CN108441705A - A kind of high intensity ni-base wrought superalloy and preparation method thereof - Google Patents

A kind of high intensity ni-base wrought superalloy and preparation method thereof Download PDF

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CN108441705A
CN108441705A CN201810222447.1A CN201810222447A CN108441705A CN 108441705 A CN108441705 A CN 108441705A CN 201810222447 A CN201810222447 A CN 201810222447A CN 108441705 A CN108441705 A CN 108441705A
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ingot
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wrought superalloy
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CN108441705B (en
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贾崇林
张丰麟
张勇
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AECC Beijing Institute of Aeronautical Materials
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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
    • C22C19/056—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
    • 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
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    • C22B9/18—Electroslag remelting
    • 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
    • C22B9/20—Arc 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
    • 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%
    • 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
    • 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
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    • Y02P10/00—Technologies related to metal processing
    • Y02P10/25—Process efficiency

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Abstract

The invention belongs to nickel base superalloy technical field, it is related to a kind of high intensity ni-base wrought superalloy and preparation method thereof.Each essential element mass percent of high intensity ni-base wrought superalloy is respectively：Cr：10.0%~25.0%；Co：10.0%~20.0%；Mo：0.1%~6.0%；W：0.1%~6.0%；Al：0.1%~6.0%；Ti：0.1%~6.0%；Nb：0.05%~1.5%；Fe：0.1%~2.0%；C：0.001%~0.10%；B：0.001%~0.05%；Zr：0.01%~0.1%；Ce：0.001%~0.10%；Mg：0.001%~0.10%；Hf：0.01%~0.5%；Ni：Surplus；And inevitable impurity element；Alloy preparation method is, high cleanliness ingot casting is obtained using vacuum induction smelting+electroslag remelting+vacuum consumable remelting, High temperature diffusion homogenizing annealing is carried out to ingot casting within the scope of 1170 DEG C~1190 DEG C, ingot casting after annealing is heated to 1130 DEG C~1160 DEG C, keep the temperature 2h~4h, it is forged into required bar with quick forging machine and is heat-treated bar sample, obtains meeting the alloy material that design of the present invention is asked.

Description

A kind of high intensity ni-base wrought superalloy and preparation method thereof
Technical field
The invention belongs to nickel base superalloy technical field, it is related to a kind of high intensity ni-base wrought superalloy and its preparation Method.
Background technology
High temperature alloy is with respect to for stainless steel, heat resisting steel, and alloying level is high by adding multiple element, Neng Gou A kind of material of about 600 DEG C or more long-term works.High temperature alloy has nickel base superalloy, iron-based high according to matrix to divide mainly Temperature alloy and cobalt base superalloy are generally divided into three classes, including wrought superalloy, cast superalloy and powder by forming technology Last metallurgy high temperature alloy.Ni-base wrought superalloy has become the rotatable parts such as aero-engine turbine disk, compressor disc can not Or scarce critical material.GH4169 is a kind of ni-base wrought superalloy that temperature in use is 650 DEG C.It is sent out than aviation as height is pushed away The development of motivation, turbine inlet temperature (TIT) is higher and higher, correspondingly, contour to elevated temperature strength, the heat resistance of turbine disk high temperature alloy The requirement of warm mechanical performance index is also higher and higher.Although powder metallurgy high-temperature alloy (for example FGH4097 alloys) is following high It pushes away a kind of selection manufactured than engine turbine disk and considers scheme, still, since powder metallurgy complex procedures, technological process are long, Thus high (the document 1 of wrought superalloy turbine disk production cost of opposite casting+forging deformation process route manufacture：Devaux A,Helstroffer A,Cormier J,Villechaise P,Douin J,Hantcherli M and Pettinari- Sturmel F.Effect of aging heat-treatment on mechanical properties of AD730TM superalloy.2014 8th International Symposium on Superalloy718and Derivatives, September 28–30,2014,Pittsburgh,USA,pp.485-499；Document 2：Raisson G.Evolution of PM nickel base superalloy processes and products.Powder Metallurgy,2008,51: 10-13.).According in recent years to (document 3 from the point of view of the progress of turbine disk high temperature alloy：Chinese patent：CN102443721A； Document 4：Francis R.Preli,David Furrer.Lessons learned from the development, application and advancement of alloy 718.2014 8th International Symposium on Superalloy 718and Derivatives, September 28-30,2014Pittsburgh, USA, pp.3-14.), it adopts With the cast forging process technology of short route low cost come to prepare high-performance deformation high temperature alloy be the side that will give priority to from now on both at home and abroad To and trend.Therefore, it is necessary to develop a kind of elevated temperature strength ratio GH4169 alloys higher, with powder metallurgy superalloy (such as FGH4097) Comprehensive performance comparable high-strength deformation high temperature alloy, the aero-engine turbine disk to meet higher mechanical property requirements make With demand and low cost manufacturing requirement.
