TWI612143B - Precipitation-hardened nickel-based alloy and method of producing the same - Google Patents

Abstract

The present invention provides a high strength precipitation-strengthened nickel-based alloy and a method of producing the same. In the above method, the alloy preform of a specific composition is subjected to a hot working treatment and an aging treatment to obtain a precipitation-strengthened nickel-based alloy. The resulting precipitation-strengthened nickel-based alloy has high strength and is also ductile.

Description

Precipitation-enhanced nickel-based alloy and manufacturing method thereof

The present invention relates to a high-strength precipitation-strengthened nickel-based alloy and a method for producing the same, and more particularly to a method for manufacturing a precipitation-strengthened nickel-base alloy by annealing and aging treatment, excluding an annealing treatment and a cold working treatment. The method is to produce a precipitation-strengthened nickel-based alloy having high strength and ductility.

Precipitation-enhanced nickel-based alloys (for example, Alloy 718 and A-286, etc.), because of their high temperature strength, high temperature oxidation resistance and good corrosion resistance, are often used in high temperature mechanical properties, such as engine components. , turbine engine fasteners, high temperature bearings, furnace enclosures or nuclear power plant furnaces. The main component of the nickel-based alloy is nickel, and its structure is mainly a face-centered cubic structure. Since a strengthening element such as aluminum, titanium, and/or tantalum is added, a heat treatment method such as aging treatment can be used to precipitate the γ' of the Ll ₂ structure. Phase (Ni ₃ (Ti, Al)) and DO ₂₂ structure γ" phase (Ni ₃ Nb).

In general, in order to apply the above-mentioned precipitation-strengthened nickel-based alloy to the field of high-strength demand (for example, mining or oil drilling), general grade gauge Fan's mechanical properties are not enough (the general grade specification is not less than 1214MPa tensile strength, not less than 1034MPa, and not less than 12% elongation), so it will be annealed and cold processed in the process, The strength of the precipitation-strengthened nickel-based alloy can be further improved, and the target of the high-strength nickel-based alloy is a tensile strength of not more than 1670 MPa, a relief strength of not less than 1400 MPa, and an elongation of not less than 10%.

However, the above method not only has complicated process steps and high manufacturing cost, but the precipitated strengthened nickel-based alloy produced can be used only for general industrial applications due to small process margin.

Therefore, there is a need to provide a method for producing a precipitation-strengthened nickel-based alloy, which can omit the conventional annealing treatment and cold working treatment, and obtain a precipitation-strengthened nickel-based alloy having both strength and ductility to meet high-strength applications. Demand.

Accordingly, an aspect of the present invention provides a method for producing a precipitation-strengthened nickel-based alloy which can omit a conventional annealing treatment and a cold working treatment to obtain a precipitation-strengthened nickel-based alloy having both strength and ductility. Therefore, the manufacturing method of the present invention has a lower production cost and can have a better process margin (i.e., it can maintain a high ductility when strengthened to the same strength).

Another aspect of the present invention provides a precipitation-strengthened nickel-based alloy which is obtained by the above-described production method.

According to the above aspect of the invention, a method for producing a precipitation-strengthened nickel-base alloy is proposed. In an embodiment, the above manufacturing method may include The following steps. First, an alloy embryo is provided, which may comprise the following components: 10 weight percent (wt.%) to 25 wt.% chromium, 5 wt.% to 60 wt.% iron, 0.01 wt.% to 0.1 wt.% carbon, 0.2 wt.% to 1.2 wt.% aluminum, 0.5 wt.% to 2.0 wt.% titanium, 4.0 wt.% to 6.0 wt.% bismuth, 1.0 wt.% to 8.0 wt.% molybdenum, less than 5 wt. a small amount of .% of the element and the balance of nickel, and the nickel is at least 22 wt.%, wherein the small amount of the above elements may comprise cobalt, copper, boron, manganese, cerium or a combination thereof. Next, the alloy embryo is subjected to a hot working treatment to form a hot-worked alloy material, wherein the final temperature of the hot working treatment may be 850 ° C to 1050 ° C, and the presidential reduction rate may be 35% or more. Then, the hot-worked alloy material is subjected to aging treatment to obtain a precipitation-strengthened nickel-based alloy. The aging treatment may include a first stage aging treatment at 690 ° C to 750 ° C for 6 hours to 10 hours, and a second stage aging treatment at 590 ° C to 650 ° C for 2 hours to 14 hours. The method for producing a precipitation-strengthened nickel-based alloy of the present invention excludes annealing treatment and cold working treatment.

