CN110724826A - Electroslag remelting process for nickel-based superalloy - Google Patents
Electroslag remelting process for nickel-based superalloy Download PDFInfo
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Abstract
An electroslag remelting process for a nickel-based superalloy is characterized by comprising, by mass, 15-20 parts of Cr, 15-20 parts of Co, 5-10 parts of Mo, 2-6 parts of W, 1-4 parts of Ta, 1-4 parts of Al and 2.2-2.5 parts of Ti, wherein at least 2 of the four main materials of Fe, V, Nb and rare earth are selectively added, the total content of the selectively added materials is 1-5, and the balance is composed of Ni and unavoidable impurities; the electroslag remelting process adopts a specific slag system and a specific voltage, current and cooling process.
Description
Technical Field
The invention relates to the field of nickel-based high-temperature alloy, in particular to an electroslag remelting process suitable for manufacturing high-temperature structural parts used in the fields of aviation, aerospace, energy, thermal spraying, coating and the like.
Background
Different working environments of the high-temperature alloy put higher requirements on material properties. Such as high temperature, some parts are required to operate for a long time at a temperature above 800 ℃. For example, high stress is applied to some high-temperature parts, and the high stress is applied to the high-temperature parts due to the centrifugal action caused by vibration, air flow scouring and particularly rotation, and the stress of the turbine blade can reach 300-409 MPa. Such as oxidation and corrosion.
In addition, some prior arts of nickel-based superalloys have disadvantages such as a large amount of inclusions and segregation of components. The invention aims to improve an electroslag remelting process of a nickel-based superalloy, which has the advantages of low inclusion content, uniform component distribution, low segregation and even no segregation.
Disclosure of Invention
The invention aims to provide an electroslag ingot with smooth surface quality, qualified components and internal quality, obviously improved yield, less inclusion content, uniform component distribution, low segregation and even no segregation, reduced production cost, reduced energy consumption, high purity of the plate and improved corrosion resistance.
An electroslag remelting process for nickel-based superalloy, which comprises the following preparation steps:
the nickel-based high-temperature alloy comprises 15-20 mass percent of Cr, 15-20 mass percent of Co, 5-10 mass percent of Mo, 2-6 mass percent of W, 1-4 mass percent of Ta, 1-4 mass percent of Al and 2.2-2.5 mass percent of Ti, wherein at least 2 kinds of Fe, V, Nb and rare earth are selectively added, the total content of the selectively added materials is 1-5, and the balance of Ni and inevitable impurities form a preparation raw material; the electroslag remelting process adopts a slag system consisting of CaF2, Al2O3, CaO, MgO and TiO2, the remelting voltage is 45-48V, the remelting current is 4500-.
An electroslag remelting process for nickel-based superalloy, which comprises the following preparation steps:
(1) determining a target product: the nickel-based high-temperature alloy comprises the following components in percentage by mass: cr 17.5-18, Co 16.8-17.5, Mo7.2-7.5, W4.5-5, Ta 3.2-3.5, Al 3.5-3.8, Ti 2.2-2.5, Fe 2-3, V: 0.55 to 0.65 percent of Ni, 0.15 to 0.25 percent of Mn, 0.1 to 0.15 percent of Si, 0.01 to 0.03 percent of C, 0.01 to 0.02 percent of Zr, 0.0015 to 0.003 percent of B, 0.005 to 0.05 percent of Sc, 0.10 to 0.20 percent of Hf, and the balance of Ni and inevitable impurities;
(2) smelting in a vacuum induction furnace: proportioning according to the chemical composition proportion of a target product and combining the burning loss amount, and adding the mixture into a vacuum induction smelting furnace for smelting; selecting Ni-Co intermediate alloy, Ni-Cr intermediate alloy, Ni-Mo intermediate alloy and Fe-Mo intermediate alloy, selecting proper intermediate alloy from W, Ta, V and/or Nb, Zr and Hf, and selecting low-melting-point intermediate alloy or simple substance from Ti, Al, Mn, Si, C, B and rare earth; loading into a crucible, adding a covering agent at the upper part when the raw materials are completely melted, wherein the covering agent consists of 35-45% of fluorite and 55-65% of lime by mass, the adding amount of the covering agent accounts for 2-5% of the total mass of the alloy in the crucible, refining for 20-40min after complete melting, the adding amount of the refining agent accounts for 2.5-3.5% of the total mass of the alloy in the crucible in the refining process, the refining agent is an alloy containing barium, aluminum and calcium, adding a desulfurizing agent at the later stage of refining, and stirring after refining; slagging off, namely preparing for casting when the temperature of the nickel-based high-temperature alloy liquid melt reaches 1500-1700 ℃;
(3) remelting preparation: preheating the mould to 200 ℃, keeping the temperature for 30min, and casting to obtain an electrode rod with the diameter of 350 mm;
(4) electroslag remelting: taking the electrode bar obtained in the step (3) as a consumable electrode, slowly descending the consumable electrode and inserting the consumable electrode into an electroslag furnace, wherein the insertion depth is 100-160mm, regulating remelting voltage and remelting current after electrifying and arcing, and forming a remelting electroslag ingot under the forced cooling of a water-cooled crystallizer; the remelting voltage is 45-48V, the remelting current is 4500-; the water flow of the water-cooled crystallizer is 1-1.2m3/min, so as to ensure that the cooling speed reaches 20-40 ℃/s, promote the solidification of the electroslag ingot and reduce the segregation of the electroslag ingot; the used slag system is 57-60% of CaF2, 15-20% of Al2O3, 13-18% of CaO, 3-4% of MgO, 10-12% of TiO2 and inevitable impurities;
(5) forging: heating the electroslag ingot to 1100-1150 ℃, preserving heat for 2-3 hours, forging into a bar, air cooling the forged bar to room temperature, and performing surface polishing treatment on the obtained bar to obtain a finished alloy material.
