Nickel-based high-temperature deformation alloy and manufacturing method and application thereof

Abstract

The invention relates to the technical field of high-temperature alloys, and particularly discloses a nickel-based high-temperature deformation alloy and a manufacturing method and application thereof. The manufacturing method provided by the invention comprises the following steps: adding Ni-Cr in a vacuum melting stage to form a molten pool, sequentially adding Co, W, Mo and V alloys, carrying out vacuum refining for 60-90 minutes, adding Al, Ti and Nb, filling argon after refining, adding B and Mg, and pouring at 1420-1430 DEG C to obtain a consumable electrode; the consumable electrode is welded and then subjected to vacuum consumable smelting, helium is filled in the smelting process for cooling, the smelting speed is controlled to be 2.0 kg / min to 2.5 kg / min, and the pressure of the helium is 300 Pa to 500 Pa. Through the unique component adding sequence, accurate process parameter control and reasonable process combination, the quality and performance of the nickel-based high-temperature deformation alloy are remarkably improved, and collaborative optimization of alloy components, structures and performance is achieved.

Description

Technical Field

[0001] The present invention relates to the technical field of high temperature alloys, and in particular to a nickel-based high temperature deformation alloy and a manufacturing method and application thereof. Background Art

[0002] In the modern industrial field, especially in the aerospace, energy and power, petrochemical and other industries, many key equipment and components need to operate stably for a long time in high temperature environments. For example, the turbine parts of aircraft engines, the hot end parts of industrial gas turbines, and high-temperature reaction devices in petrochemicals, etc. When these devices are working, their internal fasteners need to withstand high temperatures, high pressures, complex mechanical stresses and other harsh conditions.

[0003] For fasteners used in high temperature environments above 800℃, traditional high temperature alloys are difficult to meet such harsh working conditions. GH4175 alloy has become one of the ideal choices for manufacturing high temperature fasteners due to its potential excellent performance. However, in the current research and development and production process of GH4175 alloy, there are a series of problems that need to be solved urgently.

[0004] Due to the high degree of alloying of GH4175 alloy, the internal structure of the alloy is complex and the interaction between the elements increases. In the preparation of vacuum induction electrodes in industrial production, the material is difficult to withstand stress changes during demolding and is prone to breakage after demolding. In addition, in the subsequent vacuum consumable smelting process, on the one hand, there is a serious problem of block drop, which leads to large fluctuations in the smelting curve and difficulty in stable control of the smelting process, which has an adverse effect on the quality stability of the final product; on the other hand, the segregation problem of the consumable ingot is serious, the composition distribution is uneven, and after the smelting is completed and demolded, the head of the consumable ingot is severely cracked, which not only further increases the production cost, but also significantly reduces the performance of the alloy.

[0005] The above problems have seriously restricted the large-scale application and development of GH4175 alloy in the field of high-temperature fasteners. Therefore, developing a preparation method that can effectively solve the above problems and ensure that the alloy has high strength, high toughness, good creep resistance and thermal fatigue resistance in a high temperature environment above 800°C has become the current research focus and key demand in this field. Summary of the invention

[0006] In view of the problems in the existing preparation process of GH4175 alloy, such as easy fracture during vacuum induction melting and demolding, serious block falling during vacuum consumable smelting, and serious head cracking after demolding after smelting, the present invention provides a nickel-based high-temperature deformation alloy and a manufacturing method and application thereof.

[0007] To solve the above technical problems, the technical solution provided by the embodiment of the present invention is:

[0008] In a first aspect, the present invention provides a nickel-based superalloy for hot deformation, and its chemical composition is as follows: C 0.04% - 0.08%, Cr 9.40% - 11.00%, Co 14.80% - 16.00%, W 2.90% - 4.00%, Mo 4.00% - 4.80%, Al 3.50% - 4.00%, Ti 2.30% - 2.80%, Nb 4.10% - 4.60%, V 0.40% - 0.80%, B 0.005% - 0.008%, Mg 0.001% - 0.003%, and the balance is Ni and unavoidable impurities.