According to an embodiment of the present invention, the alloy embryo may be obtained by subjecting an alloy material of the above composition to a smelting treatment and a refining treatment.

According to an embodiment of the present invention, the smelting treatment may include fuel heating furnace smelting, non-vacuum electric furnace smelting, vacuum induction furnace smelting or vacuum arc melting.

According to an embodiment of the present invention, the refining treatment may include an argon blowing oxygen decarburization treatment, a vacuum oxygen decarburization treatment, an electroslag remelting treatment, or an arc remelting treatment.

According to an embodiment of the present invention, the manufacturing method may further include a finishing process between the hot working process and the aging process.

According to an embodiment of the present invention, the manufacturing method may further include a finishing treatment after the aging treatment.

According to an embodiment of the invention, the finishing treatment may comprise pickling, rounding, slitting, straightening, peeling, calendering, grinding or any combination of the above.

According to an embodiment of the invention, the presidential reduction rate can be from 35% to 80%.

According to an embodiment of the present invention, the first stage aging treatment can be carried out at 690 ° C to 740 ° C, and the second stage aging treatment can be carried out at 590 ° C to 620 ° C.

According to the above aspect of the invention, a precipitation-strengthened nickel-based alloy which is produced by the above-described method for producing a precipitation-strengthened nickel-based alloy is further proposed. In one embodiment, the precipitation-strengthened nickel-based alloy preferably has a tensile strength of not more than 1670 MPa, a relief strength of not less than 1400 MPa, and an elongation of not less than 10%.

The manufacturing method of the precipitation-strengthened nickel-based alloy of the present invention can be omitted, and the conventional annealing treatment and cold processing can be omitted, and the high-strength strength can be obtained by heat treatment and aging treatment at a specific temperature and a presidential reduction rate. A precipitation-strengthened nickel-based alloy that is also ductile.

The above and other objects, features, advantages and embodiments of the present invention will become more apparent and understood.

1A is a graph showing a precipitation-enhanced nickel-base alloy according to Embodiment 1 of the present invention. The electron microscope of the micro-tissue has a scale of 50 μm.

1B is an electron microscope showing a microstructure of a nickel-based alloy of Comparative Example 5 of the present invention, the scale of which is 100 μm.

An aspect of the present invention provides a method for producing a precipitation-strengthened nickel-based alloy which is subjected to a heat treatment process for a specific final temperature and a presidential reduction rate, and a aging treatment at a specific temperature for a specific composition of the alloy embryo. A precipitation-strengthened nickel-based alloy that combines strength and ductility, which meets the specifications for high-strength applications. In particular, the manufacturing method of the present invention omits the conventional annealing treatment and cold working treatment, thereby simplifying the process steps, reducing the manufacturing cost, and increasing the process margin.

The final temperature referred to herein as the final temperature may be, for example, the finishing temperature or the finishing temperature.

The high-strength application demand referred to in the present invention is, for example, the application of a precipitation-strengthened nickel-based alloy to tools such as mining or oil drilling, and the applicable strength and ductility of the specification are tensile strengths of not more than 1670 MPa, not less than The 1400 MPa drop strength and the elongation of not less than 10%.

The process margin referred to in the present invention means that the strength and ductility of the precipitation-strengthened nickel-based alloy can be simultaneously improved by the manufacturing method of the present invention, so that it can meet the application requirements of high-strength applications.

