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CN119824288A - Superhigh temperature bearing alloy and preparation method thereof - Google Patents

Superhigh temperature bearing alloy and preparation method thereof Download PDF

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Publication number
CN119824288A
CN119824288A CN202510084282.6A CN202510084282A CN119824288A CN 119824288 A CN119824288 A CN 119824288A CN 202510084282 A CN202510084282 A CN 202510084282A CN 119824288 A CN119824288 A CN 119824288A
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high temperature
ultra
bearing alloy
temperature bearing
alloy
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CN119824288B (en
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王辉
曹文全
俞峰
王存宇
张泽茜
徐海峰
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China Iron and Steel Research Institute Group
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China Iron and Steel Research Institute Group
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    • 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
    • C22B—PRODUCTION AND REFINING OF METALS; PRETREATMENT OF RAW MATERIALS
    • C22B4/00—Electrothermal treatment of ores or metallurgical products for obtaining metals or alloys
    • C22B4/06—Alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C27/00—Alloys based on rhenium or a refractory metal not mentioned in groups C22C14/00 or C22C16/00
    • C22C27/02—Alloys based on vanadium, niobium, or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C27/00—Alloys based on rhenium or a refractory metal not mentioned in groups C22C14/00 or C22C16/00
    • C22C27/04—Alloys based on tungsten or molybdenum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
    • C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
    • C22C32/0052—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents only carbides
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16C—SHAFTS; FLEXIBLE SHAFTS; ELEMENTS OR CRANKSHAFT MECHANISMS; ROTARY BODIES OTHER THAN GEARING ELEMENTS; BEARINGS
    • F16C33/00—Parts of bearings; Special methods for making bearings or parts thereof
    • F16C33/02—Parts of sliding-contact bearings
    • F16C33/04—Brasses; Bushes; Linings
    • F16C33/06—Sliding surface mainly made of metal
    • F16C33/12—Structural composition; Use of special materials or surface treatments, e.g. for rust-proofing
    • F16C33/121—Use of special materials

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Organic Chemistry (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • General Engineering & Computer Science (AREA)
  • Life Sciences & Earth Sciences (AREA)
  • Environmental & Geological Engineering (AREA)
  • General Life Sciences & Earth Sciences (AREA)
  • Geochemistry & Mineralogy (AREA)
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  • Manufacturing & Machinery (AREA)
  • Sliding-Contact Bearings (AREA)

Abstract

The invention relates to an ultra-high temperature bearing alloy and a preparation method thereof. The invention relates to an ultrahigh temperature bearing alloy, which comprises, by weight, 0.02% -4.0% of C, 16.0% -19.0% of Cr, 30.0% -35.0% of Mo, 30.0% -34.0% of Nb, 16.5% -18.5% of V and unavoidable impurities, wherein a matrix in a microstructure of the ultrahigh temperature bearing alloy is a BCC crystal structure with high mixed entropy, and NbC and Nb/VC precipitated phases are uniformly distributed on the BCC matrix. The high-temperature bearing has the beneficial effects that the high-temperature structural stability is guaranteed based on the entropy effect in thermodynamics, meanwhile, the high-temperature hardness and the high-temperature strength of the high-temperature bearing are enhanced through Nb/VC high-carbide reinforcement, and the service performance requirements of the high-temperature bearing with stable tissue structure, high hardness and high wear resistance at high temperature are met.