[0009] Compared with the prior art, for the nickel-based superalloy for hot deformation provided by the present invention, Al, Ti, W, and Mo are controlled within a suitable content range to meet the high-strength requirements under high-temperature conditions. And because the contents of Al and Ti in this alloy are relatively high, the content of the strengthening phase γ' is close to 60%, and the plasticity of the alloy is poor. Therefore, the present invention adds a small amount of V, B, and Mg. Among them, V can improve the hot corrosion resistance, heat resistance strength, and oxidation resistance of the alloy, improve the tensile strength and plasticity of the alloy, and improve the forming performance of the alloy; B and Mg can segregate at the grain boundaries, purify the interface and inhibit dynamic recrystallization, enhancing the high-temperature plasticity. At the same time, the B element can form a eutectic phase with a low melting point to improve the hot working fluidity and solve the problem of difficult deformation; an appropriate amount of magnesium can also improve the toughness and fatigue resistance of the alloy, and improve the comprehensive performance of the alloy to a certain extent.

[0010] Through the synergistic effect of each component, the present invention significantly improves the strength, toughness, creep resistance, and thermal fatigue resistance of the alloy in a high-temperature environment. At the same time, it also significantly improves the forming performance of the alloy, reduces the production energy consumption, and has broad application prospects in the field of superalloys for hot deformation.

[0011] In a second aspect, the present invention provides a manufacturing method of a nickel-based superalloy for hot deformation, including the following steps:

[0012] S1. Add the Ni-Cr alloy into a vacuum induction furnace. After melting, sequentially add Co, W, Mo, V, and C to obtain an alloy liquid.

[0013] S2. Vacuum refine the alloy liquid, add Al, Ti, and Nb. After the refining is completed, fill argon gas, add B and Mg, and carry out pouring at 1420°C - 1430°C, demold, and anneal to obtain a consumable electrode.

[0014] S3. Weld the consumable electrode and then carry out vacuum consumable melting. During the melting process, fill helium gas for cooling. After the melting is completed, demold and cool slowly to obtain a nickel-based superalloy ingot; wherein, the melting rate of the vacuum consumable melting is 2.0 kg / min - 2.5 kg / min, and the pressure of the helium gas is 300 Pa - 500 Pa.

[0015] Compared with the prior art, in the manufacturing method of the nickel-based superalloy provided by the present invention, after adding Ni-Cr to form a molten pool in the vacuum melting stage, Co, W, Mo and V alloys are added in sequence. Among them, adding Co first can promote the solid solution distribution of subsequent elements such as W and Mo, enhance the lattice distortion effect, and improve the high-temperature creep resistance. V can refine the carbide size. Adding the V element preferentially in the vacuum induction melting stage is beneficial to the uniform precipitation of carbides at high temperature, providing heterogeneous nucleation sites for the subsequent γ' phase and enhancing the precipitation strengthening effect; adding Al, Ti and Nb elements preferentially in the vacuum refining stage helps these elements to dissolve and distribute uniformly in the high-temperature melt. At the same time, it can also avoid competing for melting with the previous high-melting-point elements, ensure their full diffusion in the melt, and form a uniformly distributed coherent strengthening phase; at the same time, adding Al, Ti and Nb elements in the vacuum refining stage can also reduce the oxidation loss rate and reduce the formation of oxidation inclusions; B and Mg are added at the end of refining to effectively adsorb grain boundary impurities (such as S, P, etc.), cooperate with the γ' phase strengthening of Al / Ti, and improve the thermal fatigue resistance of the alloy. In addition, choosing a lower pouring temperature can make the alloy liquid form a fine and uniform equiaxed crystal structure during solidification, and at the same time promote the dispersed distribution of carbides (such as MC type), reduce segregation, and cooperate with vacuum refining to effectively reduce porosity and shrinkage porosity defects; controlling specific melting rates and helium cooling rates reduces the tendency of columnar crystal growth and reduces the risk of inter-dendritic cracks.

[0016] The manufacturing method of the present invention significantly improves the quality and performance of the nickel-based superalloy through a unique composition addition sequence, precise process parameter control, and reasonable process combination, realizes the synergistic optimization of alloy composition - microstructure - performance, meets the requirements of extreme working conditions such as aeroengine turbine blades, and has high application prospects.

[0017] Further, in S1, the temperature of melting is 1470°C to 1490°C, and the vacuum degree ≤ 10 Pa.

[0018] Further, in S2, the temperature of vacuum refining is 1470°C to 1490°C, the vacuum degree ≤ 1 Pa, and the time of vacuum refining is 60 min to 70 min.