The alloy embryo referred to herein as the invention may include the following components: 10% by weight (wt.%) to 25 wt.% chromium, 5 wt.% to 60 wt.% iron, 0.01 wt.% to 0.1 wt.% carbon. 0.2wt.% to 1.2wt. % aluminum, 0.5 wt.% to 2.0 wt.% titanium, 4.0 wt.% to 6.0 wt.%, 1.0 wt.% to 8.0 wt.% molybdenum, less than 5 wt.% other minor elements and A quantity of nickel and a nickel content of at least 22 wt.%.

In one embodiment, the minor elements described above may comprise cobalt, ruthenium, copper, boron, manganese, or any combination of the foregoing.

The nickel element in the alloy embryo provides corrosion resistance of the resulting precipitation strengthened nickel-based alloy, particularly for stress corrosion or sulfide stress corrosion. Further, nickel may form a toughened precipitation phase structure with bismuth, aluminum, and/or titanium to increase the strength of the precipitation-strengthened nickel-based alloy. Therefore, if the amount of nickel in the alloy embryo is too small, the precipitation-strengthened nickel-based alloy cannot achieve a predetermined strength and is inferior in corrosion resistance.

The above-mentioned chromium element can provide the corrosion resistance of the precipitation-strengthened nickel-based alloy. Therefore, if the chromium element in the alloy embryo is too small, the precipitation-enhanced nickel-based alloy is inferior in corrosion resistance. On the other hand, excessive chromium element affects the thermal stability and ductility of the alloy embryo, so the chromium content is preferably within the scope of the present invention.

As mentioned above, the lanthanum element can form a toughened phase structure with nickel. In the aging treatment, it contributes to the improvement of the strength of the reinforced nickel-based alloy, so that the precipitation-enhanced nickel-based alloy can have both strength and ductility. . However, too much bismuth element is prone to large segregation during casting, resulting in uneven grain and difficult processing.

The above-mentioned titanium element and aluminum element contribute to the improvement of the strength of the precipitation-strengthened nickel-based alloy. However, excessive titanium and aluminum elements are not conducive to the stability of the nickel-based alloy matrix, so the titanium element and the aluminum element are in the range of content claimed by the present invention. It is appropriate.

The carbon element has a solid solution strengthening effect, and an appropriate amount of carbon can increase the strength of the precipitation strengthened nickel base alloy. However, if the content of the carbon element is too large, the corrosion resistance of the precipitation-strengthened nickel-based alloy is deteriorated.

The above-mentioned molybdenum element can enhance the ability of the precipitation-enhanced nickel-based alloy to resist local corrosion such as pitting corrosion and seam corrosion, in particular, corrosion resistance in a halogen ion or a reducing medium. However, excessive molybdenum also causes poor thermal stability and ductility of the alloy embryo.

The above-mentioned small elements such as cobalt, ruthenium, copper, boron, manganese, etc. are liable to form a harmful phase (for example, a phase having a high brittleness) in the precipitation-strengthened nickel-based alloy, or increase the production cost, so the content of the above trace elements is not more than 5 wt. .% is better.

Method for manufacturing alloy embryo

In one embodiment, the alloy embryo may be obtained by an smelting treatment and a refining treatment using an alloy material containing the foregoing components. Specifically, the smelting treatment may include fuel heating furnace smelting, electric vacuum furnace melting (EAF), vacuum induction furnace melting (VIM), or vacuum arc melting (VAM). The refining treatment may include Argon Oxygen Decarburization (AOD) treatment, Vacuum Oxygen Decarburization (VOD) treatment, Electroslag Remelting (ESR) treatment or arc remelting ( Vacuum Arc Remelting; VAR) treatment.

Method for producing precipitation-strengthened nickel-based alloy

Next, a method for producing the precipitation-strengthened nickel-base alloy of the present invention will be described in order.

