CN113846247A - W-Mo-Co reinforced high-temperature alloy hot-rolled bar and preparation method thereof - Google Patents
W-Mo-Co reinforced high-temperature alloy hot-rolled bar and preparation method thereof Download PDFInfo
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- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 78
- 239000000956 alloy Substances 0.000 title claims abstract description 78
- 229910017313 Mo—Co Inorganic materials 0.000 title claims abstract description 23
- 238000002360 preparation method Methods 0.000 title claims abstract description 15
- 238000005242 forging Methods 0.000 claims abstract description 34
- 238000000034 method Methods 0.000 claims abstract description 32
- 238000003723 Smelting Methods 0.000 claims abstract description 26
- 238000005098 hot rolling Methods 0.000 claims abstract description 18
- 230000006698 induction Effects 0.000 claims abstract description 17
- 230000001681 protective effect Effects 0.000 claims abstract description 17
- 239000013078 crystal Substances 0.000 claims abstract description 13
- 239000012535 impurity Substances 0.000 claims abstract description 13
- 238000004519 manufacturing process Methods 0.000 claims abstract description 10
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 8
- 238000005096 rolling process Methods 0.000 claims description 32
- 238000010438 heat treatment Methods 0.000 claims description 31
- 238000001816 cooling Methods 0.000 claims description 30
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 20
- 239000006104 solid solution Substances 0.000 claims description 20
- 229910000831 Steel Inorganic materials 0.000 claims description 13
- 238000005266 casting Methods 0.000 claims description 13
- 239000010959 steel Substances 0.000 claims description 13
- GWEVSGVZZGPLCZ-UHFFFAOYSA-N Titan oxide Chemical compound O=[Ti]=O GWEVSGVZZGPLCZ-UHFFFAOYSA-N 0.000 claims description 12
- BYFGZMCJNACEKR-UHFFFAOYSA-N aluminium(i) oxide Chemical compound [Al]O[Al] BYFGZMCJNACEKR-UHFFFAOYSA-N 0.000 claims description 12
- 239000002893 slag Substances 0.000 claims description 12
- 238000000137 annealing Methods 0.000 claims description 10
- 229910052786 argon Inorganic materials 0.000 claims description 10
- 238000009792 diffusion process Methods 0.000 claims description 10
- 238000004321 preservation Methods 0.000 claims description 10
- 230000032683 aging Effects 0.000 claims description 7
- 238000002844 melting Methods 0.000 claims description 7
- 230000008018 melting Effects 0.000 claims description 7
- 229910004261 CaF 2 Inorganic materials 0.000 claims description 6
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 6
- 229910010413 TiO 2 Inorganic materials 0.000 claims description 6
- 230000007547 defect Effects 0.000 claims description 6
- 238000012840 feeding operation Methods 0.000 claims description 6
- 229910002804 graphite Inorganic materials 0.000 claims description 6
- 239000010439 graphite Substances 0.000 claims description 6
- 239000002994 raw material Substances 0.000 claims description 6
- 238000001514 detection method Methods 0.000 claims description 5
- 238000013461 design Methods 0.000 claims description 4
- 238000005204 segregation Methods 0.000 claims description 4
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 claims description 2
- 229910052698 phosphorus Inorganic materials 0.000 claims description 2
- 239000011574 phosphorus Substances 0.000 claims description 2
- 229910000601 superalloy Inorganic materials 0.000 claims 2
- 230000003009 desulfurizing effect Effects 0.000 claims 1
- 238000010304 firing Methods 0.000 claims 1
- 238000012423 maintenance Methods 0.000 abstract description 2
- 239000000463 material Substances 0.000 description 6
- 239000000203 mixture Substances 0.000 description 4
- 238000004140 cleaning Methods 0.000 description 3
- 238000006477 desulfuration reaction Methods 0.000 description 3
- 230000023556 desulfurization Effects 0.000 description 3
- 238000005498 polishing Methods 0.000 description 3
- 229910000851 Alloy steel Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 238000010079 rubber tapping Methods 0.000 description 2
- 238000005728 strengthening Methods 0.000 description 2
- 238000009864 tensile test Methods 0.000 description 2
- 230000009286 beneficial effect Effects 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 230000018109 developmental process Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
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- 229910052721 tungsten Inorganic materials 0.000 description 1
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- 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
- C22C19/055—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 20% but less than 30%
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
- B21B37/74—Temperature control, e.g. by cooling or heating the rolls or the product
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21K—MAKING FORGED OR PRESSED METAL PRODUCTS, e.g. HORSE-SHOES, RIVETS, BOLTS OR WHEELS
