CN115323219A - High-temperature oxidation-resistant high-strength nickel-based alloy and preparation method thereof - Google Patents
High-temperature oxidation-resistant high-strength nickel-based alloy and preparation method thereof Download PDFInfo
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Abstract
The invention discloses a high-temperature oxidation-resistant high-strength nickel-based alloy and a preparation method thereof, belonging to the technical field of high-temperature alloys and being mainly characterized in that the alloy comprises the following chemical components in percentage by weight: 0.03 to 0.05 percent, cr:15.5 to 16.5 percent, fe:3.1 to 4.0%, al:4.1 to 4.7%, mn:0.10 to 0.25%, Y:0.002 to 0.010%, zr:0.01 to 0.03%, B:0.001 to 0.005 percent, and the balance of Ni and inevitable impurities, so that the content of oxide inclusions in the high-temperature alloy is reduced, and meanwhile, the high-temperature alloy obtained by the method has excellent high-temperature durability and cold and hot processability, and can still keep the effect of a complete and compact surface oxide film under the condition of the temperature of up to 1100 ℃.
Description
Technical Field
The invention relates to the field of high-temperature alloys, in particular to a high-temperature oxidation-resistant high-strength nickel-based alloy and a preparation method thereof.
Background
In order to improve the thrust of an aeroengine, a honeycomb sealing structure is required to be designed on the inner wall of a casing at the matching part of a rotor and a stator of a worm gear part of the aeroengine, the honeycomb structure is made of foil with the thickness of only dozens of microns and is equivalent to the size of four-stage crystal grains of a common strip-shaped high-temperature alloy, and the strip-shaped high-temperature alloy with the honeycomb structure is the basis for preparing the honeycomb structure on the inner wall of the casing of the engine. Considering the use condition of an aeroengine, the strip-shaped high-temperature alloy with the honeycomb structure is required to still maintain excellent oxidation resistance at a higher temperature (1000-1100 ℃), and the strength of the high-temperature alloy is required to be considered. The existing strip-shaped high-temperature alloy with a honeycomb structure adopts high A1 content (the highest Al content is 8%) and rare earth Y element as an auxiliary material to improve the oxidation resistance and the strength of the high-temperature alloy, but in the actual application process, when the Al content in the alloy is higher, the forming tendency of oxide inclusion of the alloy is extremely strong, the hardness of the oxide inclusion containing Al is very high, once the inclusion exists, micro longitudinal cracks are formed in the rolling process of the final high-temperature alloy foil, and thus the surface quality, the processing plasticity and the mechanical property of the product are influenced.
Disclosure of Invention
Aiming at the problem that the high-temperature alloy for the strip-shaped honeycomb has a strong forming tendency of oxide inclusions caused by the fact that the oxidation resistance of the high-temperature alloy is improved by adopting a high A1 content in the high-temperature alloy in the prior art, the invention provides the high-temperature oxidation-resistant high-strength nickel-based alloy and the preparation method thereof, the content of the oxide inclusions in the high-temperature alloy can be reduced, and meanwhile, the high-temperature alloy obtained by the method has excellent high-temperature durability and cold and hot processability, and can still keep a complete and compact surface oxidation film under the condition of the temperature of 1100 ℃.
The invention aims to provide a high-temperature oxidation-resistant high-strength nickel-based alloy, which adopts the following technical scheme:
the high-temperature oxidation-resistant high-strength nickel-based alloy comprises the following chemical components in percentage by weight: 0.03 to 0.05%, cr:15.5 to 16.5%, fe:3.1 to 4.0%, al:4.1 to 4.7%, mn:0.10 to 0.25%, Y:0.002 to 0.010%, zr:0.01 to 0.03%, B:0.001 to 0.005, and the balance of Ni and unavoidable impurities.
Preferably, the chemical components of the alloy are, by weight percent, C:0.03 to 0.05%, cr:15.5 to 16.5%, fe:3.1 to 4.0%, al:4.2 to 4.6%, mn:0.10 to 0.25%, Y:0.002 to 0.006%, zr:0.01 to 0.03%, B:0.001 to 0.005, and the balance of Ni and unavoidable impurities.