The electroslag remelting process of the nickel-based superalloy is characterized by comprising the following steps: the covering agent consists of fluorite and lime with the mass ratio of 40 percent and 60 percent, the adding amount of the covering agent accounts for 4 percent of the total mass of the alloy in the crucible, the covering agent is refined for 30min after being completely melted, the adding amount of the refining agent accounts for 3 percent of the total mass of the alloy in the crucible in the refining process, the refining agent is the alloy containing barium, aluminum and calcium, a desulfurizing agent is added in the later period of refining, and the mixture is stirred after the refining is finished; and (4) slagging off, namely preparing for casting when the temperature of the nickel-based high-temperature alloy liquid melt reaches 1500-1600 ℃.
The electroslag remelting process of the nickel-based superalloy is characterized in that the nickel-based superalloy comprises the following components in percentage by mass: cr 17.5, Co 17.5, Mo7.2, W5, Ta 3.2, Al 3.8, Ti 2.5, Fe 3, V: 0.55, Mn 0.15, Si0.1, C0.01, Zr0.01, B0.003, Sc 0.05, Hf 0.20, and the balance of Ni and unavoidable impurities.
The electroslag remelting process of the nickel-based superalloy is characterized in that the nickel-based superalloy comprises the following components in percentage by mass: cr 18, Co 16.8, Mo 7.5, W4.5, Ta3.5, Al 3.5, Ti 2.2, Fe 2, V: 0.65, Mn 0.25, Si0.15, C0.03, Zr 0.02, B0.0015, Sc 0.005, Hf0.10, and the balance Ni and unavoidable impurities.
The electroslag remelting process of the nickel-based superalloy is characterized in that the nickel-based superalloy comprises the following components in percentage by mass: cr 17.5, Co 17, Mo 7.4, W4.75, Ta 3.3, Al 3.7, Ti 2.4, Fe 2.5, V: 0.6, 0.2 Mn, 0.12 Si, 0.02C, 0.015 Zr, 0.002B, 0.03 Sc and 0.15 Hf, and the balance Ni and unavoidable impurities.
The functions and ranges of the alloying elements in the present invention are as follows:
co can improve high temperature strength. Further, the γ ' phase [ Ni3(Al, Ti, Nb, Ta) ] is also dissolved in a solid state, and this has the effect of strengthening the γ ' phase and increasing the amount of γ ' phase precipitated. However, too much Co generates intermetallic compound phases, which lower the mechanical strength and increase the alloy cost. On the other hand, if Co is too low, the strength decreases. Therefore, Co is 15 to 20, more preferably 16.8 to 17.5%.
Cr is an element that is solid-solution strengthened, and contributes to improvement of oxidation resistance and corrosion resistance. Moreover, the M23C6 type carbide is also indispensable as a constituent element, and the creep strength of the alloy can be maintained. In addition, Cr can also improve oxidation resistance in high temperature environments. When the Cr content is less than 15%, the oxidation resistance is lowered. When the Cr content exceeds 20%, precipitation of M23C6 type carbide is significantly promoted to increase the tendency to coarsen, and the strength and ductility are deteriorated when the alloy is held at high temperature for a long time. Therefore, Cr is 15 to 20%, more preferably 17.5 to 18%.
Mo has strong solid solution strengthening effect, can effectively block dislocation movement, improves alloy performance, and is beneficial to comprehensive strengthening of the alloy. However, excessive addition of Mo also causes precipitation of harmful phases, which adversely affect the hot corrosion properties of the alloy, and therefore the content of Mo is controlled to be 5-10%, preferably 7.2-7.5%.
The solid solution strengthening effect of W in the nickel-based high-temperature alloy is strong, and W is also dissolved in a gamma 'strengthening phase in a large amount, so that the thermal stability of the gamma' phase is improved. Excessive addition of W results in supersaturation of the gamma phase, destabilizing the microstructure. Excessive addition of W also affects the castability of the alloy, and equiaxed grains and other defects appear in the growth of single crystals. Therefore, the content of W is controlled to be W2-6%, preferably W4.5-5%.
Ta is also one of main forming elements of a gamma 'phase in the nickel-based single crystal superalloy, and has the effect of inhibiting the aggregation and growth of the gamma' phase, so that the heat strength of the alloy can be improved, the casting performance of the alloy can be improved, the structural stability of the alloy is not reduced, and a high Ta content can be added into the alloy. However, too high Ta increases the eutectic content in the alloy and the heat treatment is complicated. Therefore, the amount of Ta added in the present alloy is controlled to Ta 1 to 4%, preferably Ta 3.2 to 3.5%.
Al forms a gamma' phase [ Ni3(Al, Ti, Nb, Ta) ] together with Ni, and the high-temperature strength of the Ni-based cast alloy can be improved by precipitation. In addition, the high temperature corrosion resistance is improved. If the content of Al is less than 1%, the γ 'phase is not sufficiently precipitated, the strengthening effect is not sufficient, and if Ti, Nb, and Ta are present in a large amount, the γ' phase is unstable, and η phase (Ni3Ti) and δ phase [ Ni3(Nb, Ta) ] are precipitated, thereby deteriorating the workability. On the other hand, if a large amount of the eutectic γ 'phase is added, a large amount of the eutectic γ' phase precipitates during casting, and the high-temperature strength is lowered. Therefore, Al is 1 to 4%, more preferably Al is 3.5 to 3.8%.
Like Al, Ti forms a γ' phase [ Ni3(Al, Ti, Nb, Ta) ] together with Ni, and the high-temperature strength of the Ni-based superalloy can be improved by precipitation. If the Ti content is less than 2.2%, the precipitation strengthening effect is not significant, but if the Ti content exceeds 2.5%, a brittle η phase (Ni3Ti) precipitates, resulting in a decrease in high-temperature strength and an increase in defect sensitivity. Therefore, Ti is 2.2-2.5%.
Fe contributes to the reduction of the cost of the alloy in the field of Ni-based superalloy. However, if added in a large amount, not only a decrease in high-temperature strength is caused, but also an increase in the coefficient of thermal expansion of the alloy is involved, which has an effect on the service life under high-temperature conditions. Thus, Fe 2-3%.
V contributes to the high temperature strength by forming carbide by combining with C. If the content of V is less than 0.55%, the above-mentioned effects cannot be exhibited, and if the content of V exceeds 0.65%, precipitates cause embrittlement. Thus, V: 0.55 to 0.65 percent.