- B21K29/00—Arrangements for heating or cooling during processing
-
- 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
- C21D9/0075—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for rods of limited length
-
- 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
- C22B9/00—General processes of refining or remelting of metals; Apparatus for electroslag or arc remelting of metals
- C22B9/16—Remelting metals
- C22B9/18—Electroslag remelting
-
- 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
- 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
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/25—Process efficiency
Abstract
The invention discloses a high-temperature alloy hot-rolled bar, in particular to a W-Mo-Co reinforced high-temperature alloy hot-rolled bar and a preparation method thereof, belonging to the technical field of metallurgical production. The W-Mo-Co reinforced high-temperature alloy hot-rolled bar and the preparation method thereof have the advantages of high quality stability, good tissue uniformity, strong high-temperature durability and high strength maintenance. The W-Mo-Co reinforced high-temperature alloy hot-rolled bar comprises the following components in parts by weight: 0.03% -0.08%; cr: 17.50% -21.00%; w: 5.50% -7.50%; 3.00 to 5.00 percent of Mo; 1.80 to 2.35 percent of Al; ti: 1.2% -1.50%; 6.00 to 9.00 percent of Co; mg: 0.003 to 0.01 percent; fe: less than or equal to 5.00 percent; the balance is Ni and impurities, the internal structure of the finished hot rolled bar is uniform, the grain size is finer than grade 7, and the internal structure is free of mixed crystal structure. The preparation method adopts a vacuum induction smelting and protective atmosphere electroslag remelting duplex smelting process to prepare ingot billets, and small-sized alloy bars with uniform internal structure, grain size smaller than 7 grade and no mixed crystal structure inside are obtained by forging and cogging the ingots and hot rolling the ingots by a two-fire process.
Description
Technical Field
The invention relates to a high-temperature alloy hot-rolled bar, in particular to a W-Mo-Co reinforced high-temperature alloy hot-rolled bar, belonging to the technical field of metallurgical production. The invention also provides a preparation method of the W-Mo-Co reinforced high-temperature alloy hot-rolled bar.
Background
The small-size high-temperature alloy hot-rolled bar is mainly applied to manufacturing fasteners, blades and the like for aerospace. In practical application, the small-size high-temperature alloy hot-rolled bar has important problems of poor tissue uniformity, unstable performance and the like for a long time, so that the product has low qualification rate and poor quality stability, and the development and production requirements of a new generation of aerospace vehicles and aero-engines are severely restricted. With the increase of the demand of high-temperature alloy rod and wire products for domestic aviation fasteners, the improvement of the product quality and the process upgrading of small-size high-temperature alloy hot-rolled rods are needed.
Disclosure of Invention
The technical problem to be solved by the invention is as follows: provides a W-Mo-Co reinforced high-temperature alloy hot-rolled bar which has high quality stability, good structure uniformity and strong bar high-temperature durability and keeps high strength. The invention also provides a preparation method of the W-Mo-Co reinforced high-temperature alloy hot-rolled bar.
The technical scheme adopted for solving the technical problems is as follows: the W-Mo-Co reinforced high-temperature alloy hot rolled bar comprises the following components in parts by weight,
c: 0.03% -0.08%; cr: 17.50% -21.00%; w: 5.50% -7.50%; 3.00 to 5.00 percent of Mo; 1.80 to 2.35 percent of Al; ti: 1.2% -1.50%; 6.00 to 9.00 percent of Co; mg: 0.003 to 0.01 percent; fe: less than or equal to 5.00 percent; the balance of Ni and impurities,
the finished hot rolled bar has uniform internal structure, grain size smaller than 7 grade, and no mixed crystal structure inside.
Furthermore, the impurities comprise the following components in parts by weight, wherein Si is less than or equal to 0.35%; mn is less than or equal to 0.35 percent; p is less than or equal to 0.015 percent; s is less than or equal to 0.010 percent; b: less than or equal to 0.005 percent and less than or equal to 0.02 percent of Ce.
A preparation method for the W-Mo-Co reinforced high-temperature alloy hot rolled steel is characterized in that a vacuum induction smelting and protective atmosphere electroslag remelting duplex smelting process is adopted to prepare an ingot casting billet, and a small-size alloy bar with uniform internal structure, grain size smaller than 7 grade and no mixed crystal structure inside is obtained by forging and cogging an ingot and hot rolling with two heating processes.