[0019] Further, in S2, after adding B and Mg, pouring is completed within 20 min.

[0020] Rapid pouring after adding B and Mg can effectively reduce the burning loss rate of alloy elements and reduce oxidation inclusions.

[0021] Further, in S2, the pressure of argon is 18000 Pa to 25000 Pa.

[0022] Further, in S2, the diameter of the consumable electrode is 240 mm to 260 mm.

[0023] Due to size limitations, traditional 180 mm electrode ingots require multiple splicing or stacked welding to manufacture large components. However, large-sized electrode ingots (such as those with a diameter ≥ 250 mm) can directly meet the forging requirements of large-sized turbine disks (with a diameter of 1250 - 1500 mm), reducing the risk of welding interface defects.

[0024] Through alloy composition design and process optimization, the present invention can prepare large-sized consumable electrodes, solving problems such as element segregation, difficult forming, and easy fracture in the production of large-sized ingots by traditional processes. It meets the requirements for integral formed large forgings in new-generation aero-engines, heavy-duty gas turbines, etc., avoids the reliability risks brought by multi-component welding, and provides technical support for the application of superalloys under extreme working conditions.

[0025] Further, in S2, after adding Al, Ti, and Nb, continue refining for 20 min to 30 min.

[0026] Further, in S2, the annealing temperature is 1000 °C to 1190 °C, and the annealing time is 15 h to 20 h.

[0027] Further, in S3, the vacuum consumable melting includes an arc starting stage, a melting stage, and a filling stage; among them, the droplet speed in the melting stage is 5 drops / s to 8 drops / s.

[0028] Precisely controlling the melting speed at 2.0 kg / min to 2.5 kg / min, the droplet speed, and the helium pressure at 18000 Pa to 25000 Pa can significantly improve the solidification structure of the alloy steel ingot, reduce internal defects, increase the density and uniformity of the alloy steel ingot, thereby enhancing the comprehensive performance of the nickel-based superalloy for hot deformation and meeting the requirements of more stringent usage environment.

[0029] Further, in S3, the current in the arc starting stage is 2.5 KA to 5.2 KA, the voltage is 22 V to 23 V, and the smelting time in the arc starting stage is 60 min to 70 min.

[0030] Further, in S3, the current in the filling stage is 2.5 KA to 3.5 KA, and the voltage is 22 V to 23 V.

[0031] Further, in S3, the filling stage is carried out when 70 kg to 90 kg remains during melting, and the filling ends when 15 kg to 25 kg remains.

[0032] Further, the diameter of the nickel-based superalloy steel ingot for hot deformation is 290 mm to 310 mm.

[0033] In a third aspect, the present invention also provides an application of a nickel-based superalloy with hot deformation resistance in high-temperature fasteners.

[0034] The manufacturing method of the nickel-based superalloy with hot deformation resistance provided by the present invention effectively improves the high-temperature strength, toughness and plasticity, and thermal fatigue resistance of the prepared nickel-based superalloy through precise alloy composition design and process conditions of processes such as casting and vacuum consumable melting. At the same time, it effectively solves problems such as difficult forming and easy fracture during the preparation of the superalloy with hot deformation resistance, meets the requirements of alloys for fasteners at 800 °C, provides a solid and reliable material support for a new generation of aeroengines, heavy-duty gas turbines, etc., and has high practical value. Description of the Drawings

[0035] Figure 1 Photo of the intermediate billet prepared in Example 1;

[0036] Figure 2 Photo of the annealed electrode prepared in Comparative Example 2;

[0037] Figure 3 Photo of the intermediate billet prepared in Comparative Example 3. Detailed Embodiments

[0038] In order to make the objectives, technical solutions and advantages of the present invention clearer, the present invention will be further described in detail below with reference to embodiments. It should be understood that the specific embodiments described herein are only used to explain the present invention and are not used to limit the present invention.

[0039] To better illustrate the present invention, further examples are given below through embodiments.

[0040] Example 1

[0041] The present invention provides a GH4175 alloy for fasteners at 800 °C, and its chemical composition is:

[0042] C 0.06%, Cr 10.00%, Co 15.50%, W 3.00%, Mo 4.50%, Al 4.00%, Ti 2.50%, Nb 4.50%, V 0.60%, B 0.007%, Mg 0.002%, and the balance is Ni and unavoidable impurities.