On one hand, Mn has a deoxidizing effect, can influence the austenitizing temperature at the same time, and has a certain improvement effect on the strength. However, if the content is too high, the high-temperature oxidation characteristics are degraded and the ductility is degraded by the precipitation of η phase (Ni3 Ti). Therefore, Mn is 0.15 to 0.25%.
Si is useful as a deoxidizer in melt refining. It can also improve oxidation resistance. However, if the content is too high, a decrease in ductility is caused. The appropriate Si content is 0.1-0.15% Si.
C is a constituent element of M23C6 type carbide which is a strengthening phase, and particularly, one of important factors for maintaining the creep strength of an alloy is to precipitate M23C6 type carbide in a high temperature environment of 700 ℃. In addition, coarsening of crystal grains can be prevented. When the content of C is less than 0.01%, a sufficient amount of carbide precipitation cannot be ensured. If the content of C exceeds 0.04%, the possibility of component segregation increases when manufacturing a large-sized structural member, and corrosion resistance and ductility deteriorate. Therefore, C is 0.01-0.03%.
Zr enters the crystal boundary, and the high-temperature strength can be improved. In addition, the carbon forms carbide in combination with C, which contributes to the improvement of high-temperature strength. If the Zr content is less than 0.01%, the above-mentioned effects cannot be exhibited, and if the Zr content exceeds 0.02%, the high-temperature strength is rather lowered, and the ductility is also lowered. Therefore, the Zr content is defined to be 0.01 to 0.02%.
B can play a role in deterioration. The boron is deviated and gathered in the grain boundary, which is beneficial to changing the form of a second phase on the grain boundary, leading the second phase to be easy to spheroidize and improving the strength of the grain boundary. In the aspect of high-temperature alloy, boron mainly affects grain boundary diffusion and precipitation by grain boundary segregation, and further has a strengthening effect on the durability and creep property of the alloy. Therefore, B is 0.0015 to 0.003%.
The rare earth elements have obvious effect on improving the performance of the high-temperature alloy. A small amount of rare earth elements are added into the high-temperature alloy, so that the vulcanization resistance, the high-temperature strength and the thermoplasticity can be improved, and meanwhile, the oxidation resistance and the long service life of the high-temperature alloy can be improved. The rare earth elements are in various types, and the inventor finds that the rare earth Sc is more beneficial to the spheroidization ratio of the powder and the final product made of the powder, such as a turbine disk and a compressor disk. Therefore, 0.005-0.05% of Sc is added into the alloy.
Hf is a grain boundary strengthening element, and elements such as C, O form network carbon oxides in the PPB powder, so that the elements hinder the diffusion and the continuity among metal particles and become the crack starting points of the alloy. Therefore, the grain boundary strengthening element Hf is added in order to weaken the adverse effect of the carbon-oxygen compound on the grain boundary, if any. Hf can obviously improve the corrosion resistance; the addition of hafnium element changes the morphology of carbide, when the Hf is more than 0.2%, the skeleton carbide is converted into block carbide, the Hf belongs to a positive segregation element and is easy to aggregate among dendrites, and is also a main element forming a gamma 'phase, so that the growth of the gamma' phase in the solidification process of the alloy can be prevented, the size of the gamma 'phase is reduced, and the formation of gamma + gamma' eutectic can be remarkably promoted. Therefore, the content of Hf is defined as Hf0.10-0.20%.
The invention has the beneficial effects that:
(1) the electroslag ingot production process has smooth surface quality, qualified components and internal quality, obviously improved yield, low inclusion content, uniform component distribution, low segregation and even no segregation, reduced production cost, reduced energy consumption, high purity of the plate and improved corrosion resistance, and lays a foundation for the subsequent high-temperature alloy products to have excellent performance;
(2) adding alloy matrix strengthening elements, grain refining and grain boundary strengthening elements, and adjusting the percentage content of each element. By means of strengthening, the alloy matrix is strengthened, the quality of the grain boundary is improved, and the alloy obtains good comprehensive performance. Thereby realizing that the alloy has high hardness and strength and good toughness;
(3) according to the invention, by designing a new slag system, the content of TiO2 is obviously higher than that of the existing common slag system, and the fluctuation of the content of Ti is avoided, so that the parameters of waste products are avoided within the range of the final high-temperature alloy product and the target components;
(4) the invention designs a new slag system, matches with a specific electroslag remelting process, and makes the strength and plasticity of the alloy reach a better matching relation through the interaction among all components in the alloy, and the alloy is particularly suitable for parts such as aeroengine turbine discs and the like used below 750 ℃.
Detailed Description
Example 1
An electroslag remelting process for nickel-based superalloy, which comprises the following preparation steps:
(1) determining a target product: the nickel-based high-temperature alloy comprises the following components in percentage by mass: cr 17.5, Co 17.5, Mo7.2, W5, Ta 3.2, Al 3.8, Ti 2.5, Fe 3, V: 0.55, 0.15 of Mn, 0.1 of Si, 0.01 of C, 0.01 of Zr, 0.003 of B, 0.05 of Sc and 0.20 of Hf, and the balance of Ni and inevitable impurities;
(2) smelting in a vacuum induction furnace: proportioning according to the chemical composition proportion of a target product and combining the burning loss amount, and adding the mixture into a vacuum induction smelting furnace for smelting; selecting Ni-Co intermediate alloy, Ni-Cr intermediate alloy, Ni-Mo intermediate alloy and Fe-Mo intermediate alloy, selecting proper intermediate alloy from W, Ta, V and/or Nb, Zr and Hf, and selecting low-melting-point intermediate alloy or simple substance from Ti, Al, Mn, Si, C, B and rare earth; loading into a crucible, adding a covering agent at the upper part when the raw materials are completely melted, wherein the covering agent consists of 35-45% of fluorite and 55-65% of lime by mass, the adding amount of the covering agent accounts for 2-5% of the total mass of the alloy in the crucible, refining for 20-40min after complete melting, the adding amount of the refining agent accounts for 2.5-3.5% of the total mass of the alloy in the crucible in the refining process, the refining agent is an alloy containing barium, aluminum and calcium, adding a desulfurizing agent at the later stage of refining, and stirring after refining; slagging off, namely preparing for casting when the temperature of the nickel-based high-temperature alloy liquid melt reaches 1500-1700 ℃;
(3) remelting preparation: preheating the mould to 200 ℃, keeping the temperature for 30min, and casting to obtain an electrode rod with the diameter of 350 mm;
(4) electroslag remelting: taking the electrode bar obtained in the step (3) as a consumable electrode, slowly descending the consumable electrode and inserting the consumable electrode into an electroslag furnace, wherein the insertion depth is 100-160mm, regulating remelting voltage and remelting current after electrifying and arcing, and forming a remelting electroslag ingot under the forced cooling of a water-cooled crystallizer; the remelting voltage is 45-48V, the remelting current is 4500-; the water flow of the water-cooled crystallizer is 1-1.2m3/min, so as to ensure that the cooling speed reaches 20-40 ℃/s, promote the solidification of the electroslag ingot and reduce the segregation of the electroslag ingot; the used slag system is 57-60% of CaF2, 15-20% of Al2O3, 13-18% of CaO, 3-4% of MgO, 10-12% of TiO2 and inevitable impurities;
(5) forging: heating the electroslag ingot to 1100-1150 ℃, preserving heat for 2-3 hours, forging into a bar, air cooling the forged bar to room temperature, and performing surface polishing treatment on the obtained bar to obtain a finished alloy material.