The preferable mode of the scheme is that during vacuum induction smelting, alloy raw materials are proportioned according to the proportion of the alloy components, a 6t vacuum induction furnace is adopted for smelting, the content of alloy elements is adjusted in the smelting process, the mass percent of the alloy elements meets the design requirement of the components, steel is tapped after the components are qualified, an electrode rod with the diameter of 240mm is cast, the casting temperature is 1510 +/-10 ℃, and argon protection is adopted during casting.
Further, when the protective atmosphere electroslag remelting is carried out, the surface of the cast electrode bar is cleaned and polished, then an argon protective atmosphere electroslag furnace is adopted for electroslag remelting, a remelting crystallizer adopts a phi 360mm crystallizer which is convenient for dephosphorization, desulfurization and deoxidation and improves the compactness of steel ingot tissues,
the specific process of electroslag remelting is that graphite electrodes are electrified to melt slag, electrode rods required by electroslag remelting are switched, the voltage is adjusted to 60V after electrification and arcing, the current is controlled to be 7000A-8100A, the melting speed is controlled to be 5.5-6.5kg/min, and the alloy ingot with compact structure, no defect and uniform components is obtained by carrying out current reduction feeding operation at the later stage of electroslag.
The preferable mode of the scheme is that the specific proportion of slag used in electroslag remelting is as follows, CaO: 7%, Al2O 3: 20%, CaF 2: 70 percent of TiO2 and 3 percent of TiO 2.
Further, the preparation method also comprises a diffusion annealing process, wherein the ingot is firstly subjected to heat preservation for 48 hours at 1180 ℃ for diffusion annealing before forging, so that the element segregation in the alloy ingot is reduced, and the component consistency is improved.
The preferable mode of the scheme is that when forging and cogging, a 4-ton electro-hydraulic hammer is adopted to forge an electroslag ingot with the diameter of 360mm into a square billet with the diameter of 55 mm-60 mm, the cogging temperature is more than or equal to 1100 ℃, the finish forging temperature is more than or equal to 920 ℃, when forging is required to be carried out for multiple times, the remelting heat preservation is required to be carried out so as to ensure that the forging temperature is not less than 920 ℃, the remelting heat preservation time is 40-60min each time, and the cooling is carried out in an air cooling mode after forging.
Further, during hot rolling, a 280 rolling mill is adopted for carrying out two-fire process rolling, the heating temperature during hot rolling is 1130-1160 ℃, the starting rolling temperature is not less than 1080 ℃, the final rolling temperature is not less than 950 ℃,
wherein the first heating time is 2 hours, and the round bar with the diameter of 30-35mm is rolled; heating for 30min for the second heating time, finally rolling to obtain a bar with the diameter of 12-22 mm, wherein the rolling linear speed is 2.0-2.5m/s, and finally carrying out grain size detection on the obtained bar according to GB/T6394.
Furthermore, the bar after hot rolling needs to be strengthened through two heat treatment systems of solid solution and aging,
the parameters of solid solution and aging heat treatment are that solid solution is carried out at 1080 +/-10 ℃ for 2 h/air cooling, air cooling is carried out at 900 +/-10 ℃/5h, or solid solution is carried out at 990 +/-10 ℃ for 4 h/air cooling, and air cooling is carried out at 700 +/-10 ℃/16 h.
The invention has the beneficial effects that: according to the technical scheme provided by the application, ingot casting billets are prepared by adopting a vacuum induction smelting and protective atmosphere electroslag remelting duplex smelting process, and then the ingot casting is forged and cogging, and hot rolling is carried out by two times of heating, so that the alloy steel comprises the following components in parts by weight: 0.03% -0.08%; cr: 17.50% -21.00%; w: 5.50% -7.50%; 3.00 to 5.00 percent of Mo; 1.80 to 2.35 percent of Al; ti: 1.2% -1.50%; 6.00 to 9.00 percent of Co; mg: 0.003 to 0.01 percent; fe: less than or equal to 5.00 percent; the balance is Ni and impurities, the internal structure is uniform, the grain size is finer than grade 7, and the inside of the small-sized alloy bar has no mixed crystal structure. Therefore, the technical problems of poor tissue uniformity and unstable performance of the high-temperature alloy hot-rolled bar existing in the prior art for a long time are solved, the requirement of practical production is met, and the high-temperature alloy hot-rolled bar which is strong in quality stability, good in tissue uniformity, strong in high-temperature durability and high in strength is provided for fasteners and blades for aerospace.