[0043] The preparation steps of the above-mentioned GH4175 alloy for fasteners at 800 °C are as follows:

[0044] S1. When the vacuum induction furnace is powered on, add Ni-Cr alloy. The melting temperature is 1490 °C and the vacuum degree is ≤10 Pa. After the molten pool is formed, add Co, W, Mo, V and C in sequence. After all the alloy materials are melted, evacuate to ≤1 Pa, stir and degas the molten steel, refine for 60 min, add Al, Ti and Nb, continue to refine for 20 min. After sampling and analyzing that the composition is qualified, fill with argon. The argon pressure is controlled at 25000 Pa, add B and Mg, and complete pouring within 20 min. The pouring temperature is 1425 °C;

[0045] S2. After pouring, cool naturally for 40 min, demold to obtain an electrode with a diameter of φ250 mm; anneal the electrode. The annealing temperature is 1100 °C and the annealing time is 18 h. After annealing is completed, turn and polish the electrode;

[0046] S3. After welding the turned and polished electrode, start consumable melting. In the arc starting stage, control the current at 4.5 KA and the voltage at 22 V. The arc starting smelting time is 65 min. Enter the melting stage. The melting rate is 2.0 kg / min, and the molten droplets are controlled at 6 drops / s. Helium is used for cooling during the melting process. The helium pressure is controlled at 400 Pa. When 80 Kg remains in the melting, enter the filling stage, control the current at 3.0 KA and the voltage at 22 V. When 20 Kg remains, the filling ends;

[0047] S4. After the ingot cools in the furnace for 60 min, demold and cool slowly to obtain a φ305 mm consumable ingot.

[0048] Heat the above-prepared consumable ingot to 1150 °C, hold for 3 h, forge and bloom it to φ150 mm - φ160 mm through 8 times of forging. Then heat the billet to 1150 °C, hold for 1 h, and roll it to φ8 mm - φ12 mm through 5 times of rolling. Take samples from the φ8 mm - φ12 mm bars for testing, and test the high-temperature tensile and creep rupture properties at 800 °C. The high-temperature tensile property is tested according to the GB / T 4338-2006 Test method for high-temperature tensile of metallic materials, and the high-temperature creep rupture property is tested according to the GB / T 2039 Test method for uniaxial tensile creep of metallic materials. The results are shown in Table 1.

[0049] Table 1

[0050]

[0051] The photo of the above-prepared intermediate billet with a diameter of φ150 mm - φ160 mm is as Figure 1 shown. It can be seen from the figure that the surface quality of the billet is good, and there are no problems such as shrinkage cavity, crack and composition segregation.

[0052] Example 2

[0053] An embodiment of the present invention provides a GH4175 alloy for fasteners at 800°C, and its chemical composition is as follows:

[0054] C 0.04%, Cr 9.40%, Co 14.80%, W 2.90%, Mo 4.00%, Al 3.50%, Ti 2.30%, Nb 4.10%, V 0.40%, B 0.008%, Mg 0.001%, and the balance is Ni and unavoidable impurities.

[0055] The preparation steps of the above-mentioned GH4175 alloy for fasteners at 800°C are as follows:

[0056] S1, when the vacuum induction furnace is powered on, add Ni-Cr alloy, the melting temperature is 1470°C, the vacuum degree ≤ 10 Pa. After forming a molten pool, add Co, W, Mo, V, and C in sequence. After all the alloy materials are melted, evacuate to ≤ 1 Pa, stir and degas the molten steel, refine for 70 min, add Al, Ti, and Nb, continue to refine for 30 min. After sampling and analyzing that the composition is qualified, fill with argon, control the argon pressure to 18000 Pa, add B and Mg, and complete pouring within 20 min, and the pouring temperature is 1430°C;

[0057] S2, after pouring, cool naturally for 40 min, demold to obtain an electrode with a diameter of φ250 mm; anneal the electrode, the annealing temperature is 1000°C, the annealing time is 20 h. After annealing is completed, turn the electrode smooth;

[0058] S3, weld the turned electrode and then start consumable melting. Control the current at 2.5 KA and the voltage at 23 V during the arc starting stage, and the arc starting smelting time is 70 min. Enter the melting stage, the melting rate is 2.2 kg / min, control the droplet at 5 drops / S, cool with helium during the melting process, control the helium pressure at 300 Pa. When there are 70 Kg left in the melting, enter the filling stage, control the current at 2.5 KA and the voltage at 23 V. When there are 15 Kg left, the filling ends;

[0059] S4, after the ingot cools in the furnace for 60 min, demold and cool slowly to obtain a φ305 mm consumable ingot.