Description

Superhigh temperature bearing alloy and preparation method thereof
Technical Field
The invention relates to the technical field of high-temperature bearing materials, in particular to an ultrahigh-temperature bearing alloy and a preparation method thereof.
Background
With the rapid development of the fields of aerospace, medical treatment and the like, the requirements for high-temperature bearing materials with high temperature resistance and better performance are more and more urgent. At present, the service temperature of the high-temperature bearing steel represented by Cr14Mo4V is not more than 524 ℃, and the service temperature of the 55 alloy and the Cr40Al3Ti nickel-based high-temperature bearing alloy is not more than 600 ℃. After the service temperature exceeds 600 ℃, the structure is changed, so that the service requirement of the bearing material for high strength and high hardness cannot be met, and development of novel high-temperature-resistant bearing materials is urgently needed.
Refractory high-entropy alloy containing Mo, V, nb and other high-melting elements is a novel potential material for manufacturing extreme-temperature service parts due to the characteristics of high melting point, high strength, high hardness and the like.
CN13088787a discloses a single-phase WNbMoTaZr refractory high-entropy alloy and a preparation method thereof, wherein the element composition comprises W, nb, mo, ta and Zr, and the molar ratio of W, nb, mo, ta to Zr is 1:1:1:1:0.1-0.5. The alloy has the average hardness of 546HV, the yield strength at room temperature of 1584Mpa, the compression plasticity of 8.4 percent and good thermal stability in the range of room temperature to 1400 ℃. But its high temperature strength and hardness data are not reported.
The CN114606424A patent discloses a high-strength high-toughness Mo-Nb-Ta-Hf-Zr refractory high-entropy alloy and a preparation method thereof, wherein the expression of the Mo-Nb-Ta-Hf-Zr refractory high-entropy alloy is MoxNbyTazHfuZrv, x, y, z, u, v is the mole percentage of elements, and x+y+z+u+v=1 is satisfied, wherein x is 0.05< 0.3, y+z is 0.4< 0.5, and u+v is 0.45. The yield strength at 1000 ℃ is 700-1100MPa, and the compression strength is 770-1800MPa. But its high temperature hardness data is not reported.
In summary, aiming at the characteristics of high hardness, high heat resistance and stable structure of the high-temperature bearing material, developing and preparing a novel bearing alloy with high yield strength, high hardness and high wear resistance at the high temperature of 1000 ℃ is a technical problem to be solved urgently.
Disclosure of Invention
The invention aims to overcome the defects of the prior art and provide an ultrahigh temperature bearing alloy with high yield strength, high hardness and high wear resistance and a preparation method thereof.
The invention provides an ultra-high temperature bearing alloy, which has the technical scheme that:
The ultra-high temperature bearing alloy comprises, by weight, 0.02% -4.0% of C, 16.0% -19.0% of Cr, 30.0% -35.0% of Mo, 30.0% -34.0% of Nb, 16.5% -18.5% of V and unavoidable impurities, wherein a matrix in a microstructure of the ultra-high temperature bearing alloy is a BCC crystal structure with high mixed entropy, and a separated phase of NbC and Nb/VC is uniformly distributed on the BCC matrix.
Further, the volume percentage of the NbC and Nb/VC precipitated phases on the BCC matrix is 0-40%, and the average size of the NbC and Nb/VC precipitated phases is 3-30 mu m.
Further, the ultra-high temperature bearing alloy has stable structure at room temperature to 1000 ℃, room temperature hardness is more than or equal to 58HRC,800 ℃ high temperature hardness is more than or equal to 51HRC, and 1000 ℃ high temperature hardness is more than or equal to 49HRC.
Further, the ultra-high temperature bearing alloy has high temperature compression strength of more than or equal to 2095MPa at 800 ℃ and compression engineering strain of more than or equal to 20%, and has high temperature compression strength of more than or equal to 1219MPa and compression engineering strain of more than or equal to 30% at 1000 ℃.