Invention content
The purpose of the present invention is to provide a kind of high intensity ni-base wrought superalloy and preparation method thereof, meet more high-tensile strength Learn turbine disk use demand and the low cost manufacturing requirement of performance requirement.
Realize the technical scheme is that：High intensity ni-base wrought superalloy each element mass percent is respectively： Cr：10.0%~25.0%；Co：10.0%~20.0%；Mo：0.1%~6.0%；W：0.1%~6.0%；Al：0.1%~ 6.0%；Ti：0.1%~6.0%；Nb：0.05%~1.5%；Fe：0.1%~2.0%；C：0.001%~0.10%；B： 0.001%~0.05%；Zr：0.01%~0.1%；Ce：0.001%~0.10%；Mg：0.001%~0.10%；Hf： 0.01%~0.5%；Ni：Surplus.
Each essential element mass percent is respectively：Cr：14%；Co：13%；Mo：3.8%；W：4.5%；Al： 2.0%；Ti：3.5%；Nb：1.0%；Fe：1.0%；C：0.03%；B：0.02%；Zr：0.02%；Ce：0.01%；Mg： 0.01%；Hf：0.1%；Ni：Surplus.
Each essential element mass percent is respectively：Cr：16%；Co：12%；Mo：4.3%；W：3.5%；Al： 1.8%；Ti：3.8%；Nb：0.8%；Fe：0.8%；C：0.02%；B：0.015%；Zr：0.04%；Ce：0.01%；Mg： 0.01%；Hf：0.15%；Ni：Surplus.
Each essential element mass percent is respectively：Cr：15%；Co：11.5%；Mo：4.5%；W：3.0%；Al： 2.5%；Ti：3.3%；Nb：0.6%；Fe：0.9%；C：0.01%；B：0.018%；Zr：0.03%；Ce：0.01%；Mg： 0.01%；Hf：0.2%；Ni：Surplus.
The method for preparing a kind of high intensity ni-base wrought superalloy includes the following steps：
Step A：Alloyage, the then melting in vaccum sensitive stove are matched by above-mentioned element, fusion process controls fine melt Temperature：1510 DEG C~1570 DEG C；Control liquid steel refining temperature：1500 DEG C~1560 DEG C；Melting latter stage taps, and solution is poured into Alloy electrode；
Step B：The alloy electrode of gained in step A is subjected to electroslag remelting, remelting is at ESR ingot；Electroslag remelting is using pre- Slag, slag system and proportioning are CaF2:Al2O3:CaO:TiO2:MgO=67 ± 2.0:13±2.0:13±2.0:3±0.5:6± 2.0；
Step C：The ESR ingot of gained in step B is subjected to vacuum consumable remelting, obtains consumable ingot；Vacuum consumable remelting When, it is 3.0~4.0Kg/min to control molten speed；
Step D：The consumable ingot of gained in step C is carried out High temperature diffusion homogenization to move back within the scope of 1170 DEG C~1190 DEG C Fire obtains homogenizing annealing ingot；
Step E：The homogenizing annealing ingot of gained in step D is heated to 1130 DEG C~1160 DEG C, 2h~4h is kept the temperature, fast Required bar is forged into forging machine；
Step F：Sample is cut using wire cutting mode to the head of the bar of gained in step E, and sample is heat-treated, Sample system of heat treatment process is：1060 DEG C are heated to, 4h is kept the temperature, sample is then heated to 760 DEG C by oil cooling to room temperature, is protected Warm 8h is air-cooled to room temperature to get to high intensity ni-base wrought superalloy bar.