In order to further improve the performance of the bar after heat treatment, heat treatment is carried out after the step (5), specifically, heating is carried out at a heating rate of 50-60 ℃/min to 1150-1180 ℃ for 3-5 h, and then oil quenching is carried out; then slowly raising the temperature to 880-900 ℃ at the speed of 20-30 ℃/min, and treating for 15-20 h.
Placing the product after the heat treatment at 900 ℃ and 200MPa, wherein the lasting life is more than or equal to 380 h; at 750 ℃, the yield strength is more than or equal to 1200MPa, the tensile strength is more than or equal to 1400MPa, and the elongation is more than or equal to 25 percent.
Example 2
An electroslag remelting process for nickel-based superalloy, which comprises the following preparation steps:
(1) determining a target product: the nickel-based high-temperature alloy comprises the following components in percentage by mass: cr 18, Co 16.8, Mo 7.5, W4.5, Ta3.5, Al 3.5, Ti 2.2, Fe 2, V: 0.65, Mn 0.25, Si0.15, C0.03, Zr 0.02, B0.0015, Sc 0.005, Hf0.10, the balance consisting of Ni and unavoidable impurities;
(2) smelting in a vacuum induction furnace: proportioning according to the chemical composition proportion of a target product and combining the burning loss amount, and adding the mixture into a vacuum induction smelting furnace for smelting; selecting Ni-Co intermediate alloy, Ni-Cr intermediate alloy, Ni-Mo intermediate alloy and Fe-Mo intermediate alloy, selecting proper intermediate alloy from W, Ta, V and/or Nb, Zr and Hf, and selecting low-melting-point intermediate alloy or simple substance from Ti, Al, Mn, Si, C, B and rare earth; loading into a crucible, adding a covering agent at the upper part when the raw materials are to be completely melted, wherein the covering agent consists of 35-45% of fluorite and 55-65% of lime by mass, the adding amount of the covering agent accounts for 2-5% of the total mass of the alloy in the crucible, refining for 20-40min after complete melting, the adding amount of the refining agent accounts for 2.5-3.5% of the total mass of the alloy in the crucible in the refining process, the refining agent is an alloy containing barium, aluminum and calcium, adding a desulfurizing agent in the later stage of refining, and stirring after refining: slagging off, namely preparing for casting when the temperature of the nickel-based high-temperature alloy liquid melt reaches 1500-1700 ℃;
(3) remelting preparation: preheating the mould to 200 ℃, keeping the temperature for 30min, and casting to obtain an electrode rod with the diameter of 350 mm;
(4) electroslag remelting: taking the electrode bar obtained in the step (3) as a consumable electrode, slowly descending the consumable electrode and inserting the consumable electrode into an electroslag furnace, wherein the insertion depth is 100-160mm, regulating remelting voltage and remelting current after electrifying and arcing, and forming a remelting electroslag ingot under the forced cooling of a water-cooled crystallizer; the remelting voltage is 45-48V, the remelting current is 4500-; the water flow of the water-cooled crystallizer is 1-1.2m3/min, so as to ensure that the cooling speed reaches 20-40 ℃/s, promote the solidification of the electroslag ingot and reduce the segregation of the electroslag ingot; the used slag system is 57-60% of CaF2, 15-20% of Al2O3, 13-18% of CaO, 3-4% of MgO, 10-12% of TiO2 and inevitable impurities;
(5) forging: heating the electroslag ingot to 1100-1150 ℃, preserving heat for 2-3 hours, forging into a bar, air cooling the forged bar to room temperature, and performing surface polishing treatment on the obtained bar to obtain a finished alloy material.
In order to further improve the performance of the bar after heat treatment, heat treatment is carried out after the step (5), specifically, heating is carried out at a heating rate of 50-60 ℃/min to 1150-1180 ℃ for 3-5 h, and then oil quenching is carried out; then slowly raising the temperature to 880-900 ℃ at the speed of 20-30 ℃/min, and treating for 15-20 h.
Placing the product after the heat treatment at 900 ℃ and 200MPa, wherein the lasting life is more than or equal to 420 h; at 750 ℃, the yield strength is more than or equal to 1250MPa, the tensile strength is more than or equal to 1480MPa, and the elongation is more than or equal to 28 percent.