Further preferably, the chemical components of the alloy are, by weight percent, C:0.037 to 0.05%, cr:16.2 to 16.5%, fe:3.55 to 4.0%, al:4.2 to 4.66%, mn:0.15 to 0.25%, Y:0.002 to 0.006%, zr:0.01 to 0.03%, B:0.003 to 0.005, and the balance of Ni and unavoidable impurities.
By adopting the technical scheme, the influence of the contents of C, al, zr, B, Y and Mn on the alloy performance is relatively large by adjusting the contents of C, al, zr, B, Y and Mn. Mainly, the content of C directly determines the amount of carbide in the alloy, and the amount, size and distribution of the carbide have important influence on dynamic recrystallization in the thermal deformation process of the alloy and static recrystallization in the subsequent annealing process due to the pinning effect of the carbide on grain boundaries, when the content of the carbon is too low, the pinning of the grain boundaries is insufficient, the alloy is mainly softened by dynamic reversion and is not beneficial to recrystallization nucleation, so that the full progress of the dynamic recrystallization is influenced, and excessive carbide is easy to form strip-shaped distribution in the unidirectional cold deformation process, so that the processing and service performance (tensile property and durability) of the alloy is influenced. Therefore, when the content of C is controlled within the range of 0.03-0.05%, the mechanical property of the alloy is effectively ensured.
The three elements of Al, cr and Y are used in a matched manner, the oxidation weight increase (oxide film thickening) per unit area is increased along with the increase of the content of the Al element, and the oxidation resistance of the alloy is generally characterized by adopting the average oxidation weight increase per unit area within 100h at a certain temperature, so when the content of Al is increased, the oxidation resistance of the alloy is enhanced, the outward diffusion of the Cr element can be more effectively hindered after the oxide film is thickened, the thickness of the oxide film of Cr is reduced on the contrary, the volatilization of the Cr element is inhibited, the high-temperature mechanical property of the alloy is ensured, meanwhile, the inward diffusion of oxygen ions can be accelerated along with the increase of the content of the Y element, the oxide film is bent inwards, the bonding strength of the bent oxide film and a base body is higher, and the adhesion of the oxide film is improved.
And with the increase of the content of Al element, the precipitation amount and the precipitation speed of a second phase (gamma ' phase) are remarkably improved, the precipitation of the second phase is beneficial to improving the high-temperature performance of the alloy, after the mass fraction of the gamma ' phase is increased, the redissolution temperature of the gamma ' phase is increased (the redissolution temperature refers to the temperature at which the gamma ' phase is redissolved in a matrix), especially when the content of Al is higher than 5%, the gamma ' phase is precipitated in a large amount at the temperature of 950 ℃, so that the hot-working performance of the alloy is seriously reduced, the heat deformation amount of forging cogging is also reduced, the forging frequency is also increased, the processing cost is increased, meanwhile, the second phase is easy to crack when the strain rate is relatively high when the corner or local temperature is relatively low, and is easy to crack when the temperature is reduced in the later stage of hot rolling is relatively high, so that when the content of Al is controlled within the range of 4.1-4.7%, the precipitation of the second phase can be avoided in the temperature increasing and decreasing processes of homogenization, the intermediate annealing, the strain aging crack is avoided, and the final forging temperature can be reduced to 920 ℃, and the later stage of the final forging is convenient to process.
The addition of Zr, B and Mn elements is beneficial to improving the plasticity of the alloy, but when the addition amount of Zr, B and Mn elements exceeds the limit, the plasticity of the alloy is reduced, and the endurance life is also reduced.
The invention also aims to provide a preparation method of the high-temperature oxidation-resistant high-strength nickel-based alloy, which comprises the following steps:
(1) Adding graphite, metal chromium, ferroboron, metal manganese and nickel plate raw materials into a vacuum induction furnace according to weight percentage for vacuum refining, sequentially adding metal aluminum, metal zirconium and metal yttrium after refining, uniformly stirring, and then casting to form a consumable electrode rod;
(2) Carrying out electroslag remelting on the consumable electrode bar obtained in the step (1) to obtain an ingot;
(3) Carrying out homogenization heat treatment on the ingot obtained in the step (2);
(4) Preparing a forging stock: and (4) forging and cogging the cast ingot treated in the step (3) to prepare a forged blank.