1. Thermal processing

In one embodiment, the alloy embryo of the specific composition described above is first subjected to a hot working treatment to form a hot worked alloy material. Specifically, the hot working treatment may be hot rolling or hot forging. The final temperature of the thermal processing is preferably not more than the complete recrystallization temperature, and the complete recrystallization temperature of the alloy embryo claimed in the present invention is greater than 1050 °C. Preferably, the thermal processing may have a final temperature of 850 ° C to 1050 ° C and a presidential reduction of more than 35%. In a preferred embodiment, the president's reduction rate for thermal processing may range from 35% to 80%.

In one example, the hot-worked alloy material is a wire, and its presidential reduction rate can be calculated by the following formula (I): presidential reduction rate = (A ₀ -A _f ) / A ₀ × 100% (I)

Wherein A ₀ represents the original cross-sectional area of the alloy embryo (which may be, for example, a cylindrical embryo or other shaped alloy embryo), and A _f represents the cross-sectional area of the wire of the alloy material after hot working.

The hot working process of the present invention can pass through a specific final temperature and a presidential reduction rate, so that the hot-worked alloy material has smaller crystal grains (for example, less than 20 μm) and high differential discharge density to achieve fine grain strengthening and work hardening effect. . Further, according to the Hall-Petch relation as shown in the formula (II), it can be understood that when the crystal grains are smaller, the grain boundary table The larger the area, the grain boundary can hinder the movement of the difference row, so refining the grains can increase the strength of the hot-worked alloy material.

Yield Stress = σ ₀ +kD ^-1/2 (II)

Where σ ₀ represents the frictional stress, k represents the locking parameter, and D represents the grain size.

Further, according to the relationship of the formula (III), the amount of strain generated by the hot working treatment (for example, the presidential reduction rate referred to herein as the present invention) is positively correlated with the difference in the density of the rows. When the hot working treatment of the present invention is carried out at a treatment temperature not higher than the complete recrystallization temperature, the alloy embryo is plastically deformed, so that the crystal grains are twisted and the differential discharge density is increased, so that the strength of the obtained hot-worked alloy material is increased but extended. Sexual decline.

△τ=Gαbρ ^1/2 (III)

Where Δτ represents the processing strain, G represents the Shear Modulus, α is a constant, b represents a Burgers vector, and ρ represents the difference density.

Therefore, if the final temperature of the hot working treatment is lower than 850 ° C, the ductility of the hot worked alloy material is insufficient. On the other hand, if the final temperature of the hot working treatment is higher than 1050 ° C, complete recrystallization is caused to affect the poor discharge density, and the strength of the precipitation strengthened nickel-based alloy is further lowered. In addition, if the above-mentioned president's reduction is less than 35%, the increase in the differential density of the hot-worked alloy material will be insufficient, thereby reducing the strength of the alloy. When the president reduces the amount by 80%, continuing to increase the president's reduction will lead to excessive strength of the alloy but insufficient ductility.

In addition, the present invention also excludes the high temperature (higher than the end of the segregation of the segregated component for a long time (for example, 24 hours to 72 hours) before the hot working treatment. Full recrystallization temperature) homogenization treatment. Although the above homogenization treatment can increase the elongation of the nickel-based alloy, it simultaneously reduces the strength, lengthens the process time, and increases the cost.

2. Aging treatment

Next, the hot worked alloy material is subjected to aging treatment. The aging treatment referred to herein as the invention may include a first stage aging treatment and a second stage aging treatment. The first stage aging treatment can be carried out at 690 ° C to 750 ° C for 6 hours to 10 hours. The second stage aging treatment can be carried out at 590 ° C to 650 ° C for 2 hours to 14 hours. In a preferred embodiment, the first stage aging treatment can be carried out at 690 ° C to 740 ° C, and the second stage aging treatment can be carried out at 590 ° C to 620 ° C.