Example 3
An electroslag remelting process for nickel-based superalloy, which comprises the following preparation steps:
(1) determining a target product: the nickel-based high-temperature alloy comprises the following components in percentage by mass: cr 17.5, Co 17, Mo 7.4, W4.75, Ta 3.3, Al 3.7, Ti 2.4, Fe 2.5, V: 0.6, 0.2 of Mn, 0.12 of Si, 0.02 of C, 0.015 of Zr, 0.002 of B, 0.03 of Sc and 0.15 of Hf, and the balance of Ni and inevitable impurities;
(2) smelting in a vacuum induction furnace: proportioning according to the chemical composition proportion of a target product and combining the burning loss amount, and adding the mixture into a vacuum induction smelting furnace for smelting; selecting Ni-Co intermediate alloy, Ni-Cr intermediate alloy, Ni-Mo intermediate alloy and Fe-Mo intermediate alloy, selecting proper intermediate alloy from W, Ta, V and/or Nb, Zr and Hf, and selecting low-melting-point intermediate alloy or simple substance from Ti, Al, Mn, Si, C, B and rare earth; loading into a crucible, adding a covering agent at the upper part when the raw materials are completely melted, wherein the covering agent consists of 35-45% of fluorite and 55-65% of lime by mass, the adding amount of the covering agent accounts for 2-5% of the total mass of the alloy in the crucible, refining for 20-40min after complete melting, the adding amount of the refining agent accounts for 2.5-3.5% of the total mass of the alloy in the crucible in the refining process, the refining agent is an alloy containing barium, aluminum and calcium, adding a desulfurizing agent at the later stage of refining, and stirring after refining; slagging off, namely preparing for casting when the temperature of the nickel-based high-temperature alloy liquid melt reaches 1500-1700 ℃;
(3) remelting preparation: preheating the mould to 200 ℃, keeping the temperature for 30min, and casting to obtain an electrode rod with the diameter of 350 mm;
(4) electroslag remelting: taking the electrode bar obtained in the step (3) as a consumable electrode, slowly descending the consumable electrode and inserting the consumable electrode into an electroslag furnace, wherein the insertion depth is 100-160mm, regulating remelting voltage and remelting current after electrifying and arcing, and forming a remelting electroslag ingot under the forced cooling of a water-cooled crystallizer; the remelting voltage is 45-48V, the remelting current is 4500-; the water flow of the water-cooled crystallizer is 1-1.2m3/min, so as to ensure that the cooling speed reaches 20-40 ℃/s, promote the solidification of the electroslag ingot and reduce the segregation of the electroslag ingot; the used slag system is 57-60% of CaF2, 15-20% of Al2O3, 13-18% of CaO, 3-4% of MgO, 10-12% of TiO2 and inevitable impurities;
(5) forging: heating the electroslag ingot to 1100-1150 ℃, preserving heat for 2-3 hours, forging into a bar, air cooling the forged bar to room temperature, and performing surface polishing treatment on the obtained bar to obtain a finished alloy material.
In order to further improve the performance of the bar after heat treatment, heat treatment is carried out after the step (5), specifically, heating is carried out at a heating rate of 50-60 ℃/min to 1150-1180 ℃ for 3-5 h, and then oil quenching is carried out; then slowly raising the temperature to 880-900 ℃ at the speed of 20-30 ℃/min, and treating for 15-20 h.
Placing the product after the heat treatment at 900 ℃ and 200MPa, wherein the lasting life is more than or equal to 400 h; at 750 ℃, the yield strength is more than or equal to 1220MPa, the tensile strength is more than or equal to 1440MPa, and the elongation is more than or equal to 26.5 percent.
Comparative example 1
In general, comparative example 1 differs from example 1 mainly in the change in composition, and processes (2) to (5) are in accordance with examples.
Specifically, the preparation method of the nickel-based superalloy powder comprises the following steps of: cr 14.5, co14.5, Mo 4.8, W1.8, Ta 0.9, Al 0.8, Ti 2, Fe 2.5, V: 0.5, Mn 0.15, Si0.1, C0.01, Zr0.01, B0.003, Sc 0.05, Hf 0.20, and the balance of Ni and unavoidable impurities;
in order to further improve the performance of the bar after heat treatment, heat treatment is carried out after the step (5), specifically, heating is carried out at a heating rate of 50-60 ℃/min to 1150-1180 ℃ for 3-5 h, and then oil quenching is carried out; then slowly raising the temperature to 880-900 ℃ at the speed of 20-30 ℃/min, and treating for 15-20 h.
Placing the product after the heat treatment at 900 ℃ and 200MPa, wherein the lasting life is more than or equal to 300 h; at 750 ℃, the yield strength is more than or equal to 1000MPa, the tensile strength is more than or equal to 1150MPa, and the elongation is more than or equal to 15 percent.
Comparative example 2
In general, comparative example 2 differs from example 1 mainly in the change in composition, and processes (2) to (5) are in accordance with examples.
Specifically, the preparation method of the nickel-based superalloy powder comprises the following steps of: cr 21, Co21, Mo 10.5, W6.5, Ta 4.2, Al 4.2, Ti 2.6, Fe 3, V: 0.55, Mn 0.15, Si0.1, C0.01, Zr0.01, B0.003, Sc 0.05, Hf 0.20, and the balance of Ni and unavoidable impurities;
in order to further improve the performance of the bar after heat treatment, heat treatment is carried out after the step (5), specifically, heating is carried out at a heating rate of 50-60 ℃/min to 1150-1180 ℃ for 3-5 h, and then oil quenching is carried out; then slowly raising the temperature to 880-900 ℃ at the speed of 20-30 ℃/min, and treating for 15-20 h.
Placing the product after the heat treatment at 900 ℃ and 200MPa, wherein the lasting life is more than or equal to 380 h; at 750 ℃, the yield strength is more than or equal to 1250MPa, the tensile strength is more than or equal to 1330MPa, and the elongation is more than or equal to 24 percent.
Comparative example 3
In general, the main difference between comparative example 3 and example 1 is the change of slag system in the production process (4).
Specifically, the preparation step (4) is as follows: electroslag remelting: taking the electrode bar obtained in the step (3) as a consumable electrode, slowly descending the consumable electrode and inserting the consumable electrode into an electroslag furnace, wherein the insertion depth is 100-160mm, regulating remelting voltage and remelting current after electrifying and arcing, and forming a remelting electroslag ingot under the forced cooling of a water-cooled crystallizer; the remelting voltage is 45-48V, the remelting current is 4500-; the water flow of the water-cooled crystallizer is 1-1.2m3/min, so as to ensure that the cooling speed reaches 20-40 ℃/s, promote the solidification of the electroslag ingot and reduce the segregation of the electroslag ingot; the used slag system is 50-60% of CaF2, 15-20% of Al2O3, 13-18% of CaO, 5-8% of MgO, 1-8% of TiO2 and inevitable impurities;
in order to further improve the performance of the bar after heat treatment, heat treatment is carried out after the step (5), specifically, heating is carried out at a heating rate of 50-60 ℃/min to 1150-1180 ℃ for 3-5 h, and then oil quenching is carried out; then slowly raising the temperature to 880-900 ℃ at the speed of 20-30 ℃/min, and treating for 15-20 h.