Preferably, the refining temperature in the step (1) is 1480-1490 ℃, and the refining time is 20-25min.
Preferably, the electroslag used in the electroslag remelting in the step (2) comprises CaF in percentage by weight 2 :50-65％、CaO:15-25％、Al 2 O 3 :10-25％。
Preferably, the smelting speed of electroslag remelting in the step (2) is 0.4-2kg/min, the smelting current is 3000-4500A, and the lateral current is 100-450A.
Preferably, the ingot drawing speed in the step (2) is 4-6mm/min, and the cooling water amount is as follows: 3-5 grade; wherein the first water flow is 8-10L/min.
Preferably, the temperature of the homogenization heat treatment in the step (3) is 1140-1180 ℃, and the time of the homogenization heat treatment is 20-40h.
Preferably, the forging temperature in the step (4) is 1000-1200 ℃, and the deformation per fire is 30-70%.
By adopting the technical scheme, the smelting speed of electroslag remelting is limited to 0.4-2kg/min, the smelting current is limited to 3000-4500A, and when the lateral current is 100-450A, the casting structure and the annealing structure of a forged product are ensured, and the segregation condition of primary carbides is reduced.
The method effectively controls the temperature and refining time of the refining stage, the ingot drawing speed and the cooling water amount, and further can effectively control the content of harmful elements O and S of the alloy in the refining and electroslag remelting stages, so that raw materials capable of forming oxide inclusions are effectively reduced from the source, the series of the coarse series and the fine series of the A-type (sulfide inclusions), the B-type (alumina inclusions) and the C-type (silicate inclusions) in the alloy obtained by the preparation method is 0 grade, the series of the DS-type (round spherical inclusions) is 0 grade, the fine series of the D-type (spherical oxide inclusions) is 0.5 grade, the coarse series is 0 grade, and the alloy can be effectively rolled into a foil.
The forging of the application is carried out within the range of 1200 ℃ to 1000 ℃, when the deformation amount of each heating is limited within the range of 30-70%, the average grain size of the forged blank prepared by forging is 3-6 grade, the forging efficiency of each heating can also be effectively ensured, especially when the deformation amount of each heating of forging is within the range of 40-50%, the heating of deformation can be effectively reduced, the production efficiency is improved, the average grain size of the prepared forged blank is higher (the average grain size reaches 4-5 grade), when the deformation amount of each heating is lower than 30%, the recrystallization energy of the alloy is insufficient, so that the plasticity of the final alloy product is insufficient, and when the deformation amount of each heating is higher than 70%, the plasticity and the strength of the alloy are also reduced, therefore, as long as the forging deformation amount of each heating of the alloy is between 30-70%, the integrity, the mechanical property and the plasticity of the forged blank can be effectively ensured.
In conclusion, the invention has the following beneficial effects:
this application is through adjusting C, al, zr, B, Y, the content scope of Mn element, not only can guarantee the mechanical properties of alloy, can also guarantee permanence property and the antioxidant property of alloy under high temperature simultaneously, this application is at the reasonable refining temperature of control in the preparation process, the technological parameter in refining time and electroslag smelting stage simultaneously, effectively reduce the harmful element in the alloy, make the oxidation inclusion control in the final product at very low level, it provides effectual guarantee to roll into the foil for follow-up alloy.
Drawings
FIG. 1 is an electron microscope image showing the change of the morphology of the oxide film section with the Al element content in the alloy.
FIG. 2 is an electron microscope image of the morphology of the oxide film section as a function of the content of Y element in the alloy.
FIG. 3 shows the structure of different C content alloys after hot forging with the same deformation.
FIG. 4 shows the structure of different C content alloys after hot forging and annealing with the same deformation.
Detailed Description
The present invention will be described in further detail with reference to the accompanying drawings.