[0060] Example 3

[0061] An embodiment of the present invention provides a GH4175 alloy for fasteners at 800°C, and its chemical composition is as follows:

[0062] C 0.08%, Cr 11.00%, Co 16.00%, W 4.00%, Mo 4.80%, Al 3.80%, Ti 2.80%, Nb 4.60%, V 0.80%, B 0.005%, Mg 0.003%, and the balance is Ni and unavoidable impurities.

[0063] The preparation steps of the GH4175 alloy for fasteners at 800 °C are as follows:

[0064] S1. When the vacuum induction furnace is powered on, add Ni-Cr alloy with a melting temperature of 1480 °C and a vacuum degree ≤ 10 Pa. After forming a molten pool, add Co, W, Mo, V, and C in sequence. After all the alloy materials are melted, evacuate to ≤ 1 Pa, stir and degas the molten steel, refine for 90 min, add Al, Ti, and Nb, continue to refine for 25 min. After sampling and analyzing that the composition is qualified, fill with argon with the argon pressure controlled at 20000 Pa, add B and Mg, and complete pouring within 20 min. The pouring temperature is 1420 °C;

[0065] S2. After pouring, cool naturally for 40 min, demold to obtain an electrode with a diameter of φ250 mm; anneal the electrode at an annealing temperature of 1190 °C for 15 h. After annealing is completed, turn and polish the electrode;

[0066] S3. Weld the turned and polished electrode and then start consumable melting. Control the current at 5.2 KA and the voltage at 22 V during the arc starting stage, and the arc starting smelting time is 60 min. Enter the melting stage, with a melting rate of 2.5 kg / min and the droplet control at 8 drops / s. Cool with helium during the melting process, with the helium pressure controlled at 500 Pa. When 90 Kg remains in the melting process, enter the filling stage, control the current at 3.5 KA and the voltage at 22 V. When 25 Kg remains, the filling ends;

[0067] S4. After the ingot cools in the furnace for 60 min, demold and cool slowly to obtain a consumable ingot with a diameter of φ305 mm.

[0068] The consumable ingots prepared in Examples 2 - 3 are prepared into bars with a diameter of φ8 mm - φ12 mm according to the method of Example 1, and the high-temperature tensile and creep properties at 800 °C can both reach technical effects basically equivalent to those of Example 1.

[0069] Comparative Example 1

[0070] This comparative example provides a GH4175 alloy for fasteners at 800 °C, which is only different from Example 1 in that B and Mg are not added, and its chemical composition is:

[0071] C 0.06%, Cr 10.00%, Co 15.50%, W 3.00%, Mo 4.50%, Al 4.00%, Ti 2.50%, Nb 4.50%, V 0.60%, and the balance is Ni and unavoidable impurities.

[0072] The preparation steps of the GH4175 alloy for fasteners at 800 °C are as follows:

[0073] S1. When the vacuum induction furnace is powered on, add Ni-Cr alloy. The melting temperature is 1490°C and the vacuum degree is ≤10 Pa. After forming a molten pool, add Co, W, Mo, V, and C in sequence. After all the alloy materials are melted, evacuate to ≤1 Pa, stir and degas the molten steel for 60 min, add Al, Ti, and Nb, continue refining for 20 min. After sampling and analyzing that the composition is qualified, fill with argon. The argon pressure is controlled at 25000 Pa, and the molten steel is poured through a launder. The pouring temperature is 1425°C;

[0074] S2. After pouring, cool naturally for 40 min, demold to obtain an electrode with a diameter of φ250 mm; anneal the electrode. The annealing temperature is 1100°C and the annealing time is 18 h. After annealing is completed, turn and polish the electrode;

[0075] S3. After welding the turned and polished electrode, start consumable electrode melting. In the arcing stage, control the current at 4.5 KA and the voltage at 22 V. The arcing smelting time is 65 min. Enter the melting stage. The melting rate is 2.2 kg / min, and the droplet control is 6 drops / s. Helium is used for cooling during the melting process. The helium pressure is controlled at 400 Pa. When 80 Kg remains in the melting process, enter the filling stage. Control the current at 3.0 KA and the voltage at 22 V. When 20 Kg remains, the filling ends;

[0076] S4. After the ingot cools in the furnace for 60 min, demold and cool slowly to obtain a φ305 mm consumable electrode ingot.