The rated pressure of the quick forging machine is 4500T.
The beneficial effects of the invention are as follows：Implement composite multi-component reinforcing by adding multiple element and rational proportion, obtains A kind of high intensity ni-base wrought superalloy, compares comparative alloy GH4169 through standard heat treatment, and invention alloy has more High mechanical properties, wherein room temperature tensile intensity improves 20%；Higher high temperature tensile strength, wherein at 700 DEG C Tensile strength improve 33%.Meanwhile invention alloy, in the case where bearing higher load, has in 650 DEG C, 700 DEG C of temperature conditions Have the lasting service life longer than GH4169 alloy, therefore, invention alloy ratio GH4169 alloys have higher heat resistance and Temperature in use.In addition, high temperature endurance performance of the invention alloy at 650 DEG C, 700 DEG C is suitable with FGH4097 alloys, but stretch strong Degree is than FGH4097 alloy highers, wherein mechanical properties ratio FGH4097 improves 10%, and the tensile strength at 700 DEG C carries High by 12%, i.e. invention alloy ratio FGH4097 has superior comprehensive performance, can meet the whirlpool of higher mechanical property requirements Wheel disc use demand；In addition, appropriate Fe is added in invention alloy, it can be the high temperature alloy (such as GH4169) containing Fe in smelting It returns to material to use as furnace charge, smelting cost is reduced from source；Importantly, invention alloy uses cast forging process route system Standby, the complicated procedures of forming compared to powder metallurgy superalloy manufactures route, and technological process is short, and total production cost reduces, and mechanical property It compares favourably with powder metallurgy superalloy or more winning, the low cost manufacturing requirement of the advanced aero engine turbine disk, tool can be met There are good economic benefit and social benefit, is suitble to promote the use of.
A kind of composition characteristic of high intensity ni-base wrought superalloy of the present invention considers following factor：
Cr in high temperature alloy mainly play a part of increase anti-oxidant and corrosion resistance, when the Cr contents in alloy not When less than 10%, the anti-oxidant and corrosion resistant effect of Cr can just give full play to, meanwhile, Cr is harmful phase in nickel base superalloy The main component of σ phases, there is the strong tendency for promoting σ phases to be formed at high temperature, this will directly deteriorate the performance of alloy. Consider improve inoxidizability, inhibit the factors such as harmful phase content on the basis of, control Cr ranging from 10.0%~ 25.0%, it is preferable that control range is 14%~17%.
Co can form continuous substitution solid solution with Ni, be the important composition element for constituting matrix solid solution, and it is strong to play solid solution Change acts on.Co can also reduce the stacking fault energy of matrix, thus can improve the croop property of alloy.But Co cannot be added Excessively, on the one hand because harmful phase can be improved from the precipitation tendency in matrix by adding excessive Co, another aspect Co belongs to strategy Property resource, it is expensive, increase manufacturing cost.Therefore, the control range for designing Co is 10.0%~20.0%, it is preferable that control System ranging from 11%~15%.
Mo and W it can play solution strengthening effect to matrix Ni, it is important that Mo and W can improve high temperature alloy creep Diffusion activation energy, slow down the creep softening rate of high temperature alloy, improve creep and the enduring quality of high temperature alloy, improve alloy Temperature in use.But excessive Mo promotes the precipitation of harmful phase μ phases, excessive W to increase the notch sensitivity of alloy.Therefore, In view of two elements are in the similar action of high temperature alloy, by 1:1 balanced proportions, the range of control Mo and W is respectively 0.1%~ 6.0%, it is preferable that control range is respectively 3.0%~4.5%.