Examples 1-5 were prepared using the same process, the resulting superalloys having the compositions shown in table 1, the process was as follows:
examples 1 to 5
A preparation method of a high-temperature oxidation-resistant high-strength nickel-based alloy comprises the following steps:
(1) Vacuum induction smelting, namely adding graphite, chromium metal, ferroboron, manganese metal and a nickel plate into a vacuum induction furnace to be smelted according to the requirements of alloy components, controlling the vacuum degree to be 5Pa, controlling the refining temperature to be 1480 ℃ after smelting, refining for 20min, sequentially adding aluminum metal, zirconium metal and yttrium metal into the vacuum induction furnace after refining is finished, stirring uniformly, and casting into a consumable electrode rod with the diameter being 0.6 times of that of an electroslag ingot crystallizer; the oxygen content in the alloy is 0.0007 after 20min of refining;
(2) Electroslag remelting, namely adding the consumable electrode rod obtained in the step (1) into an electroslag ingot crystallizer, then adding electroslag for smelting, wherein the smelting speed is 0.4kg/min, the smelting current is 3000A, the lateral current is 100A, the thickness of the electroslag after the electroslag is melted is 0.4 times of the diameter of the electroslag ingot crystallizer, after the consumable electrode rod is melted, cooling and solidifying are carried out to obtain an electroslag remelting ingot, the ingot drawing speed is 6mm/min, and the cooling water amount is 3 grades; wherein the diameter of the electroslag ingot crystallizer is 150mm, and the used electroslag comprises the following components in percentage by weight: caF 2 :50％、CaO:25％、Al 2 O 3 25 percent of; meanwhile, the influence of the pumping speed and the cooling water quantity on the O and S contents in the alloy is also detected, and the specific test result is shown in the following table
(3) Carrying out homogenization heat treatment on the ingot obtained in the step (2), and treating for 20h at the homogenization heat treatment temperature of 1145 +/-5 ℃;
(4) And (3) preparing a forging blank, namely forging and cogging the ingot obtained in the step (3) at 1200 ℃, stopping forging when the temperature is lower than 1000 ℃ in the forging process, and preparing the forging blank, wherein the forging deformation per heat exceeds 30%.
Example 6
The difference from example 3 is that the content of Al element in example 6 is 4.36%, and the contents of the other components are the same as those in example 3.
Example 7
The difference from example 3 is that the content of Al element in example 7 is 4.66%, and the contents of the remaining components are the same as those in example 3.
Example 8
The difference from example 3 is that the content of element Y in example 8 is 0.008% and the contents of the remaining components are the same as those in example 3.
Table 1 shows the contents of elements in the alloys obtained in examples 1 to 8 in terms of% by weight
| Composition (I) | Example 1 | Example 2 | Example 3 | Example 4 | Example 5 | Example 6 | Example 7 | Example 8 |
| C | 0.03 | 0.03 | 0.037 | 0.05 | 0.05 | 0.037 | 0.037 | 0.037 |
| Cr | 15.5 | 15.5 | 16.2 | 16.5 | 16.5 | 16.2 | 16.2 | 16.2 |
| Fe | 3.1 | 3.1 | 3.55 | 4.0 | 4.0 | 3.55 | 3.55 | 3.55 |
| Al | 4.1 | 4.2 | 4.4 | 4.6 | 4.7 | 4.36 | 4.66 | 4.4 |
| Mn | 0.10 | 0.10 | 0.15 | 0.25 | 0.25 | 0.15 | 0.15 | 0.15 |
| Y | 0.002 | 0.002 | 0.004 | 0.006 | 0.01 | 0.004 | 0.004 | 0.008 |
| Zr | 0.01 | 0.01 | 0.02 | 0.03 | 0.03 | 0.02 | 0.02 | 0.02 |
| B | 0.001 | 0.001 | 0.003 | 0.005 | 0.005 | 0.003 | 0.003 | 0.003 |
| Ni | Balance of | Balance of | Balance of | Balance of | Balance of | Balance of | Allowance of | Allowance of |
Example 9
The difference from example 3 is that the refining temperature in step (1) was 1490 ℃, the other conditions and steps were the same as in example 3, and the content of oxygen element in the alloy after refining was 0.0008.
Example 10
The difference from example 3 is that the refining time in step (1) was 25min, the other conditions and steps were the same as in example 3, and the content of oxygen element in the alloy after refining was 0.0007.