Drawings
FIG. 1 is a microstructure of a bar according to example 1 of the present invention;
FIG. 2 is a microstructure diagram of a bar of example 2 of the present invention.
Detailed Description
In order to solve the technical problems in the prior art, the invention provides the W-Mo-Co reinforced high-temperature alloy hot rolled bar which has high quality stability, good structure uniformity, strong bar high-temperature durability and high strength maintenance, and the preparation method for the W-Mo-Co reinforced high-temperature alloy hot rolled bar. The W-Mo-Co reinforced high-temperature alloy hot-rolled bar comprises the following components in parts by weight: 0.03% -0.08%; cr: 17.50% -21.00%; w: 5.50% -7.50%; 3.00 to 5.00 percent of Mo; 1.80 to 2.35 percent of Al; ti: 1.2% -1.50%; 6.00 to 9.00 percent of Co; mg: 0.003 to 0.01 percent; fe: less than or equal to 5.00 percent; the balance is Ni and impurities, the internal structure of the finished hot rolled bar is uniform, the grain size is finer than grade 7, and the internal structure is free of mixed crystal structure. The preparation method adopts a vacuum induction smelting and protective atmosphere electroslag remelting duplex smelting process to prepare ingot billets, and small-sized alloy bars with uniform internal tissues, grain sizes smaller than 7 grades and no mixed crystal tissues inside are obtained by forging and cogging the ingots and hot rolling the ingots by a two-fire process. According to the technical scheme provided by the application, ingot casting billets are prepared by adopting a vacuum induction smelting and protective atmosphere electroslag remelting duplex smelting process, and then the ingot casting is forged and cogging, and hot rolling is carried out by two times of heating, so that the alloy steel comprises the following components in parts by weight: 0.03% -0.08%; cr: 17.50% -21.00%; w: 5.50% -7.50%; 3.00 to 5.00 percent of Mo; 1.80 to 2.35 percent of Al; ti: 1.2% -1.50%; 6.00 to 9.00 percent of Co; mg: 0.003 to 0.01 percent; fe: less than or equal to 5.00 percent; the balance is Ni and impurities, the internal structure is uniform, the grain size is finer than grade 7, and the inside of the small-sized alloy bar has no mixed crystal structure. Therefore, the technical problems of poor tissue uniformity and unstable performance of the high-temperature alloy hot-rolled bar existing in the prior art for a long time are solved, the requirement of practical production is met, and the high-temperature alloy hot-rolled bar which is strong in quality stability, good in tissue uniformity, strong in high-temperature durability and high in strength is provided for fasteners and blades for aerospace.
In the embodiment, in order to provide a high-temperature alloy hot-rolled bar with high quality in terms of composition, the impurities comprise the following components in parts by weight, wherein Si is less than or equal to 0.35%; mn is less than or equal to 0.35 percent; p is less than or equal to 0.015 percent; s is less than or equal to 0.010 percent; b: less than or equal to 0.005 percent and less than or equal to 0.02 percent of Ce.
Correspondingly, in order to obtain a high-temperature alloy hot-rolled bar which is strong in quality stability, good in tissue uniformity, strong in bar high-temperature durability and high in strength from a preparation process, alloy raw materials are proportioned according to the alloy component proportion during vacuum induction smelting, a 6t vacuum induction furnace is adopted for smelting, the content of alloy elements is adjusted during smelting, the mass percentage of the alloy elements meets the component design requirement, steel is tapped after the components are qualified, an electrode bar with the diameter of 240mm is cast, the casting temperature is 1510 +/-10 ℃, and argon protection is adopted during casting. When in electroslag remelting in protective atmosphere, the surface of a cast electrode bar is cleaned and polished, then electroslag remelting is carried out by adopting an argon protective atmosphere electroslag furnace, a remelting crystallizer adopts a phi 360mm crystallizer which is convenient for dephosphorization, desulfurization and deoxidation and improves the compactness of a steel ingot structure,
in the specific process of electroslag remelting, after slag is melted by electrifying a graphite electrode, an electrode bar required by electroslag remelting is switched, the voltage is adjusted to 60V after electrification and arcing, the current is controlled to be 7000A-8100A, the melting speed is controlled to be 5.5-6.5kg/min, and the alloy ingot with compact structure, no defect and uniform components is obtained by carrying out current reduction feeding operation in the later stage of electroslag. And slag used for electroslag remelting is controlled according to the following mixture ratio, namely CaO: 7%, Al2O 3: 20%, CaF 2: 70 percent of TiO2 and 3 percent of TiO 2.