In an example, the first stage aging treatment can be performed, for example, by furnace cooling, and the second stage aging treatment can be performed, for example, by air cooling, but only to achieve the temperature range claimed by the present invention, and is not limited to a specific processing environment. .

In one embodiment, the first stage aging treatment and the second stage aging treatment further comprise a cooling treatment for cooling the hot worked alloy material from 690 ° C to 750 ° C to 590 ° C to 650 ° C. In a preferred embodiment, the cooling rate of the cooling treatment may range from 80 ° C / hour to 150 ° C / hour. If the cooling rate is lower than 80 ° C / hour, the strength of the obtained nickel-based alloy is insufficient.

The aging treatment of the present invention adopts a two-stage type and an aging treatment with different temperature ranges to avoid the occurrence of harmful phases (such as the aforementioned brittle phase) of the hot-worked alloy material during the aging treatment. Therefore, if the long-term aging treatment is continued at the same temperature, the processing time of each stage is too long. Or, if the treatment temperature is too high, the brittleness of the precipitated reinforced nickel-based alloy obtained increases, resulting in a decrease in ductility. On the other hand, if the time in each of the above stages is too short or the treatment temperature is too low, the strengthening effect of the aging treatment cannot be exerted, and the obtained precipitation-strengthened nickel-based alloy cannot achieve a predetermined strength.

In particular, one of the technical features of the present invention is to omit the annealing treatment and the cold processing between the thermal processing and the aging treatment by the prior art, and directly perform the aging treatment to obtain the precipitation having both strength and ductility. Reinforced nickel-based alloy. Therefore, the present invention simplifies the cumbersome steps of the conventional process, reduces the production cost, and increases the process margin and productivity.

3. Finishing

The method for producing a precipitation-strengthened nickel-based alloy of the present invention may further comprise a finishing treatment, which may be carried out, for example, between a hot working treatment and an aging treatment, and/or after an aging treatment.

The purpose of the finishing treatment is to adjust the specific specifications such as the surface quality, straightness or size of the precipitation-strengthened nickel-based alloy to meet the market demand.

In an embodiment, the finishing treatment may comprise pickling, rounding, slitting, straightening, peeling, calendering, grinding, or any combination of the above. The manner in which the finishing treatment is carried out should be well known to those of ordinary skill in the art and will not be described herein.

Precipitation-enhanced nickel-based alloy

Precipitation-enhanced nickel-based alloy prepared by the method for producing a precipitation-enhanced nickel-base alloy of the present invention, which meets the requirements for high-strength application requirements Fan. The specification is a tensile strength of not more than 1670 MPa, a relief strength of not less than 1400 MPa, and an elongation of not less than 10%, so that the precipitation-strengthened nickel-based alloy has both strength and ductility, thereby improving the manufacture of the present invention. Process margin of the method.

Hereinafter, a method for producing a precipitation-strengthened nickel-based alloy of the present invention will be specifically described using a plurality of examples.

Example 1

Example 1 is an alloy preform having a composition as shown in Table 1, which is hot rolled to form a wire, wherein the hot rolling temperature is 876 ° C, and the presidential reduction rate is 80%. Next, the wire was oven-cooled at 720 ° C for 8 hours, and the wire was air-cooled at 620 ° C for 8 hours to obtain a precipitation-strengthened nickel-based alloy of Example 1, and the related evaluation results and process conditions were Details are listed in Table 2.

Examples 2 to 7 and Comparative Example 1

Examples 2 to 7 and Comparative Example 1 were carried out in the same manner as in Example 1, except that Examples 2 to 7 and Comparative Example 1 changed their process conditions. The specific process conditions and evaluation results of Examples 2 to 7 and Comparative Example 1 are shown in Table 2 and Table 3, and are not described herein. In particular, the heating temperature of the hot rolling of the embodiment and the comparative example may be, for example, Between 1120 ° C and 1160 ° C to reach a predetermined final temperature.