Example 11
The difference from example 3 is that the homogenization heat treatment temperature in step (2) is 1175 + -5 deg.C and the homogenization heat treatment time is 40h, and the rest of the conditions and steps are the same as those in example 3.
Example 12
The difference from the example 3 is that the smelting speed of the electroslag remelting in the step (2) is 1kg/min, the smelting current is 4000A, the lateral current is 300A, and the used electroslag comprises the following components in percentage by weight: caF 2 :65％、CaO:15％、Al 2 O 3 :20％。
Example 13
The difference from example 3 is that in step (2)The smelting speed of electroslag remelting is 2kg/min, the smelting current is 4500A, the lateral current is 450A, and the used electroslag comprises the following components in percentage by weight: caF 2 :65％、CaO:25％、Al 2 O 3 10% and the remaining conditions and steps are the same as those in example 3.
Example 14
The difference from example 3 is that the ingot pulling speed in step (2) was 4mm/min, and the other conditions and steps were the same as those in example 3.
Example 15
The difference from example 3 is that the ingot pulling speed in step (2) was 5mm/min, and the other conditions and steps were the same as those in example 3.
Example 16
The difference from example 3 is that the amount of water in step (2) is 4 steps, and the rest of the conditions and steps are the same as those in example 3.
Example 17
The difference from example 3 is that the amount of water in step (2) is 5 stages, and the remaining conditions and steps are the same as those in example 3.
Effect of ingot withdrawal speed and Water amount on O and S content in examples 14-17
Comparative example 1
The difference from example 3 is that the content of the element A1 is 3.96%, and the remaining element contents are the same as example 3.
Comparative example 2
The difference from example 3 is that the content of the element A1 is 5.19%, and the contents of the remaining elements are shown in Table 2.
Comparative example 3
The difference from example 3 is that the content of C element is 0.021%, and the contents of the other elements are shown in Table 2.
Comparative example 4
The difference from example 3 is that the content of C element is 0.055%, and the contents of the remaining elements are shown in table 2.
Comparative example 5
The difference from example 3 is that the content of C element is 0.1%, and the contents of the remaining elements are shown in Table 2.
Comparative example 6
The difference from example 3 is that the content of the Y element is 0.02%, and the contents of the remaining elements are shown in Table 2.
Comparative example 7
The difference from example 3 was that the content of Zr element was 0%, and the contents of the remaining elements are shown in Table 2.
Comparative example 8
The difference from example 3 is that the content of Zr element is 0.06%, and the contents of the other elements are shown in Table 2.
Comparative example 9
The difference from example 3 is that the content of B element is 0% and the contents of the other elements are shown in Table 2.
Comparative example 10
The difference from example 3 is that the content of Mn element is 0%, and the contents of the remaining elements are shown in Table 2.
TABLE 2 elemental contents of the alloys obtained in comparative examples 1 to 10 in% by weight
| Composition (I) | Example 3 | Comparative example 1 | Comparative example 2 | Comparative example 3 | Comparison ofExample 4 | Comparative example 5 |
| C | 0.036 | 0.036 | 0.036 | 0.021 | 0.055 | 0.1 |
| Cr | 16.2 | 16.2 | 16.2 | 16.2 | 16.2 | 16.2 |
| Fe | 3.55 | 3.55 | 3.55 | 3.55 | 3.55 | 3.55 |
| Al | 4.4 | 3.96 | 5.19 | 4.4 | 4.4 | 4.4 |
| Mn | 0.15 | 0.15 | 0.15 | 0.15 | 0.15 | 0.15 |
| Y | 0.004 | 0.004 | 0.004 | 0.004 | 0.004 | 0.004 |
| Zr | 0.02 | 0.02 | 0.02 | 0.02 | 0.02 | 0.02 |
| B | 0.003 | 0.003 | 0.003 | 0.003 | 0.003 | 0.003 |
| Ni | Allowance of | Balance of | Allowance of | Allowance of | Allowance of | Balance of |
TABLE 2
Note: the balance in the above examples and preparation examples includes Ni and inevitable impurities.