When the uniformity of the internal structure of the material with high quality is obtained, the preparation method further comprises a diffusion annealing process, wherein the ingot is subjected to heat preservation for 48 hours at 1180 ℃ for diffusion annealing before forging, so that the element segregation in the alloy ingot is reduced, and the component consistency is improved. Meanwhile, when forging and cogging, forging an electroslag ingot with the diameter of 360mm into a square billet with the diameter of 55mm to 60mm by adopting a 4-ton electro-hydraulic hammer, wherein the cogging temperature is more than or equal to 1100 ℃, the finish forging temperature is more than or equal to 920 ℃, when forging is required for multiple times, the remelting and heat preservation are required to be carried out so as to ensure that the forging temperature is not less than 920 ℃, the time for remelting and heat preservation is 40-60min each time, and cooling is carried out in an air cooling mode after forging. During hot rolling, a 280 rolling mill is adopted for carrying out two-firing-time process rolling, the heating temperature during hot rolling is 1130-1160 ℃, the starting temperature is not less than 1080 ℃, the final rolling temperature is not less than 950 ℃,
wherein the first heating time is 2 hours, and the round bar with the diameter of 30-35mm is rolled; heating for 30min for the second heating time, finally rolling to obtain a bar with the diameter of 12-22 mm, wherein the rolling linear speed is 2.0-2.5m/s, and finally carrying out grain size detection on the obtained bar according to GB/T6394. The hot rolled bar is further strengthened by two heat treatment systems of solid solution and aging, wherein the parameters of the solid solution and the aging are that solid solution is carried out at 1080 +/-10 ℃ for 2 h/air cooling, air cooling is carried out at 900 +/-10 ℃/5h, or solid solution is carried out at 990 +/-10 ℃ for 4 h/air cooling, and air cooling is carried out at 700 +/-10 ℃/16 h.
DETAILED DESCRIPTION OF EMBODIMENT (S) OF INVENTION
The invention aims to provide a W-Mo-Co reinforced small-specification high-quality high-temperature alloy hot rolled bar for aerospace and a manufacturing process thereof, wherein a vacuum induction smelting and protective atmosphere electroslag remelting duplex smelting process is adopted, so that the accurate control of alloy components can be ensured, the purity of the alloy is improved, and the content of non-metal impurities and gas is reduced; the small-size alloy bar hot rolled by forging cogging and two-fire process has uniform structure, grain size smaller than 7 grade and no mixed crystal structure, so that the prepared alloy bar greatly improves the durability of the material and keeps high strength on the basis of meeting the requirement of aviation standard, and meets the requirement of aviation parts. The invention is mainly realized by the following technical scheme:
a W-Mo-Co reinforced small-specification high-quality high-temperature alloy hot-rolled bar for aerospace comprises the following components in percentage by weight:
c: 0.03% -0.08%; cr: 17.50% -21.00%; w: 5.50% -7.50%; 3.00 to 5.00 percent of Mo; 1.80 to 2.35 percent of Al; ti: 1.2% -1.50%; 6.00 to 9.00 percent of Co; mg: 0.003 to 0.01 percent; fe: less than or equal to 5.00 percent; the balance being Ni and impurities.
In order to improve the high-temperature durability and maintain the high strength of the alloy bar, the invention adds the grain boundary strengthening element Mg on the basis of improving the alloy solid solution strengthening elements W, Mo and Co, and further controls the content of impurity elements. In order to better realize the invention, the mass percentages of the impurity elements are as follows:
Si:≤0.35％；Mn:≤0.35％；P:≤0.015％；S:≤0.010％；；B：≤0.005％；Ce:≤0.02％。
the W-Mo-Co reinforced small-specification high-quality high-temperature alloy hot-rolled bar for aerospace is prepared by the following steps:
1. vacuum induction smelting: the alloy raw materials are proportioned according to the proportion of the alloy components, a 6t vacuum induction furnace is adopted for smelting, the content of alloy elements is adjusted in the smelting process, the mass percentage of the alloy elements meets the design requirements of the components, steel can be discharged and electrode rods with the diameter of 240mm can be cast after the components are qualified, the casting temperature is 1510 +/-10 ℃, and argon is adopted for protection during casting.