Example 8

In Example 8, the precipitation-strengthened nickel-base alloy of Example 4 was pickled, and then cut into a straight rod having a length of 8 m, and further rounded from 0.83 mm to 0.15 mm. Thereafter, it was straightened to a straightness of 0.35 mm/m, and calendered to a smooth bar having a diameter of 30.0 mm. The evaluation results of Example 8 are shown in Table 2.

Comparative example 2

Comparative Example 2 was hot rolled by an alloy blank as shown in Table 1 to form a wire in which the hot rolling was completed at a temperature of 1063 ° C and the presidential reduction rate was 80%. The above wire was annealed at 980 ° C for 1 hour to obtain a nickel-based alloy of Comparative Example 2. The evaluation results of Comparative Example 2 are shown in Table 3 and will not be further described herein.

Comparative Examples 3 to 8

Comparative Examples 3 to 8 were carried out in the same manner as in Comparative Example 2, except that Comparative Examples 3 to 8 changed their process conditions (for example, further aging treatment and/or cold treatment). The specific process conditions of Comparative Examples 3 to 8 and the evaluation results thereof are shown in Table 3, and are not described herein.

Evaluation method

Intensity

1-1. Tensile strength

The tensile strength of the present invention is obtained by performing a tensile test of the standard test method ASTM E112 at 25 °C. The above tensile strength is not more than 1670 MPa.

1-2. Falling strength

The lodging strength of the present invention is obtained by performing a tensile test of the standard test method ASTM E112 at 25 °C. The above-mentioned lodging strength is not less than 1400 MPa.

2. Elongation

The elongation of the present invention is obtained by performing a tensile test of the standard test method ASTM E112 at 25 °C. In general, the above elongation is not less than 10%.

According to Table 2, after the alloy preform of a specific composition is subjected to the hot working treatment and the aging treatment of the present invention, a precipitation-strengthened nickel-base alloy having strength and ductility which meets the requirements for high-strength applications can be obtained. In particular, when the finishing temperature of the hot working treatment is high (for example, Example 3 of the present invention) or the president has a large reduction rate (for example, Example 4 of the present invention), the strength and elongation of the precipitation-strengthened nickel-based alloy Sex can be further improved. Further, as shown in Example 8, by further performing the finishing treatment, the strength of the precipitation-strengthened nickel-base alloy can be increased to a small extent.

On the other hand, according to Table 3, the obtained nickel-based alloy could not reach a predetermined strength even if the annealing treatment was carried out without performing the heat treatment of the specific finish rolling temperature and the presidential reduction rate claimed in the present invention. Further, even if the aging treatment is additionally performed for the purpose of increasing the strength, or even the cold working treatment is performed, although the appropriate elongation can be maintained, the strength still does not meet the specifications for the high-strength application. If the reduction rate of cold working is increased to increase the strength, Sacrifice the ductility of nickel-based alloys. In addition, additional annealing and cold working are performed to increase the complexity of the process and increase the manufacturing cost of the nickel-based alloy.

Further, as shown in Comparative Example 8, if the temperature of the aging treatment is higher than that of the present invention, the nickel-based alloy cannot achieve the predetermined strength and ductility.

1A and FIG. 1B, FIG. 1A is an electron microscope showing the microstructure of the precipitation-enhanced nickel-base alloy according to Embodiment 1 of the present invention, and FIG. 1B is a view showing the nickel of Comparative Example 5 of the present invention. Electron microscopy of the microstructure of the base alloy. As shown in FIG. 1A, the precipitation-strengthened nickel-based alloy obtained by the hot working treatment and the aging treatment under specific conditions has a crystal grain size of about 4.5 μm. The grain size shown in Fig. 1B is about 8.6 μm, which is significantly larger than that of the embodiment 1 of the present invention. It can be seen from the above that the present invention achieves the effect of refining the crystal grains by specific heat processing conditions, thereby improving the processing strength.