Further, the alloy comprises, by weight, 0.02-0.05% of C, 16.0-19.0% of Cr, 30.0-35.0% of Mo, 30.0-34.0% of Nb, 16.5-18.5% of V and unavoidable impurities.
Further, the alloy comprises, by weight, 0.6-0.8% of C, 16.0-19.0% of Cr, 30.0-35.0% of Mo, 30.0-34.0% of Nb, 16.5-18.5% of V and unavoidable impurities.
Further, the alloy comprises, by weight, 3.0-4.0% of C, 16.0-19.0% of Cr, 30.0-35.0% of Mo, 30.0-34.0% of Nb, 16.5-18.5% of V and unavoidable impurities.
Further, the alloy is prepared by a vacuum induction smelting method or a vacuum arc smelting method, and the alloy is repeatedly smelted and solidified for 8-10 times to ensure the uniformity of the structure.
Further, the raw materials prepared according to the component proportion are placed into a DHL400 high-vacuum non-consumable arc furnace, the vacuum is pumped to 5 multiplied by 10 -3 Pa, argon gas is introduced into a vacuum chamber until the pressure of the chamber is minus 0.05MPa, the raw materials are subjected to arc melting, alloy ingots at each station are kept for 1min after being completely melted, the melting temperature is kept between 2100 ℃ and 2200 ℃, and the alloy ingots are cooled along with a water-cooled copper mold after the melting is finished.
The implementation of the invention comprises the following technical effects:
The ultra-high temperature bearing alloy guarantees the stability of a high temperature structure based on the entropy effect in thermodynamics, and simultaneously enhances the high temperature hardness and the high temperature strength through Nb/VC high carbide reinforcement, thereby meeting the material service performance requirements of the high temperature bearing on stable tissue structure, high hardness and high wear resistance at high temperature. The alloy based on the BCC matrix has the characteristics of stable structure at ultra-high temperature (room temperature to 1000 ℃), high temperature and high hardness (800 ℃ high temperature hardness is more than or equal to 51HRC,1000 ℃ high temperature hardness is more than or equal to 49 HRC), high strength (800 ℃ compressive strength is more than or equal to 2095MPa, 1000 ℃ compressive strength is more than or equal to 1219 MPa) and high strength. The novel high-entropy alloy is a novel high-entropy bearing alloy material with potential, solves the problem that the strength and hardness of the existing high-temperature bearing alloy are insufficient in 800-1000 ℃ ultra-high temperature service, and can greatly promote the rapid large-scale development of hot end materials and related industries.
Drawings
FIG. 1 is a typical structure diagram of the ultra-high temperature bearing alloy obtained in example 3.
FIG. 2 is a typical structure diagram of the ultra-high temperature bearing alloy obtained in example 1.
FIG. 3 is a typical structure diagram of the ultra-high temperature bearing alloy obtained in example 2.
FIG. 4 is a typical structure diagram of the ultra-high temperature bearing alloy obtained in example 3.
Fig. 5 is a thermal differential analysis DSC profile of example 1 and example 2.
Fig. 6 is a graph of high temperature compressive stress strain at 800 ℃ and 1000 ℃ for example 2.
Fig. 7 is a graph of the high temperature compressive stress strain at 800 ℃ for example 3.
Detailed Description
The invention will now be described in detail with reference to the following examples and the accompanying drawings, it being pointed out that the examples described are intended only to facilitate an understanding of the invention and are not intended to be limiting in any way.
Example 1
The ultrahigh temperature bearing alloy comprises, by weight, 0.02-0.05% of C, 16.0-19.0% of Cr, 30.0-35.0% of Mo, 30.0-34.0% of Nb, 16.5-18.5% of V and unavoidable impurities. The preparation method comprises the steps of putting raw materials prepared according to the component proportion into a DHL400 high-vacuum non-consumable arc furnace, vacuumizing to 5X 10 -3 Pa, introducing argon gas into a vacuum chamber until the pressure of the chamber is minus 0.05MPa, carrying out arc melting on the raw materials, keeping alloy ingots at each station for 1min after the alloy ingots are completely melted, carrying out ingot turning melting for 8-10 times in order to ensure the uniformity of the alloy components, keeping the melting temperature between 2100 ℃ and 2200 ℃, and cooling along with a water-cooled copper mold after the melting is finished. After smelting is finished, sampling the chemical components to be tested and carrying out other tests.