2. And (3) protective atmosphere electroslag remelting, namely cleaning and polishing the surface of the cast electrode bar, and then performing electroslag remelting by adopting an argon protective atmosphere electroslag furnace, wherein a remelting crystallizer is in a phi 360mm range, so that phosphorus is removed, desulfurization and deoxidation are performed, and the compactness of a steel ingot structure is improved. The specific proportion of the slag is CaO: 7%, Al2O 3: 20%, CaF 2: 70 percent of TiO2 and 3 percent of TiO 2. After graphite electrodes are electrified to melt slag, electrode rods required by electroslag remelting are switched, after electrification and arc striking, the voltage is adjusted to 60V, the current is 7000A-8100A, the melting speed is 5.5-6.5kg/min, and the current reduction feeding operation is carried out at the later stage of electroslag, so that an alloy ingot with compact structure, no defect and uniform components is further formed.
3. And (3) diffusion annealing: before forging, the ingot needs to be kept warm for 48h at 1180 ℃ for diffusion annealing, and the main purpose is to further reduce the element segregation in the alloy ingot and improve the component consistency.
4. An electroslag ingot with the diameter of 360mm is forged into a square billet with the diameter of 55mm to 60mm by adopting a 4-ton electro-hydraulic hammer. The forging temperature is more than or equal to 1100 ℃, the finish forging temperature is more than or equal to 920 ℃, and because the high-temperature alloy has large deformation resistance and is easy to crack when being forged at the temperature of less than 920 ℃, the time of returning to the furnace and keeping the temperature is 40-60min when being forged for multiple times, and the cooling is carried out in an air cooling mode after being forged.
5. Hot rolling: and (3) carrying out two-heating-time process rolling by adopting a 280 rolling mill, wherein the heating temperature during hot rolling is 1130-1160 ℃, the initial rolling temperature is more than or equal to 1080 ℃, the final rolling temperature is more than or equal to 950 ℃, the first heating and heat preservation time is 2 hours, the round bar with the diameter of 30-35mm is rolled, the second heating and heat preservation time is 30 minutes, the bar with the diameter of 12-22 mm is finally rolled, and the rolling linear speed during rolling is 2.0-2.5 m/s. And carrying out grain size detection on the obtained bar according to GB/T6394.
6. The bar after hot rolling can be strengthened through two heat treatment systems of solid solution and aging, wherein the solid solution is carried out at 1080 +/-10 ℃ for 2 h/air cooling, and the air cooling is carried out at 900 +/-10 ℃/5 h; secondly, solid solution is carried out at 990 +/-10 ℃ for 4 h/air cooling, and air cooling is carried out at 700 +/-10 ℃/16 h. And (3) detecting the mechanical properties of the bars obtained after the two heat treatments, wherein the detection standards are GB/T228 (metal tensile test method), GB/T2039 (metal tensile creep and endurance test method) and GB/T4338 (metal material high-temperature tensile test method).
Example one
The high-quality high-temperature alloy hot-rolled bar with the diameter of 22mm for aerospace reinforced by W-Mo-Co is prepared in the first embodiment.
1. Alloy raw materials are loaded into a crucible according to the component proportion, 6t vacuum induction melting is adopted, steel can be tapped after the components are qualified, the tapping temperature is 1508 ℃, and electrode rods with the diameter of 240mm are cast.
2. Cleaning and polishing the surface of the electrode bar cast in the step 1, carrying out electroslag remelting in an argon protective atmosphere electroslag furnace, wherein the slag mixture ratio is CaO: 7%, Al2O 3: 20%, CaF 2: 70 percent of TiO2 and 3 percent of TiO 2. And after the graphite electrode is electrified to melt the slag, switching electrode rods required by electroslag remelting, adjusting the voltage to 60V and the current to 7500A after electrification and arcing, carrying out current reduction feeding operation at the later stage of electroslag, and demoulding to obtain the phi 360mm alloy ingot with compact structure, no defect and uniform components.
3. And (3) keeping the temperature of the ingot obtained in the step (2) at 1180 ℃ for 48 hours for diffusion annealing.
4. And (3) forging the electroslag ingot with the diameter of 360mm obtained in the step (3) into a square billet with the diameter of 60 multiplied by 60mm by adopting a 4-ton electro-hydraulic hammer, wherein the forging temperature is 1100 ℃, and the final forging temperature is 920 ℃.