Placing the product after the heat treatment at 900 ℃ and 200MPa, wherein the lasting life is more than or equal to 330 h; at 750 ℃, the yield strength is more than or equal to 1120MPa, the tensile strength is more than or equal to 1220MPa, and the elongation is more than or equal to 21 percent.
Comparative example 4
In general, the main difference between comparative example 3 and example 1 is the change of slag system in the production process (4).
Specifically, the preparation step (4) is as follows: electroslag remelting: taking the electrode bar obtained in the step (3) as a consumable electrode, slowly descending the consumable electrode and inserting the consumable electrode into an electroslag furnace, wherein the insertion depth is 100-160mm, regulating remelting voltage and remelting current after electrifying and arcing, and forming a remelting electroslag ingot under the forced cooling of a water-cooled crystallizer; the remelting voltage is 45-48V, the remelting current is 4500-; the water flow of the water-cooled crystallizer is 1-1.2m3/min, so as to ensure that the cooling speed reaches 20-40 ℃/s, promote the solidification of the electroslag ingot and reduce the segregation of the electroslag ingot; the slag system used is 57-60% of CaF2, 15-20% of Al2O3, 13-18% of CaO, 13-14% of MgO and inevitable impurities;
in order to further improve the performance of the bar after heat treatment, heat treatment is carried out after the step (5), specifically, heating is carried out at a heating rate of 50-60 ℃/min to 1150-1180 ℃ for 3-5 h, and then oil quenching is carried out; then slowly raising the temperature to 880-900 ℃ at the speed of 20-30 ℃/min, and treating for 15-20 h.
Placing the product after the heat treatment at 900 ℃ and 200MPa, wherein the lasting life is more than or equal to 340 h; at 750 ℃, the yield strength is more than or equal to 1110MPa, the tensile strength is more than or equal to 1220MPa, and the elongation is more than or equal to 19 percent.
Comparative example 5
In overview, comparative example 5 differs from example 2 mainly in the change in rare earth type, and the other processes are consistent with example 2.
Specifically, the weight percentage is as follows: cr 18, Co 16.8, Mo 7.5, W4.5, Ta3.5, Al 3.5, Ti 2.2, Fe 2, V: 0.65, Mn 0.25, Si0.15, C0.03, Zr 0.02, B0.0015, La 0.005, Hf0.10, the balance consisting of Ni and unavoidable impurities;
in order to further improve the performance of the bar after heat treatment, heat treatment is carried out after the step (5), specifically, heating is carried out at a heating rate of 50-60 ℃/min to 1150-1180 ℃ for 3-5 h, and then oil quenching is carried out; then slowly raising the temperature to 880-900 ℃ at the speed of 20-30 ℃/min, and treating for 15-20 h.
Placing the product after the heat treatment at 900 ℃ and 200MPa, wherein the lasting life is more than or equal to 350 h; at 750 ℃, the yield strength is more than or equal to 1260MPa, the tensile strength is more than or equal to 1360MPa, and the elongation is more than or equal to 24.5 percent.
Comparative example 6
In summary, the main difference between comparative example 6 and example 2 is the change in rare earth content, the process is generally consistent with example 2, and the type of raw material is adjusted mainly according to the change of composition.
Specifically, the weight percentage is as follows: cr 18, Co 16.8, Mo 7.5, W4.5, Ta3.5, Al 3.5, Ti 2.2, Fe 2, V: 0.65, Mn 0.25, Si0.15, C0.03, Zr 0.02, B0.0015, Sc 0.001, Hf0.10, and the balance Ni and unavoidable impurities;
in order to further improve the performance of the bar after heat treatment, heat treatment is carried out after the step (5), specifically, heating is carried out at a heating rate of 50-60 ℃/min to 1150-1180 ℃ for 3-5 h, and then oil quenching is carried out; then slowly raising the temperature to 880-900 ℃ at the speed of 20-30 ℃/min, and treating for 15-20 h.
Placing the product after the heat treatment at 900 ℃ and 200MPa, wherein the lasting life is more than or equal to 350 h; at 750 ℃, the yield strength is more than or equal to 1140MPa, the tensile strength is more than or equal to 1300MPa, and the elongation is more than or equal to 21 percent.
Comparative example 7
In general, comparative example 1 is mainly different from example 2 in the change in rare earth content, and the process is identical to example 2.
Specifically, the weight percentage is as follows: cr 18, Co 16.8, Mo 7.5, W4.5, Ta3.5, Al 3.5, Ti 2.2, Fe 2, V: 0.65, 0.25 of Mn, 0.15 of Si, 0.03 of C, 0.02 of Zr, 0.0015 of B, 0.1 of Sc and 0.10 of Hf, and the balance of Ni and inevitable impurities;
in order to further improve the performance of the bar after heat treatment, heat treatment is carried out after the step (5), specifically, heating is carried out at a heating rate of 50-60 ℃/min to 1150-1180 ℃ for 3-5 h, and then oil quenching is carried out; then slowly raising the temperature to 880-900 ℃ at the speed of 20-30 ℃/min, and treating for 15-20 h.
Placing the product after the heat treatment at 900 ℃ and 200MPa, wherein the lasting life is more than or equal to 370 h; at 750 ℃, the yield strength is more than or equal to 1190MPa, the tensile strength is more than or equal to 1350MPa, and the elongation is more than or equal to 27 percent.
Comparative example 8
In general, comparative example 1 differs from example 3 mainly in the change in the production process (4).