Example 2
The ultrahigh temperature bearing alloy comprises, by weight, 0.6-0.8% of C, 16.0-19.0% of Cr, 30.0-35.0% of Mo, 30.0-34.0% of Nb, 16.5-18.5% of V and unavoidable impurities. Unlike example 1, the hardness and strength are improved by alloying with 0.6 to 0.8% C. The preparation method comprises the steps of putting raw materials prepared according to the component proportion into a DHL400 high-vacuum non-consumable arc furnace, vacuumizing to 5X 10 -3 Pa, introducing argon gas into a vacuum chamber until the pressure of the chamber is minus 0.05MPa, carrying out arc melting on the raw materials, keeping alloy ingots at each station for 1min after the alloy ingots are completely melted, carrying out ingot turning melting for 8-10 times in order to ensure the uniformity of the alloy components, keeping the melting temperature between 2100 ℃ and 2200 ℃, and cooling along with a water-cooled copper mold after the melting is finished. After smelting is finished, sampling the chemical components to be tested and carrying out other tests.
Example 3
The ultrahigh temperature bearing alloy comprises, by weight, 3.0-4.0% of C, 16.0-19.0% of Cr, 30.0-35.0% of Mo, 30.0-34.0% of Nb, 16.5-18.5% of V and unavoidable impurities. Unlike examples 1 and 2, example 3 was alloyed with 3.0-4.0% of ultrahigh content of C element, which significantly improved the hardness and strength. The preparation method comprises the steps of putting raw materials prepared according to the component proportion into a DHL400 high-vacuum non-consumable arc furnace, vacuumizing to 5X 10 -3 Pa, introducing argon gas into a vacuum chamber until the pressure of the chamber is minus 0.05MPa, carrying out arc melting on the raw materials, keeping alloy ingots at each station for 1min after the alloy ingots are completely melted, carrying out ingot turning melting for 8-10 times in order to ensure the uniformity of the alloy components, keeping the melting temperature between 2100 ℃ and 2200 ℃, and cooling along with a water-cooled copper mold after the melting is finished. After smelting is finished, sampling the chemical components to be tested and carrying out other tests.
Example 4
The ultrahigh temperature bearing alloy comprises, by weight, 1.0-2.0% of C, 17.0-18.0% of Cr, 34.0-35.0% of Mo, 30.0-31.0% of Nb, 16.5-18.5% of V and unavoidable impurities. Unlike examples 1 and 2, example 3 was alloyed with 3.0-4.0% of ultrahigh content of C element, which significantly improved the hardness and strength. The preparation method comprises the steps of putting raw materials prepared according to the component proportion into a DHL400 high-vacuum non-consumable arc furnace, vacuumizing to 5X 10 -3 Pa, introducing argon gas into a vacuum chamber until the pressure of the chamber is minus 0.05MPa, carrying out arc melting on the raw materials, keeping alloy ingots at each station for 1min after the alloy ingots are completely melted, carrying out ingot turning melting for 8-10 times in order to ensure the uniformity of the alloy components, keeping the melting temperature between 2100 ℃ and 2200 ℃, and cooling along with a water-cooled copper mold after the melting is finished. After smelting is finished, sampling the chemical components to be tested and carrying out other tests.
Example 5