5. And (3) rolling the square billet obtained in the step (4) by a 280 rolling mill for two times at a rolling line speed of 2.5m/s, keeping the temperature for 2h at 1140 ℃ during the first time rolling to obtain a round bar with the diameter of 35mm, keeping the temperature for 30min at 1140 ℃ during the second time rolling to finally obtain a round bar with the diameter of 22mm, and detecting the grain size of the obtained bar according to GB/T6394, wherein the grain size is 9 grade, the bar tissue is uniform and has no mixed crystal tissue as shown in figure 1.
6. The bar material after hot rolling in the step 5 is strengthened by adopting the following two heat treatment systems,
i: solid solution is carried out at 1080 ℃ for 2 h/air cooling, and air cooling is carried out at 900 ℃/5 h;
II: air cooling at 990 ℃ for 4h of solid solution and at 700 ℃/16h,
the mechanical properties of the bars obtained after the two heat treatments are detected, and are shown in table 1, and the internal metallographic structure is shown in fig. 1.
Table 1: example one mechanical Properties of bars after Heat treatment
The alloy bar prepared in the example 1 can greatly improve the endurance of the material and keep high strength on the basis of meeting the requirement of aviation standard, and the structure performance of the alloy bar can meet the requirement of aviation parts.
Example two
The high-quality high-temperature alloy hot-rolled bar with the diameter of 18mm for aerospace reinforced by W-Mo-Co prepared in the second embodiment.
1. Alloy raw materials are loaded into a crucible according to the component proportion, 6t vacuum induction melting is adopted, steel can be tapped after the components are qualified, the tapping temperature is 1510 ℃, and electrode rods with the diameter of 240mm are cast.
2. Cleaning and polishing the surface of the electrode bar cast in the step 1, carrying out electroslag remelting in an argon protective atmosphere electroslag furnace, wherein the slag mixture ratio is CaO: 7%, Al2O 3: 20%, CaF 2: 70 percent of TiO2 and 3 percent of TiO 2. And after the graphite electrode is electrified to melt the slag, switching electrode rods required by electroslag remelting, adjusting the voltage to 60V after electrification and arcing, regulating the current to 7200A and the melting speed to 5.8kg/min, carrying out current reduction feeding operation at the later stage of electroslag, and demoulding to obtain the phi 360mm alloy ingot with compact structure, no defect and uniform components.
3. And (3) keeping the temperature of the ingot obtained in the step (2) at 1180 ℃ for 48 hours for diffusion annealing.
4. And (3) forging the electroslag ingot with the diameter of 360mm obtained in the step (3) into a square billet with the diameter of 55 x 55mm by adopting a 4-ton electro-hydraulic hammer, wherein the forging temperature is 1100 ℃, and the finish forging temperature is 920 ℃.
5. And (3) rolling the square billet obtained in the step (4) by a 280 rolling mill for two times at a rolling line speed of 2.2m/s, keeping the temperature for 2h at 1160 ℃ during the first time rolling to obtain a round bar with the diameter of 30mm, keeping the temperature for 30min at 1140 ℃ during the second time rolling to finally obtain a round bar with the diameter of 18mm, and detecting the grain size of the obtained bar according to GB/T6394, wherein the grain size is 10 grade, the bar tissue is uniform and has no mixed crystal tissue as shown in figure 2.
6. The bar material after hot rolling in the step 5 is strengthened by adopting the following two heat treatment systems,
i: solid solution is carried out at 1080 ℃ for 2 h/air cooling, and air cooling is carried out at 900 ℃/5 h;
II: air cooling at 990 ℃ for 4h of solid solution and at 700 ℃/16h,
the mechanical properties of the bars obtained after the two heat treatments are detected, and are shown in table 2, and the internal metallographic structure is shown in fig. 2.
Table 2: EXAMPLE two mechanical Properties of bars after Heat treatment
The alloy bar prepared by the second embodiment can greatly improve the endurance of the material and keep high strength on the basis of meeting the requirement of aviation standard, and the structure performance of the alloy bar can meet the requirement of aviation parts.
Claims (10)
1. A W-Mo-Co strengthened high-temperature alloy hot-rolled bar is characterized in that: the W-Mo-Co reinforced high-temperature alloy hot-rolled bar comprises the following components in parts by weight,
c: 0.03% -0.08%; cr: 17.50% -21.00%; w: 5.50% -7.50%; 3.00 to 5.00 percent of Mo; 1.80 to 2.35 percent of Al; ti: 1.2% -1.50%; 6.00 to 9.00 percent of Co; mg: 0.003 to 0.01 percent; fe: less than or equal to 5.00 percent; the balance of Ni and impurities,
the finished hot rolled bar has uniform internal structure, grain size smaller than 7 grade, and no mixed crystal structure inside.