Specifically, the preparation step (4) is as follows: electroslag remelting: taking the electrode bar obtained in the step (3) as a consumable electrode, slowly descending the consumable electrode and inserting the consumable electrode into an electroslag furnace, wherein the insertion depth is less than 100mm, regulating remelting voltage and remelting current after electrifying and arcing, and forming a remelting electroslag ingot under the forced cooling of a water-cooled crystallizer; the remelting voltage is 25-28V, the remelting current is 4500-; the water flow of the water-cooled crystallizer is 0.8-1.0m3/min, so as to ensure that the cooling speed reaches less than 20 ℃/s, promote the solidification of the electroslag ingot and reduce the segregation of the electroslag ingot; the used slag system is 57-60% of CaF2, 15-20% of Al2O3, 13-18% of CaO, 3-4% of MgO, 10-12% of TiO2 and inevitable impurities;
in order to further improve the performance of the bar after heat treatment, heat treatment is carried out after the step (5), specifically, heating is carried out at a heating rate of 50-60 ℃/min to 1150-1180 ℃ for 3-5 h, and then oil quenching is carried out; then slowly raising the temperature to 880-900 ℃ at the speed of 20-30 ℃/min, and treating for 15-20 h.
Placing the product after the heat treatment at 900 ℃ and 200MPa, wherein the lasting life is more than or equal to 340 h; at 750 ℃, the yield strength is more than or equal to 1190MPa, the tensile strength is more than or equal to 1390MPa, and the elongation is more than or equal to 25.5 percent.
Comparative example 9
In general, comparative example 1 differs from example 3 mainly in the change in the production process (4).
Specifically, the preparation step (4) is as follows: electroslag remelting: taking the electrode bar obtained in the step (3) as a consumable electrode, slowly descending the consumable electrode and inserting the consumable electrode into an electroslag furnace, wherein the insertion depth is less than 100mm, regulating remelting voltage and remelting current after electrifying and arcing, and forming a remelting electroslag ingot under the forced cooling of a water-cooled crystallizer; the remelting voltage is 45-48V, the remelting current is 6500-7000A, and the average melting rate is 10-11 kg/min; the water flow of the water-cooled crystallizer is 1-1.2m3/min, so as to ensure that the cooling speed reaches 20-40 ℃/s, promote the solidification of the electroslag ingot and reduce the segregation of the electroslag ingot; the used slag system is 57-60% of CaF2, 15-20% of Al2O3, 13-18% of CaO, 3-4% of MgO, 10-12% of TiO2 and inevitable impurities;
in order to further improve the performance of the bar after heat treatment, heat treatment is carried out after the step (5), specifically, heating is carried out at a heating rate of 50-60 ℃/min to 1150-1180 ℃ for 3-5 h, and then oil quenching is carried out; then slowly raising the temperature to 880-900 ℃ at the speed of 20-30 ℃/min, and treating for 15-20 h.
Placing the product after the heat treatment at 900 ℃ and 200MPa, wherein the lasting life is more than or equal to 370 h; at 750 ℃, the yield strength is more than or equal to 1170MPa, the tensile strength is more than or equal to 1400MPa, and the elongation is more than or equal to 24.5 percent.
The above description is only an embodiment of the present invention, but the scope of the present invention is not limited thereto, and any changes or substitutions that can be easily conceived by those skilled in the art within the technical scope of the present invention are included in the scope of the present invention. Therefore, the protection scope of the present invention shall be subject to the protection scope of the claims.
Claims (6)
1. An electroslag remelting process for nickel-based superalloy, which comprises the following preparation steps:
the nickel-based high-temperature alloy comprises, by mass, 15-20 parts of Cr, 15-20 parts of Co, 5-10 parts of Mo, 2-6 parts of W, 1-4 parts of Ta, 1-4 parts of Al and 2.2-2.5 parts of Ti, wherein at least 2 of the four main materials of Fe, V, Nb and rare earth are selectively added, the total content of the selectively added materials is 1-5, and the balance of Ni and inevitable impurities form a preparation raw material; CaF adopted in electroslag remelting process2、Al2O3、CaO、MgO、TiO2The remelting voltage of the slag system is 45-48V, the remelting current is 4500-5000A, and the average melting rate is 6-8 kg/min.
2. An electroslag remelting process for nickel-based superalloy, which comprises the following preparation steps:
(1) determining a target product: the nickel-based high-temperature alloy comprises the following components in percentage by mass: cr 17.5-18, Co 16.8-17.5, Mo7.2-7.5, W4.5-5, Ta 3.2-3.5, Al 3.5-3.8, Ti 2.2-2.5, Fe 2-3, V: 0.55-0.65 wt%, Mn 0.15-0.25 wt%, Si 0.1-0.15 wt%, C0.01-0.03 wt%, Zr 0.01-0.02 wt%, B0.0015-0.003 wt%, Sc 0.005-0.05 wt%, Hf0.10-0.20 wt%, and Ni and inevitable impurities for the rest;
(2) smelting in a vacuum induction furnace: proportioning according to the chemical composition proportion of a target product and combining the burning loss amount, and adding the mixture into a vacuum induction smelting furnace for smelting; selecting Ni-Co intermediate alloy, Ni-Cr intermediate alloy, Ni-Mo intermediate alloy and Fe-Mo intermediate alloy, selecting proper intermediate alloy from W, Ta, V and/or Nb, Zr and Hf, and selecting low-melting-point intermediate alloy or simple substance from Ti, Al, Mn, Si, C, B and rare earth; loading into a crucible, adding a covering agent at the upper part when the raw materials are completely melted, wherein the covering agent consists of 35-45% of fluorite and 55-65% of lime by mass, the adding amount of the covering agent accounts for 2-5% of the total mass of the alloy in the crucible, refining for 20-40min after complete melting, the adding amount of the refining agent accounts for 2.5-3.5% of the total mass of the alloy in the crucible in the refining process, the refining agent is an alloy containing barium, aluminum and calcium, adding a desulfurizing agent at the later stage of refining, and stirring after refining; slagging off, namely preparing for casting when the temperature of the nickel-based high-temperature alloy liquid melt reaches 1500-1700 ℃;
(3) remelting preparation: preheating the mould to 200 ℃, keeping the temperature for 30min, and casting to obtain an electrode rod with the diameter of 350 mm;
(4) electroslag remelting: taking the electrode bar obtained in the step (3) as a consumable electrode, slowly descending the consumable electrode and inserting the consumable electrode into an electroslag furnace, wherein the insertion depth is 100-160mm, regulating remelting voltage and remelting current after electrifying and arcing, and forming a remelting electroslag ingot under the forced cooling of a water-cooled crystallizer; the remelting voltage is 45-48V, the remelting current is 4500-; the water flow of the water-cooled crystallizer is 1-1.2m3/min, so as to ensure that the cooling speed reaches 20-40 ℃/s, promote the solidification of the electroslag ingot and reduce the segregation of the electroslag ingot; the used slag system is 57-60% of CaF2, 15-20% of Al2O3, 13-18% of CaO, 3-4% of MgO, 10-12% of TiO2 and inevitable impurities;
(5) forging: heating the electroslag ingot to 1100-1150 ℃, preserving heat for 2-3 hours, forging into a bar, air cooling the forged bar to room temperature, and performing surface polishing treatment on the obtained bar to obtain a finished alloy material.