The ultrahigh temperature bearing alloy comprises, by weight, 1.0-2.0% of C, 18.0-19.0% of Cr, 30.0-31.0% of Mo, 33.0-34.0% of Nb, 16.5-18.5% of V and unavoidable impurities. Unlike examples 1 and 2, example 3 was alloyed with 3.0-4.0% of ultrahigh content of C element, which significantly improved the hardness and strength. The preparation method comprises the steps of putting raw materials prepared according to the component proportion into a DHL400 high-vacuum non-consumable arc furnace, vacuumizing to 5X 10 -3 Pa, introducing argon gas into a vacuum chamber until the pressure of the chamber is minus 0.05MPa, carrying out arc melting on the raw materials, keeping alloy ingots at each station for 1min after the alloy ingots are completely melted, carrying out ingot turning melting for 8-10 times in order to ensure the uniformity of the alloy components, keeping the melting temperature between 2100 ℃ and 2200 ℃, and cooling along with a water-cooled copper mold after the melting is finished. After smelting is finished, sampling the chemical components to be tested and carrying out other tests.
Table 1 shows the chemical compositions and weight percentages of the ultra-high temperature bearing alloys obtained in examples 1 to 5.
Table 1 chemical composition of the ultra-high temperature bearing alloy of each example, wt%
Table 2 room temperature hardness, HRC, of the superhigh temperature bearing alloys of the various examples
TABLE 3 high temperature hardness, HRC, of the ultra-high temperature bearing alloy of EXAMPLE 2
As can be seen from tables 2 and 3, the invention can realize the ultra-high temperature bearing alloy with uniform structure, high hardness and high strength and plastic through composition control, and the produced ultra-high temperature bearing alloy has stable structure in the ultra-high temperature range (room temperature to 1000 ℃), room temperature hardness of more than or equal to 58HRC,800 ℃ high temperature hardness of more than or equal to 51HRC and 1000 ℃ high temperature hardness of more than or equal to 49HRC. Has the characteristics of high strength, high hardness, high strength and plastic and stable tissue.
FIGS. 1 and 4 are typical texture diagrams of the ultra-high temperature bearing alloy obtained in example 3, wherein the volume percent of BCC matrix is about 60%, the volume percent of NbC, nb/VC precipitates is about 40%, and the average size is 30 μm. FIG. 2 is a typical texture map of the ultra-high temperature bearing alloy obtained in example 1, which is a BCC matrix with no significant precipitated phases. FIG. 3 is a typical texture map of the ultra-high temperature bearing alloy obtained in example 2, which is a BCC matrix and NbC precipitate phase, the volume percent of the precipitate phase being about 10%, and the average size being about 3 μm. FIG. 5 is a DSC graph of thermal differential analysis of examples 1 and 2, wherein the sample of example 1 has stable structure in the range of 0-1040 ℃ and precipitation transition in the range of 1044-1100 ℃, and the sample of example 2 added with C element has stable structure in the range of 0-1400 ℃ to show that the obtained ultra-high temperature bearing alloy has high structure stability in the range of 0-1000 ℃. Fig. 6 is a graph of high temperature compressive stress strain at 800 ℃ and 1000 ℃ for example 2. The ultra-high temperature bearing alloy has a high temperature compression strength of 2095MPa and 20% compressive engineering strain at 800 ℃, and a compression strength of 1219MPa and >30% compressive engineering strain at 1000 ℃, indicating that the ultra-high temperature bearing alloy has high strength and good plasticity at 800-1000 ℃. Fig. 7 example 3 is a high temperature compressive stress strain plot at 800 ℃. With the increase of C element, the compression strength is further improved, and the 800 ℃ high-temperature compression strength of 2328MPa and 24% compression engineering strain are provided. The data can indicate that the high-carbon ultrahigh-temperature bearing alloy has higher strength at high temperature and good plasticity, and the data of other embodiments are not repeated.
Finally, it should be noted that the above embodiments are only for illustrating the technical solution of the present invention, and not for limiting the scope of the present invention, and although the present invention has been described in detail with reference to the preferred embodiments, it should be understood by those skilled in the art that modifications or equivalent substitutions can be made to the technical solution of the present invention without departing from the spirit and scope of the technical solution of the present invention.