Performance detection
The oxidation resistance and mechanical property detection are carried out on the alloy obtained in the embodiment and the comparative example, wherein the oxidation resistance test is to process a sample after heat treatment into small pieces, test the oxidation conditions in different time periods at 1100 ℃, then test the oxidation weight gain condition by weighing, and the judgment is carried out according to GB/T13303-9 'method for measuring oxidation resistance of steel' and HB5258-2000 'method for measuring oxidation resistance of steel and high-temperature alloy', the weight gain method is adopted in the application for testing, and the thickness of the oxidation film is tested by observing the section morphology of the oxidation film.
The detection of the mechanical property is that a sample after heat treatment is processed into a round bar, then mechanical property test tests such as room temperature stretching, high temperature stretching at 1100 ℃ and endurance life under the condition of 980 ℃/22MPa are respectively carried out, and the detection is carried out according to GB/T228.1-2010 part I of a metal material tensile test: room temperature test method and GB/T228.2-2015 "first part of tensile test of Metal materials: and (4) detecting a high-temperature test method and GB/T2039-2012 'a metal material uniaxial tensile creep test method'.
TABLE 3 alloy room temperature mechanical property test result table
TABLE 4 mechanical property test result table of the alloy of the present application at 1100 deg.C
TABLE 5 high temperature durability test results table for each alloy at 980 deg.C/22 MPa
Since the contents of C, fe, mn, zr and B do not greatly affect the oxidation resistance of the alloy, the oxidation resistance of the alloys obtained in examples 1-8 and comparative examples 1-2 is further illustrated by the present application, and the results of the oxidation resistance test are shown in Table 6.
TABLE 6 table of the test results of the alloy oxidized at 1100 deg.C for 100h
(1) Analysis of the influence of Al and Y elements on the alloy properties:
as can be seen from Table 3, when the content of the element A1 is less than the minimum value of 4.1% defined in the present application, the tensile strength at room temperature of the alloy obtained in comparative example 1 is remarkably decreased, and when the content of the element Al is more than 4.7%, the elongation after fracture and the reduction of area in comparative example 2 are both decreased as compared with example 3, indicating that when the content of the element Al exceeds 4.7%, the room temperature plasticity of the alloy is remarkably decreased, and the cold workability of the alloy is adversely affected.
As can be seen from tables 4-5, the Al element content has no obvious influence on the high-temperature tensile property of the alloy at 1100 ℃, but has a remarkable influence on the long-term service life of the high-temperature alloy, and the long-term fracture time of the high-temperature alloy is effectively increased along with the increase of the Al element content. However, when the content of the Al element exceeds 4.7%, the room temperature plasticity of the alloy in comparative example 2 (the content of the Al element is 5.19%) is sharply reduced, and when the content of the Al element is relatively low (the content of the Al element is 3.96%), the endurance performance of the alloy is relatively poor, so that when the content of the Al element in the alloy is controlled to be 4.1-4.7%, not only the high temperature endurance performance of the alloy can be effectively ensured, but also the room temperature plasticity of the alloy can be ensured.
As can be seen from table 6, as shown in fig. 1 and fig. 2, in examples 1 to 5, the oxidation weight per unit area is gradually decreased with the increase of the content of Al and Y elements, which is mainly caused by the fact that the aluminum oxide formed on the surface increases the continuous densification degree of the oxide film of the alloy, and the rare earth element improves the adhesion of the oxide film, so that the oxide film with complete surface blocks the penetration of oxygen in the air, and effectively prevents the alloy from further oxidation. In addition, the addition of the Y element accelerates the inward diffusion of oxygen ions, bends the oxide film inward, and increases the bonding strength of the oxide film to the substrate, so that the weight increase per unit area of oxidation is smaller in examples 1 to 8 of the present application than in comparative examples 1 to 2, indicating that the alloy obtained in the examples of the present application has better oxidation resistance.
As can be seen from comparison between comparative example 1 and example 3, when the content of Al element is relatively low, the formed oxide film of aluminum is not easily continuous, and the inhibition effect on oxygen element is relatively low, oxygen in the air easily penetrates into and undergoes oxidation reaction with the alloy matrix, so that the oxidation weight increase per unit area thereof continues to increase.
