京航空材料研究院 一种涡轮增压器用高温合金k418c的制备方法
CN115261700B (zh) * 2022-08-11 2023-06-09 华能国际电力股份有限公司 一种耐蚀合金及其制备方法
CN116219230A (zh) * 2022-12-16 2023-06-06 四川六合特种金属材料股份有限公司 一种高温合金密封板材料及其制备方法

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