[0077] Heat the above-prepared consumable electrode ingot to 1150°C and hold for 3 h. Forge and bloom it to φ150 mm - φ160 mm through 8 passes of forging. Then heat the billet to 1150°C and hold for 1 h. Roll it to φ8 mm - φ12 mm through 5 passes of rolling. Take samples from the φ8 mm - φ12 mm bars for testing, and test the high-temperature tensile and creep rupture properties at 800°C. The high-temperature tensile property is tested according to the method of GB / T 4338-2006 Metallic materials - Tensile testing at elevated temperatures, and the high-temperature creep rupture property is tested according to the method of GB / T 2039 Metallic materials - Uniaxial tensile creep testing method. The results are shown in Table 2.

[0078] Table 2

[0079]

[0080] It can be seen from the results that without adding B and Mg, compared with Example 1, the plasticity at 800°C decreases significantly, and the high-temperature creep rupture property also decreases to a certain extent.

[0081] Comparative Example 2

[0082] This comparative example provides a GH4175 alloy for 800°C fasteners. The only difference from Example 1 is the casting temperature, which is 1460°C. Its chemical composition is exactly the same as that of Example 1 and will not be elaborated here.

[0083] The preparation steps of the above-mentioned GH4175 alloy for 800°C fasteners are as follows:

[0084] S1. When the vacuum induction furnace is powered on, add Ni-Cr alloy with a melting temperature of 1490°C and a vacuum degree ≤ 10 Pa. After forming a molten pool, add Co, W, Mo, V, and C in sequence. After all the alloy materials are melted, evacuate to ≤ 1 Pa, stir and degas the molten steel, refine for 60 min, add Al, Ti, and Nb, continue to refine for 20 min. After sampling and analyzing that the composition is qualified, fill with argon with the argon pressure controlled at 25000 Pa, add B and Mg, and complete casting within 20 min with a casting temperature of 1460°C;

[0085] S2. After casting, cool naturally for 40 min, demold to obtain an electrode with a diameter of φ250 mm; anneal the electrode at an annealing temperature of 1100°C for 18 h. After annealing is completed, turn the electrode smooth.

[0086] The electrode prepared in this comparative example has serious shrinkage cavities and fractures, as Figure 2 shown.

[0087] Comparative Example 3

[0088] This comparative example provides a GH4175 alloy for 800°C fasteners. The only difference from Example 1 is that the melting rate is replaced with 2.8 kg / min. Its chemical composition is exactly the same as that of Example 1 and will not be elaborated here.

[0089] The preparation steps of the above-mentioned GH4175 alloy for 800°C fasteners are as follows:

[0090] S1. When the vacuum induction furnace is powered on, add Ni-Cr alloy with a melting temperature of 1490°C and a vacuum degree ≤ 10 Pa. After forming a molten pool, add Co, W, Mo, V, and C in sequence. After all the alloy materials are melted, evacuate to ≤ 1 Pa, stir and degas the molten steel, refine for 60 min, add Al, Ti, and Nb, continue to refine for 20 min. After sampling and analyzing that the composition is qualified, fill with argon with the argon pressure controlled at 25000 Pa, add B and Mg, and complete casting within 20 min with a casting temperature of 1425°C;

[0091] S2. After casting, cool naturally for 40 min, demold to obtain an electrode with a diameter of φ250 mm; anneal the electrode at an annealing temperature of 1100°C for 18 h. After annealing is completed, turn the electrode smooth;

[0092] S3. After welding the turned electrode, start consumable melting. During the arc starting stage, control the current at 4.5 KA, the voltage at 22 V, and the arc starting smelting time at 65 min. Then enter the melting stage. The melting rate is 2.8 kg / min, the droplet control is 6 drops / s, and helium gas is used for cooling during the melting process. Control the helium gas pressure at 400 Pa. When 80 Kg remains for melting, enter the filling stage, control the current at 3.0 KA, the voltage at 22 V. When 20 Kg remains, the filling ends;

[0093] S4. After the ingot is cooled in the furnace for 60 min, demold it and cool it slowly to obtain a φ305 mm consumable ingot.