Claims (9)

1.一种超高温轴承合金，其特征在于：其合金的化学成分按重量百分含量包含：C0.02％-4.0％，Cr 16.0％-19.0％，Mo 30.0％-35.0％，Nb 30.0-34.0％，V16.5％-18.5％和不可避免的杂质；所述超高温轴承合金的微观组织中基体为高混合熵的BCC晶体结构，BCC基体上分布有NbC、Nb/VC析出相。1. An ultra-high temperature bearing alloy, characterized in that: the chemical composition of the alloy comprises, by weight percentage: C 0.02%-4.0%, Cr 16.0%-19.0%, Mo 30.0%-35.0%, Nb 30.0-34.0%, V 16.5%-18.5% and inevitable impurities; in the microstructure of the ultra-high temperature bearing alloy, the matrix is a BCC crystal structure with high mixing entropy, and NbC and Nb/VC precipitated phases are distributed on the BCC matrix. 2.根据权利要求1所述超高温轴承合金，其特征在于：NbC、Nb/VC析出相在BCC基体上的体积百分比为0％-40％，NbC、Nb/VC析出相的平均尺寸为3-30μm。2. The ultrahigh temperature bearing alloy according to claim 1, characterized in that the volume percentage of NbC and Nb/VC precipitates on the BCC matrix is 0%-40%, and the average size of the NbC and Nb/VC precipitates is 3-30 μm. 3.根据权利要求1所述超高温轴承合金，其特征在于：所述超高温轴承合金在室温至1000℃组织稳定，室温硬度≥58HRC，800℃高温硬度≥51HRC，1000℃高温硬度≥49HRC。3. The ultra-high temperature bearing alloy according to claim 1 is characterized in that: the ultra-high temperature bearing alloy has a stable structure from room temperature to 1000°C, a room temperature hardness ≥58HRC, a high temperature hardness at 800°C ≥51HRC, and a high temperature hardness at 1000°C ≥49HRC. 4.根据权利要求1所述超高温轴承合金，其特征在于：所述超高温轴承合金在800℃具有≥2095MPa的高温压缩强度，以及≥20％的压缩工程应变；在1000℃具有≥1219MPa的高温压缩强度，以及≥30％的压缩工程应变。4. The ultra-high temperature bearing alloy according to claim 1 is characterized in that: the ultra-high temperature bearing alloy has a high temperature compressive strength of ≥2095MPa and a compressive engineering strain of ≥20% at 800°C; and has a high temperature compressive strength of ≥1219MPa and a compressive engineering strain of ≥30% at 1000°C. 5.根据权利要求1所述超高温轴承合金，其特征在于：其合金的化学成分按重量百分含量包含：C 0.02-0.05％，Cr16.0％-19.0％，Mo 30.0％-35.0％，Nb30.0-34.0％，V 16.5％-18.5％和不可避免的杂质。5. The ultra-high temperature bearing alloy according to claim 1 is characterized in that the chemical composition of the alloy comprises, by weight percentage, C 0.02-0.05%, Cr 16.0%-19.0%, Mo 30.0%-35.0%, Nb 30.0-34.0%, V 16.5%-18.5% and inevitable impurities. 6.根据权利要求1所述超高温轴承合金，其特征在于：其合金的化学成分按重量百分含量包含：C 0.6-0.8％，Cr16.0％-19.0％，Mo 30.0％-35.0％，Nb30.0-34.0％，V 16.5％-18.5％和不可避免的杂质。6. The ultra-high temperature bearing alloy according to claim 1 is characterized in that the chemical composition of the alloy comprises, by weight percentage: C 0.6-0.8%, Cr 16.0%-19.0%, Mo 30.0%-35.0%, Nb 30.0-34.0%, V 16.5%-18.5% and inevitable impurities. 7.根据权利要求1所述超高温轴承合金，其特征在于：其合金的化学成分按重量百分含量包含：C 3.0-4.0％，Cr16.0％-19.0％，Mo 30.0％-35.0％，Nb30.0-34.0％，V 16.5％-18.5％和不可避免的杂质。7. The ultra-high temperature bearing alloy according to claim 1 is characterized in that the chemical composition of the alloy comprises, by weight percentage, C 3.0-4.0%, Cr 16.0%-19.0%, Mo 30.0%-35.0%, Nb 30.0-34.0%, V 16.5%-18.5% and inevitable impurities. 8.根据权利要求1所述超高温轴承合金，其特征在于：通过真空感应熔炼方法或真空电弧熔炼方法制备，合金进行8-10次反复熔炼凝固来保障组织均匀性。8. The ultrahigh temperature bearing alloy according to claim 1 is characterized in that it is prepared by a vacuum induction melting method or a vacuum arc melting method, and the alloy is repeatedly melted and solidified 8-10 times to ensure the uniformity of the structure. 9.根据权利要求8所述超高温轴承合金，其特征在于：将按照成分比例配制好的原料放入DHL400高真空非自耗电弧炉，抽真空至5×10-3Pa后向真空室通氩气气体至腔室压力为-0.05MPa，对原料进行电弧熔炼，每个工位的合金锭在完全熔化之后保持1min，熔炼温度保持在2100℃-2200℃之间，熔炼结束后随水冷铜模冷却。9. The ultra-high temperature bearing alloy according to claim 8 is characterized in that: the raw materials prepared according to the component ratio are placed in a DHL400 high vacuum non-consumable arc furnace, and after evacuating to 5× 10-3 Pa, argon gas is passed into the vacuum chamber until the chamber pressure is -0.05MPa, and the raw materials are arc melted. The alloy ingot at each station is kept for 1 minute after being completely melted, and the melting temperature is kept between 2100℃ and 2200℃. After the melting is completed, it is cooled with a water-cooled copper mold.
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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR20180035750A (en) * 2018-03-22 2018-04-06 한국과학기술원 In-situ strengthened high entropy powder, alloy thereof and method of manufacturing the same
CN113462959A (en) * 2021-05-31 2021-10-01 钢铁研究总院 Long-life high-reliability large-atom alloying high-temperature bearing steel and manufacturing method thereof
CN114606421A (en) * 2022-03-01 2022-06-10 有研工程技术研究院有限公司 Refractory high-entropy alloy and preparation method thereof

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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR20180035750A (en) * 2018-03-22 2018-04-06 한국과학기술원 In-situ strengthened high entropy powder, alloy thereof and method of manufacturing the same
CN113462959A (en) * 2021-05-31 2021-10-01 钢铁研究总院 Long-life high-reliability large-atom alloying high-temperature bearing steel and manufacturing method thereof
CN114606421A (en) * 2022-03-01 2022-06-10 有研工程技术研究院有限公司 Refractory high-entropy alloy and preparation method thereof

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