As can be seen from Table 3, the increase of the content of the Y element can further improve the room-temperature mechanical property of the alloy, but as can be seen from the comparative example 6 (the content of the Y element is 0.02%), when the content of the Y element is improved, the room-temperature mechanical property of the alloy is not further improved, and the plasticity is greatly reduced.
As can be seen from tables 4-5, the Y element has little influence on the high-temperature mechanical properties of the alloy, but when the content of the Y element exceeds 0.01%, the room-temperature plasticity is greatly reduced, and the high-temperature durability is also greatly reduced, which indicates that when the content of the Y element is limited within the range of 0.002-0.01%, the plasticity of the alloy can be effectively ensured, and simultaneously the antioxidant property of the alloy can be improved by matching with the Al element.
(2) Influence of element C on alloy properties: as can be seen from tables 3 and 4, as the C content increases, the room temperature strength and the high temperature strength of the alloy are both gradually improved, but the plasticity is gradually decreased, and further, as can be seen from Table 5, when the C content exceeds the highest value of 0.05% of the present application, the fracture time of the alloy of comparative examples 4 to 5 is remarkably decreased because, in combination with FIGS. 3 and 4, the C content is too low, grain boundary pinning is insufficient, the alloy is softened mainly by dynamic recovery, which is disadvantageous to recrystallization nucleation, affecting the sufficient progress of dynamic recrystallization, and after the C content reaches 0.055%, the ribbon distribution phenomenon of carbides occurs after forging processing, and the ribbon distribution of carbides is not significantly changed after annealing treatment, thereby adversely affecting the mechanical properties of the alloy, so that the C element content is controlled within the range of 0.03 to 0.05%.
(3) Analysis of the influence of the Zr, B and Mn contents on the alloy performance:
as can be seen from tables 3 to 5, when the Zr element content is 0, the mechanical properties at room temperature and the mechanical properties at high temperature of the alloy are not greatly affected, but from comparative example 7, the room temperature plasticity, the high temperature plasticity and the high temperature durability of the alloy are all reduced, and when the Zr element content is 0.06%, the room temperature mechanical properties of the alloy are increased and the high temperature durability is greatly reduced beyond the range defined in the present application, so that when the Zr element content is limited to the range of 0.01 to 0.03%, the mechanical properties, the plasticity and the high temperature durability of the alloy are favorably maintained.
When the content of B and Mn elements is 0, the room temperature plasticity, the high temperature plasticity and the high temperature durability of the alloy are all obviously reduced.
The embodiments of the present invention are preferred embodiments of the present invention, and the scope of the present invention is not limited by these embodiments, so: equivalent changes made according to the structure, shape and principle of the invention shall be covered by the protection scope of the invention.
Claims (10)
1. A high-temperature oxidation-resistant high-strength nickel-based alloy is characterized in that: the alloy comprises the following chemical components in percentage by weight: 0.03 to 0.05 percent, cr:15.5 to 16.5%, fe:3.1 to 4.0%, al:4.1 to 4.7%, mn:0.10 to 0.25%, Y:0.002 to 0.010%, zr:0.01 to 0.03%, B:0.001 to 0.005 percent, and the balance being Ni and inevitable impurities.
2. The high-temperature oxidation-resistant high-strength nickel-based alloy according to claim 1, characterized in that: the alloy comprises the following chemical components in percentage by weight: 0.03 to 0.05 percent, cr:15.5 to 16.5 percent, fe:3.1 to 4.0%, al:4.2 to 4.6%, mn:0.10 to 0.25%, Y:0.002 to 0.006%, zr:0.01 to 0.03%, B:0.001 to 0.005, and the balance being Ni and unavoidable impurities.
3. The high-temperature oxidation-resistant high-strength nickel-based alloy according to claim 1 or 2, characterized in that: the alloy comprises the following chemical components in percentage by weight: 0.037 to 0.05%, cr:16.2 to 16.5%, fe:3.55 to 4.0%, al:4.2 to 4.66%, mn:0.15 to 0.25%, Y:0.002 to 0.006%, zr:0.01 to 0.03%, B:0.003 to 0.005 and the balance of Ni and inevitable impurities.