The addition of Al and Ti is to realize the important channel of high temperature alloy high intensity, the reason is that since Al and Ti are that alloy is main Hardening constituent --- the formation element of γ ' phases, Al, Ti content are higher, and the quantity of γ ' phases is more, and precipitation strength effect is better, alloy Intensity also accordingly increase.But excessively high Al, Ti content, the solid solubility temperature of γ ' phases in alloy is also improved, conjunction is reduced The heat processing technique window of gold, makes the hot-working difficulty of alloy increase, therefore, the range for controlling Al and Ti is respectively 0.1%~ 6.0%, it is preferable that control ranging from the 1.0%~3.0% of Al, control ranging from the 2.0%~4.0% of Ti.
The main function of Nb is to enter γ ' phases, and suitable Nb plays reinforcing and stabilization to γ ' phases, increases dislocation cutting Apb Energies when γ ' phases improve precipitation strength effect, in the design, control ranging from the 0.05%~1.5% of Nb, excellent Selection of land, control range are 0.5%~1.0%.
The addition of Fe be in order to be conducive to the utilization to the high-temperature alloy return material containing Fe including GH4169 alloys, Reduce smelting furnace material cost；But excessive Fe is added, cause to form harmful phase in nickel base superalloy, therefore, controls the model of Fe Enclose is 0.1%~2.0%, it is preferable that control range is 0.1~1.0%.
C, B, Zr, Ce, Mg, Hf are boundary-strengthening element, and the micro addition of these elements can improve and improve alloy Plasticity, enduring quality and shape the comprehensive performances such as performance.
The rational proportion of above-mentioned each alloying element is the guarantee that alloy of the present invention obtains high intensity.
Specific implementation mode
High intensity ni-base wrought superalloy each element mass percent is respectively：Cr：10.0%~25.0%；Co： 10.0%~20.0%；Mo：0.1%~6.0%；W：0.1%~6.0%；Al：0.1%~6.0%；Ti：0.1%~ 6.0%；Nb：0.05%~1.5%；Fe：0.1%~2.0%；C：0.001%~0.10%；B：0.001%~0.05%； Zr：0.01%~0.1%；Ce：0.001%~0.10%；Mg：0.001%~0.10%；Hf：0.01%~0.5%；Ni：It is remaining Amount.
The preparation method of high intensity ni-base wrought superalloy includes the following steps：
Step A：Alloyage, the then melting in vaccum sensitive stove are matched by above-mentioned element, fusion process controls fine melt Temperature：1510 DEG C~1570 DEG C；Control liquid steel refining temperature：1500 DEG C~1560 DEG C；Melting latter stage taps, and solution is poured into Alloy electrode；
Step B：The alloy electrode of gained in step A is subjected to electroslag remelting, remelting is at ESR ingot；
Step C：The ESR ingot of gained in step B is subjected to vacuum consumable remelting, obtains consumable ingot；
Step D：The consumable ingot of gained in step C is carried out High temperature diffusion homogenization to move back within the scope of 1170 DEG C~1190 DEG C Fire obtains homogenizing annealing ingot；
Step E：The homogenizing annealing ingot of gained in step D is heated to 1130 DEG C~1160 DEG C, 2h~4h is kept the temperature, fast Required bar is forged into forging machine；
Step F：Sample is cut using wire cutting mode to the head of the bar of gained in step E, and sample is heat-treated, Bar to having cut off sample carries out surface finish, obtains meeting the alloy material that design of the present invention is asked.
It is CaF that electroslag remelting, which uses pre-melted slag, slag system and proportioning, in the step B2:Al2O3:CaO:TiO2:MgO=67 ±2.0:13±2.0:13±2.0:3±0.5:6±2.0。
In the step C when vacuum consumable remelting, it is (3.0~4.0) Kg/min to control molten speed.
The rated pressure of quick forging machine described in step E is 4500T.
Sample heat treatment, system of heat treatment process described in rapid F are：It is heated to 1060 DEG C, keeps the temperature 4h, oil cooling to room temperature, Sample is then heated to 760 DEG C, 8h is kept the temperature, is air-cooled to room temperature.