In summary, the method for producing a precipitation-strengthened nickel-based alloy according to the present invention can be combined with a conventional annealing treatment and a cold working treatment, and can be combined with a heat treatment process and an aging treatment of a specific process condition to obtain both strength and ductility. A strengthened nickel-based alloy is precipitated. Therefore, the manufacturing method of the present invention not only simplifies the complicated process steps of the prior art, reduces the production cost, but also has a large process margin.

While the invention has been described above in terms of several embodiments, it is not intended to limit the scope of the invention, and the invention may be practiced in various embodiments without departing from the spirit and scope of the invention. The scope of protection of the present invention is defined by the scope of the appended claims.

Claims (10)

A method for producing a precipitation strengthened nickel-based alloy, comprising: providing an alloy embryo comprising the following components: 10 weight percent (wt.%) to 25 wt.% chromium; 5 wt.% to 60 wt.% iron; 0.01 From wt.% to 0.1 wt.% of carbon; from 0.2 wt.% to 1.2 wt.% of aluminum; from 0.5 wt.% to 2.0 wt.% of titanium; from 4.0 wt.% to 6.0 wt.%; 1.0 wt. % to 8.0 wt.% of molybdenum; less than 5 wt.% of a minor element, wherein the minor element comprises cobalt, copper, boron, manganese, cerium or a combination thereof; and the balance of nickel, wherein the nickel is at least 22 wt.%, Wherein one of the alloy embryos has a complete recrystallization temperature of greater than 1050 ° C; the alloy embryo is subjected to a thermal processing to form a hot-worked alloy material, wherein the hot working treatment comprises hot rolling or hot forging, one of the hot working treatments The final temperature is 850 ° C to 1050 ° C, and a presidential reduction rate is more than 35%; and the hot-worked alloy material is subjected to an aging treatment to obtain the precipitation-strengthened nickel-based alloy, wherein the aging treatment comprises: One-stage aging treatment, which is carried out at 690 ° C to 750 ° C for 6 hours to 10 hours; and a second stage aging treatment, which is carried out at 590 ° C to 650 ° C 2 hours to 14 hours, Wherein the manufacturing method excludes an annealing treatment and a cold processing. The method for producing a precipitation-strengthened nickel-based alloy according to claim 1, wherein the alloy precursor is obtained by an alloying material of the component, a smelting treatment, and a refining treatment. The method for producing a precipitation-strengthened nickel-based alloy according to claim 2, wherein the smelting treatment comprises a fuel heating furnace smelting, a non-vacuum electric furnace smelting, a vacuum induction furnace smelting or a vacuum arc melting. The method for producing a precipitation-strengthened nickel-based alloy according to claim 2, wherein the refining treatment comprises an argon gas oxygen decarburization treatment, a vacuum oxygen decarburization treatment, an electroslag remelting treatment or an electric arc. Remelting treatment. The method for producing a precipitation-strengthened nickel-base alloy according to claim 1, wherein a finishing treatment is further included between the hot working treatment and the aging treatment. The method for producing a precipitation-strengthened nickel-based alloy according to claim 1, wherein after the aging treatment, a finishing treatment is further included. The method for producing a precipitation-strengthened nickel-based alloy according to claim 5, wherein the finishing treatment comprises pickling, rounding, slitting, straightening, peeling, calendering, grinding, or the like. random combination. The method for producing a precipitation-strengthened nickel-based alloy according to claim 1, wherein the president's reduction rate is 35% to 80%. The method for producing a precipitation-strengthened nickel-based alloy according to claim 1, wherein the first-stage aging treatment is performed at 690 ° C to 740 ° C, and the second-stage aging treatment is performed at 590 ° C to 620 Perform at °C. A precipitation-strengthened nickel-based alloy obtained by the method for producing a precipitation-strengthened nickel-based alloy according to any one of claims 1 to 9, wherein the precipitation-strengthened nickel-based alloy has no One tensile strength greater than 1670 MPa, one tensile strength not less than 1400 MPa, and one elongation not less than 10%.