[0094] Heat the above-prepared consumable ingot to 1150 °C and hold for 3 h. Forge and bloom it 8 times to φ150 mm - φ160 mm. The photo of the obtained intermediate billet is as Figure 3 shown. It can be seen that by changing the consumable melting rate, the component segregation is serious.

[0095] The above are only the preferred embodiments of the present invention and are not intended to limit the present invention. Any modification, equivalent replacement, or improvement made within the spirit and principle of the present invention shall be included in the protection scope of the present invention.

Claims

1. A nickel-based high temperature deformation alloy, characterized in that: Its chemical composition is: C 0.04% ~ 0.08%, Cr 9.40% ~ 11.00%, Co 14.80% ~ 16.00%, W 2.90% ~ 4.00%, Mo 4.00% ~ 4.80%, Al 3.50% ~ 4.00%, Ti 2.30% ~ 2.80%, Nb 4.10% ~ 4.60%, V 0.40% ~ 0.80%, B 0.005% ~ 0.008%, Mg 0.001% ~ 0.003%, and the balance is Ni and unavoidable impurities.

2. The method for producing a nickel-based high temperature deformed alloy according to claim 1, characterized in that: The steps include: S1, adding Ni-Cr alloy into a vacuum induction furnace, and after melting, sequentially adding Co, W, Mo, V and C to obtain alloy liquid; S2, vacuum refining the alloy liquid, adding Al, Ti and Nb, filling with argon after refining, adding B and Mg, casting at 1420° C. to 1430° C., demolding, annealing, and obtaining a consumable electrode; S3, after welding the consumable electrode, perform vacuum consumable smelting, fill helium for cooling during the smelting process, and after the smelting is completed, demould and slowly cool to obtain a nickel-based high-temperature deformable alloy steel ingot; wherein the melting rate of the vacuum consumable smelting is 2.0kg / min~2.5kg / min, and the pressure of the helium is 300Pa~500Pa.

3. The method for manufacturing a nickel-based high temperature deformed alloy according to claim 2, characterized in that: In S1, the melting temperature is 1470°C to 1490°C, and the vacuum degree is ≤10Pa.

4. The method for manufacturing a nickel-based high temperature deformed alloy according to claim 2, characterized in that: In S2, the vacuum refining temperature is 1470°C to 1490°C, the vacuum degree is ≤1Pa, and the vacuum refining time is 60min to 90min; and / or In S2, after adding B and Mg, the pouring was completed within 20 minutes.

5. The method for manufacturing a nickel-based high temperature deformed alloy according to claim 2, characterized in that: In S2, the pressure of the argon gas is 18000Pa to 25000Pa; and / or In S2, the diameter of the consumable electrode is 240 mm to 260 mm.

6. The method for manufacturing a nickel-based high temperature deformed alloy according to claim 2, characterized in that: After adding Al, Ti and Nb to S2, continue refining for 20min to 30min; and / or In S2, the annealing temperature is 1000°C to 1190°C, and the annealing time is 15h to 20h.

7. The method for manufacturing a nickel-based high temperature deformed alloy according to claim 2, characterized in that: In S3, the vacuum consumable melting includes an arc starting stage, a melting stage and a filling stage; wherein the droplet speed in the melting stage is 5 drops / s to 8 drops / s.

8. The method for manufacturing a nickel-based high temperature deformed alloy according to claim 7, characterized in that: In S3, the current in the arc starting stage is 2.5KA-5.2KA, the voltage is 22V-23V, and the smelting time in the arc starting stage is 60min-70min; and / or In S3, the current in the filling stage is 2.5KA-3.5KA, and the voltage is 22V-23V; and / or In S3, the filling stage is carried out when 70kg to 90kg of smelting remains, and the filling is completed when 15kg to 25kg remains.

9. The method for manufacturing a nickel-based high temperature deformed alloy according to claim 2, characterized in that: The diameter of the nickel-based high-temperature deformable alloy steel ingot is 290 mm to 310 mm.

10. Use of the nickel-based high temperature deformation alloy according to claim 1 in high temperature resistant fasteners.

Images