Embodiment 1
A method of the high intensity ni-base wrought superalloy preparing the present invention includes the following steps：
Step A：By Cr：22%；Co：13%；Mo：3.8%；W：5.0%；Al：2.0%；Ti：3.5%；Nb：1.0%； Fe：1.0%；C：0.06%；B：0.02%；Zr：0.02%；Ce：0.03%；Mg：0.01%；Hf：0.1%；Ni：The matter of surplus It measures percent composition and matches alloyage, the then melting in vaccum sensitive stove, fusion process controls fine melt temperature：1553℃； Control liquid steel refining temperature：1550℃；Melting latter stage taps, and solution is poured into alloy electrode；
Step B：The alloy electrode of gained in step A is subjected to electroslag remelting, remelting is at ESR ingot；
Step C：The ESR ingot of gained in step B is subjected to vacuum consumable remelting, obtains consumable ingot；
Step D：The consumable ingot of gained in step C is subjected to High temperature diffusion homogenizing annealing at 1170 DEG C, is obtained uniform Annealing ingot；
Step E：The homogenizing annealing ingot of gained in step D is heated to 1130 DEG C, 4h is kept the temperature, is forged into quick forging machine Required bar；
Step F：Sample is cut using wire cutting mode to the head of the bar of gained in step E, and sample is heat-treated, Bar to having cut off sample carries out surface finish, obtains meeting the alloy material that design of the present invention is asked.
It is CaF that electroslag remelting, which uses pre-melted slag, slag system and proportioning,2：Al2O3：CaO：TiO2：MgO=65：13：13：3：6； When vacuum consumable remelting, it is 3.0Kg/min to control molten speed；The rated pressure of the quick forging machine is 4500T；At the sample heat Reason, system of heat treatment process are：1060 DEG C are heated to, 4h is kept the temperature, sample is then heated to 760 DEG C, heat preservation by oil cooling to room temperature 8h is air-cooled to room temperature.
Embodiment 2
The method for preparing the high intensity ni-base wrought superalloy of the present invention includes the following steps：
Step A：By Cr：16%；Co：15%；Mo：5.5%；W：4.5%；Al：1.5%；Ti：4.0%；Nb：0.8%； Fe：0.8%；C：0.03%；B：0.015%；Zr：0.04%；Ce：0.002%；Mg：0.002%；Hf：0.15%；Ni：Surplus Mass percent composition proportion alloyage, the then melting in vaccum sensitive stove, fusion process control fine melt temperature：1552 ℃；Control liquid steel refining temperature：1560℃；Melting latter stage taps, and solution is poured into alloy electrode；
Step B：The alloy electrode of gained in step A is subjected to electroslag remelting, remelting is at ESR ingot；
Step C：The ESR ingot of gained in step B is subjected to vacuum consumable remelting, obtains consumable ingot；
Step D：The consumable ingot of gained in step C is subjected to High temperature diffusion homogenizing annealing at 1180 DEG C, is obtained uniform Annealing ingot；
Step E：The homogenizing annealing ingot of gained in step D is heated to 1140 DEG C, 3h is kept the temperature, is forged into quick forging machine Required bar；
Step F：Sample is cut using wire cutting mode to the head of the bar of gained in step E, and sample is heat-treated, Bar to having cut off sample carries out surface finish, obtains meeting the alloy material that design of the present invention is asked.
It is CaF that electroslag remelting, which uses pre-melted slag, slag system and proportioning,2：Al2O3：CaO：TiO2：MgO=65：13：13：3：6； When vacuum consumable remelting, it is 3.5Kg/min to control molten speed；The rated pressure of the quick forging machine is 4500T；At the sample heat Reason, system of heat treatment process are：1060 DEG C are heated to, 4h is kept the temperature, sample is then heated to 760 DEG C, heat preservation by oil cooling to room temperature 8h is air-cooled to room temperature.