2. The W-Mo-Co strengthened superalloy hot rolled steel product of claim 1, wherein: the impurities comprise the following components in parts by weight, wherein Si is less than or equal to 0.35%; mn is less than or equal to 0.35 percent; p is less than or equal to 0.015 percent; s is less than or equal to 0.010 percent; b: less than or equal to 0.005 percent and less than or equal to 0.02 percent of Ce.
3. A method for producing a W-Mo-Co strengthened superalloy hot rolled steel product according to claim 2, comprising: the preparation method adopts a vacuum induction smelting and protective atmosphere electroslag remelting duplex smelting process to prepare ingot billets, and small-sized alloy bars with uniform internal tissues, grain sizes smaller than 7 grades and no mixed crystal tissues inside are obtained by forging and cogging the ingots and hot rolling the ingots by a two-fire process.
4. The production method according to claim 3, characterized in that: during vacuum induction smelting, alloy raw materials are proportioned according to the proportion of the alloy components, a 6t vacuum induction furnace is adopted for smelting, the content of alloy elements is adjusted in the smelting process, the mass percent of the alloy elements meets the design requirements of the components, steel is discharged after the components are qualified, electrode rods with the diameter of 240mm are cast, the casting temperature is 1510 +/-10 ℃, and argon protection is adopted during casting.
5. The method of claim 4, wherein: when the electroslag remelting is carried out in the protective atmosphere, the surface of a cast electrode bar is cleaned and polished, then the electroslag remelting is carried out by adopting an argon protective atmosphere electroslag furnace, a remelting crystallizer adopts a phi 360mm crystallizer which is convenient for removing phosphorus, desulfurizing and deoxidizing and improving the compactness of a steel ingot structure,
in the specific process of electroslag remelting, after slag is melted by electrifying a graphite electrode, an electrode bar required by electroslag remelting is switched, the voltage is adjusted to 60V after electrification and arcing, the current is controlled to be 7000A-8100A, the melting speed is controlled to be 5.5-6.5kg/min, and the alloy ingot with compact structure, no defect and uniform components is obtained by carrying out current reduction feeding operation in the later stage of electroslag.
6. The method of claim 5, wherein: the specific proportion of slag used for electroslag remelting is as follows: 7%, Al2O 3: 20%, CaF 2: 70 percent of TiO2 and 3 percent of TiO 2.
7. The production method according to claim 3, 4, 5 or 6, characterized in that: the preparation method also comprises a diffusion annealing process, wherein the ingot is subjected to diffusion annealing after being kept at 1180 ℃ for 48 hours before forging, so that the element segregation in the alloy ingot is reduced, and the component consistency is improved.
8. The method of claim 7, wherein: when forging and cogging, forging an electroslag ingot with the diameter of 360mm into a square billet with the diameter of 55 mm-60 mm by adopting a 4-ton electro-hydraulic hammer, wherein the cogging temperature is more than or equal to 1100 ℃, the finish forging temperature is more than or equal to 920 ℃, when forging is required for multiple times, returning to a furnace for heat preservation is required to ensure that the forging temperature is not less than 920 ℃, the time for returning to the furnace for heat preservation is 40-60min each time, and cooling in an air cooling mode after forging.
9. The method of claim 8, wherein: when in hot rolling, a 280 rolling mill is adopted for carrying out two-firing process rolling, the heating temperature during the hot rolling is 1130-1160 ℃, the starting temperature is more than or equal to 1080 ℃, the final rolling temperature is more than or equal to 950 ℃,
wherein the first heating time is 2 hours, and the round bar with the diameter of 30-35mm is rolled; heating for 30min for the second heating time, finally rolling to obtain a bar with the diameter of 12-22 mm, wherein the rolling linear speed is 2.0-2.5m/s, and finally carrying out grain size detection on the obtained bar according to GB/T6394.
10. The method of claim 9, wherein: the hot rolled bar needs to be strengthened by two heat treatment systems of solid solution and aging,
the parameters of solid solution and aging heat treatment are that solid solution is carried out at 1080 +/-10 ℃ for 2 h/air cooling, air cooling is carried out at 900 +/-10 ℃/5h, or solid solution is carried out at 990 +/-10 ℃ for 4 h/air cooling, and air cooling is carried out at 700 +/-10 ℃/16 h.
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