3. A process for electroslag remelting of a nickel base superalloy according to claim 1 or 2, wherein: the covering agent consists of fluorite and lime with the mass ratio of 40 percent and 60 percent, the adding amount of the covering agent accounts for 4 percent of the total mass of the alloy in the crucible, the covering agent is refined for 30min after being completely melted, the adding amount of the refining agent accounts for 3 percent of the total mass of the alloy in the crucible in the refining process, the refining agent is the alloy containing barium, aluminum and calcium, a desulfurizing agent is added in the later period of refining, and the mixture is stirred after the refining is finished; and (4) slagging off, namely preparing for casting when the temperature of the nickel-based high-temperature alloy liquid melt reaches 1500-1600 ℃.
4. The electroslag remelting process for a nickel-base superalloy according to claim 1 or 2, wherein the nickel-base superalloy comprises, in mass percent: cr 17.5, Co 17.5, Mo7.2, W5, Ta 3.2, Al 3.8, Ti 2.5, Fe 3, V: 0.55, Mn 0.15, Si0.1, C0.01, Zr0.01, B0.003, Sc 0.05, Hf 0.20, and the balance Ni and unavoidable impurities.
5. The electroslag remelting process for a nickel-base superalloy according to claim 1 or 2, wherein the nickel-base superalloy comprises, in mass percent: cr 18, Co 16.8, Mo 7.5, W4.5, Ta3.5, Al 3.5, Ti 2.2, Fe 2, V: 0.65, Mn 0.25, Si0.15, C0.03, Zr 0.02, B0.0015, Sc 0.005, Hf0.10, and the balance Ni and unavoidable impurities.
6. Electroslag of nickel-base superalloy according to claim 1 or 2, wherein the nickel-base superalloy comprises, in mass percent: cr 17.5, Co 17, Mo 7.4, W4.75, Ta 3.3, Al 3.7, Ti 2.4, Fe 2.5, V: 0.6, Mn0.2, Si0.12, C0.02, Zr 0.015, B0.002, Sc 0.03, Hf 0.15, and the balance Ni and unavoidable impurities.
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| CN111575536A (en) * | 2020-05-28 | 2020-08-25 | 江苏隆达超合金航材有限公司 | Nickel-based high-temperature alloy with high W, Mo content and preparation method thereof |
| CN111778439A (en) * | 2020-07-13 | 2020-10-16 | 江苏隆达超合金航材有限公司 | GH2018 alloy electroslag ingot and preparation method thereof |
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Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP2778241A1 (en) * | 2011-12-15 | 2014-09-17 | National Institute for Materials Science | Heat-resistant nickel-based superalloy |
| CN108315599A (en) * | 2018-05-14 | 2018-07-24 | 钢铁研究总院 | A kind of high cobalt nickel base superalloy and preparation method thereof |
| CN108384992A (en) * | 2018-04-20 | 2018-08-10 | 温州市赢创新材料技术有限公司 | A kind of high-strength corrosion-resisting nickel base superalloy and its manufacturing method |
| CN108441705A (en) * | 2018-03-16 | 2018-08-24 | 中国航发北京航空材料研究院 | A kind of high intensity ni-base wrought superalloy and preparation method thereof |
| CN108441707A (en) * | 2018-03-30 | 2018-08-24 | 四川六合锻造股份有限公司 | A kind of high intensity tungstenic system nickel-base high-temperature alloy material and its preparation method and application |
| CN108441741A (en) * | 2018-04-11 | 2018-08-24 | 张文久 | A kind of aerospace high-strength corrosion-resisting nickel base superalloy and its manufacturing method |
| CN109128102A (en) * | 2018-07-19 | 2019-01-04 | 钢铁研究总院 | A kind of high strength and high flexibility nickel base superalloy band and preparation method thereof |
-
2019
- 2019-04-16 CN CN201910303311.8A patent/CN110724826A/en active Pending
Patent Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP2778241A1 (en) * | 2011-12-15 | 2014-09-17 | National Institute for Materials Science | Heat-resistant nickel-based superalloy |
| CN108441705A (en) * | 2018-03-16 | 2018-08-24 | 中国航发北京航空材料研究院 | A kind of high intensity ni-base wrought superalloy and preparation method thereof |
| CN108441707A (en) * | 2018-03-30 | 2018-08-24 | 四川六合锻造股份有限公司 | A kind of high intensity tungstenic system nickel-base high-temperature alloy material and its preparation method and application |
| CN108441741A (en) * | 2018-04-11 | 2018-08-24 | 张文久 | A kind of aerospace high-strength corrosion-resisting nickel base superalloy and its manufacturing method |
| CN108384992A (en) * | 2018-04-20 | 2018-08-10 | 温州市赢创新材料技术有限公司 | A kind of high-strength corrosion-resisting nickel base superalloy and its manufacturing method |
| CN108315599A (en) * | 2018-05-14 | 2018-07-24 | 钢铁研究总院 | A kind of high cobalt nickel base superalloy and preparation method thereof |
| CN109128102A (en) * | 2018-07-19 | 2019-01-04 | 钢铁研究总院 | A kind of high strength and high flexibility nickel base superalloy band and preparation method thereof |
Non-Patent Citations (1)
| Title |
|---|
| 郭爱莲: "《铸造工基本技术》", 31 October 1997 * |
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