Embodiment 3
A method of the high intensity ni-base wrought superalloy preparing the present invention includes the following steps：
Step A：By Cr：12%；Co：18.5%；Mo：4.5%；W：3.0%；Al：3.0%；Ti：2.5%；Nb： 0.6%；Fe：1.2%；C：0.01%；B：0.01%；Zr：0.03%；Ce：0.01%；Mg：0.015%；Hf：0.3%；Ni： The mass percent composition proportion alloyage of surplus, the then melting in vaccum sensitive stove, fusion process control fine melt temperature： 1550℃；Control liquid steel refining temperature：1555℃；Melting latter stage taps, and solution is poured into alloy electrode；
Step B：The alloy electrode of gained in step A is subjected to electroslag remelting, remelting is at ESR ingot；
Step C：The ESR ingot of gained in step B is subjected to vacuum consumable remelting, obtains consumable ingot；
Step D：The consumable ingot of gained in step C is subjected to High temperature diffusion homogenizing annealing at 1190 DEG C, is obtained uniform Annealing ingot；
Step E：The homogenizing annealing ingot of gained in step D is heated to 1150 DEG C, 2.5h is kept the temperature, is forged in quick forging machine At required bar；
Step F：Sample is cut using wire cutting mode to the head of the bar of gained in step E, and sample is heat-treated, Bar to having cut off sample carries out surface finish, obtains meeting the alloy material that design of the present invention is asked.
It is CaF that electroslag remelting, which uses pre-melted slag, slag system and proportioning,2：Al2O3：CaO：TiO2：MgO=65：13：13：3：6； When vacuum consumable remelting, it is 3.8Kg/min to control molten speed；The rated pressure of the quick forging machine is 4500T；At the sample heat Reason, system of heat treatment process are：1060 DEG C are heated to, 4h is kept the temperature, sample is then heated to 760 DEG C, heat preservation by oil cooling to room temperature 8h is air-cooled to room temperature.
Above-mentioned high intensity ni-base wrought superalloy also inevitably contains impurity element, type and mass percent point It is not：P≤0.010%；S≤0.0015%；Si≤0.1%；Mn≤0.1%；Pb≤0.0005%；Ag≤0.0005%；Te ≤ 0.00005%；Tl≤0.00005%；Bi≤0.00003%.
Example the above is only the implementation of the present invention is not intended to limit protection scope of the present invention, every to utilize this hair Equivalent structure or equivalent flow shift made by bright content is applied directly or indirectly in other relevant technical fields, same Reason includes within the scope of the present invention.
Alloy of the present invention has excellent mechanical property, specific performance such as the following table 1, table 2,3 institute of table after above-mentioned steps Show：
The room temperature tensile properties of 1 alloy of table
The high temperature tensile properties of 2 alloy of table
The high-temperature duration life of 3 alloy of table

Claims (6)

1. a kind of high intensity ni-base wrought superalloy, it is characterised in that：Each element mass percent is respectively：Cr：10.0% ~25.0%；Co：10.0%~20.0%；Mo：0.1%~6.0%；W：0.1%~6.0%；Al：0.1%~6.0%；Ti： 0.1%~6.0%；Nb：0.05%~1.5%；Fe：0.1%~2.0%；C：0.001%~0.10%；B：0.001%~ 0.05%；Zr：0.01%~0.1%；Ce：0.001%~0.10%；Mg：0.001%~0.10%；Hf：0.01%~ 0.5%；Ni：Surplus.
2. high intensity ni-base wrought superalloy according to claim 1, it is characterised in that：Each essential element quality Percentage is respectively：Cr：14%；Co：13%；Mo：3.8%；W：4.5%；Al：2.0%；Ti：3.5%；Nb：1.0%；Fe： 1.0%；C：0.03%；B：0.02%；Zr：0.02%；Ce：0.01%；Mg：0.01%；Hf：0.1%；Ni：Surplus.
3. high intensity ni-base wrought superalloy according to claim 1, it is characterised in that：Each essential element quality Percentage is respectively：Cr：16%；Co：12%；Mo：4.3%；W：3.5%；Al：1.8%；Ti：3.8%；Nb：0.8%；Fe： 0.8%；C：0.02%；B：0.015%；Zr：0.04%；Ce：0.01%；Mg：0.01%；Hf：0.15%；Ni：Surplus.
4. high intensity ni-base wrought superalloy according to claim 1, it is characterised in that：Each essential element quality Percentage is respectively：Cr：15%；Co：11.5%；Mo：4.5%；W：3.0%；Al：2.5%；Ti：3.3%；Nb：0.6%； Fe：0.9%；C：0.01%；B：0.018%；Zr：0.03%；Ce：0.01%；Mg：0.01%；Hf：0.2%；Ni：Surplus.
5. a kind of method preparing a kind of high intensity ni-base wrought superalloy described in claim 1, which is characterized in that including Following steps：
Step A：Alloyage, the then melting in vaccum sensitive stove are matched by above-mentioned element, fusion process controls fine melt temperature： 1510 DEG C~1570 DEG C；Control liquid steel refining temperature：1500 DEG C~1560 DEG C；Melting latter stage taps, and solution is poured into alloy Electrode；
Step B：The alloy electrode of gained in step A is subjected to electroslag remelting, remelting is at ESR ingot；Electroslag remelting uses fritting Slag, slag system and proportioning are CaF2:Al2O3:CaO:TiO2:MgO=67 ± 2.0:13±2.0:13±2.0:3±0.5:6±2.0；
Step C：The ESR ingot of gained in step B is subjected to vacuum consumable remelting, obtains consumable ingot；When vacuum consumable remelting, control The molten speed of system is 3.0~4.0Kg/min；
Step D：The consumable ingot of gained in step C is subjected to High temperature diffusion homogenizing annealing within the scope of 1170 DEG C~1190 DEG C, Obtain homogenizing annealing ingot；
Step E：The homogenizing annealing ingot of gained in step D is heated to 1130 DEG C~1160 DEG C, 2h~4h is kept the temperature, in quick forging machine On be forged into required bar；
Step F：Sample is cut using wire cutting mode to the head of the bar of gained in step E, and sample is heat-treated, sample System of heat treatment process is：1060 DEG C are heated to, 4h is kept the temperature, sample is then heated to 760 DEG C by oil cooling to room temperature, keeps the temperature 8h, Room temperature is air-cooled to get to high intensity ni-base wrought superalloy bar.
6. the method according to claim 5 for preparing high intensity ni-base wrought superalloy, which is characterized in that the fast forging The rated pressure of machine is 4500T.
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CN115505790B (en) * 2022-09-20 2023-11-10 北京北冶功能材料有限公司 Nickel-based superalloy with stable weld strength, and preparation method and application thereof
CN115446494A (en) * 2022-09-20 2022-12-09 中国航发北京航空材料研究院 NiCoCrNbTiAl high-entropy alloy brazing solder for high-temperature alloy brazing connection
CN115446494B (en) * 2022-09-20 2024-03-22 中国航发北京航空材料研究院 NiCoCrNbTiAl high-entropy alloy brazing material for high-temperature alloy brazing connection
CN115446495A (en) * 2022-09-20 2022-12-09 中国航发北京航空材料研究院 Multi-element high-entropy alloy brazing material for high-temperature alloy brazing connection
CN115446495B (en) * 2022-09-20 2024-04-05 中国航发北京航空材料研究院 Multielement high-entropy alloy brazing material for high-temperature alloy brazing connection
CN115572850A (en) * 2022-10-27 2023-01-06 惠州市惠阳协力精密铸造有限公司 High-temperature alloy casting and preparation method thereof
CN116144985A (en) * 2023-03-02 2023-05-23 江苏隆达超合金航材有限公司 Manufacturing method of C263 alloy fine-grain bar
CN118166240A (en) * 2024-05-09 2024-06-11 成都先进金属材料产业技术研究院股份有限公司 High-temperature alloy cast ingot containing large-size eutectic phase gamma+gamma' and furnace combination homogenization treatment method thereof

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