4. A method for preparing a high temperature oxidation resistant high strength nickel base alloy according to any one of claims 1 to 3, comprising the steps of:
(1) Adding raw materials of graphite, chromium metal, ferroboron, manganese metal and nickel plate into a vacuum induction furnace according to weight percentage for vacuum refining, sequentially adding aluminum metal, zirconium metal and yttrium metal after refining, uniformly stirring, and then casting to form a consumable electrode rod;
(2) Carrying out electroslag remelting on the consumable electrode bar obtained in the step (1) to obtain an ingot;
(3) Carrying out homogenization heat treatment on the ingot obtained in the step (2);
(4) Preparing a forging stock: and (4) forging and cogging the cast ingot treated in the step (3) to prepare a forged blank.
5. The preparation method of the high-temperature oxidation-resistant high-strength nickel-based alloy according to claim 4, characterized by comprising the following steps: the refining temperature in the step (1) is 1480-1490 ℃, and the refining time is 20-25min.
6. The preparation method of the high-temperature oxidation-resistant high-strength nickel-based alloy according to claim 4, characterized by comprising the following steps: the electroslag adopted in the electroslag remelting in the step (2) comprises CaF according to weight percentage 2 :50-65%、CaO:15-25%、Al 2 O 3 :10-25%。
7. The preparation method of the high-temperature oxidation-resistant high-strength nickel-based alloy according to claim 4, characterized by comprising the following steps: the smelting speed of electroslag remelting in the step (2) is 0.4-2kg/min, the smelting current is 3000-4500A, and the lateral current is 100-450A.
8. The preparation method of the high-temperature oxidation-resistant high-strength nickel-based alloy according to claim 4, characterized by comprising the following steps: the ingot drawing speed in the step (2) is 4-6mm/min, and the cooling water amount is as follows: 3-5 gear; wherein the first water flow is 8-10L/min.
9. The preparation method of the high-temperature oxidation-resistant high-strength nickel-based alloy according to claim 4, characterized by comprising the following steps: the homogenization heat treatment temperature in the step (3) is 1140-1180 ℃, and the homogenization heat treatment time is 20-40h.
10. The preparation method of the high-temperature oxidation-resistant high-strength nickel-based alloy according to claim 4, characterized by comprising the following steps: the forging temperature in the step (4) is 1000-1200 ℃, and the deformation per firing time is 30-70%.
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|---|---|---|---|---|
| JPH04358037A (en) * | 1991-03-27 | 1992-12-11 | Sumitomo Metal Ind Ltd | Nickel-base heat resisting alloy |
| JPH11310839A (en) * | 1998-04-28 | 1999-11-09 | Hitachi Ltd | Grain-oriented solidification casting of high strength nickel-base superalloy |
| CN111621674A (en) * | 2020-06-08 | 2020-09-04 | 重庆材料研究院有限公司 | Preparation method of microalloyed high-strength precise nickel-chromium resistance alloy material |
| CN111850348A (en) * | 2020-07-30 | 2020-10-30 | 北京北冶功能材料有限公司 | High-strength high-toughness nickel-based high-temperature alloy foil and preparation method thereof |
| CN113234961A (en) * | 2021-03-05 | 2021-08-10 | 北京钢研高纳科技股份有限公司 | 1100 ℃ high-temperature-resistant antioxidant combustion chamber alloy and preparation method thereof |
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Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH04358037A (en) * | 1991-03-27 | 1992-12-11 | Sumitomo Metal Ind Ltd | Nickel-base heat resisting alloy |
| JPH11310839A (en) * | 1998-04-28 | 1999-11-09 | Hitachi Ltd | Grain-oriented solidification casting of high strength nickel-base superalloy |
| CN111621674A (en) * | 2020-06-08 | 2020-09-04 | 重庆材料研究院有限公司 | Preparation method of microalloyed high-strength precise nickel-chromium resistance alloy material |
| CN111850348A (en) * | 2020-07-30 | 2020-10-30 | 北京北冶功能材料有限公司 | High-strength high-toughness nickel-based high-temperature alloy foil and preparation method thereof |
| CN113234961A (en) * | 2021-03-05 | 2021-08-10 | 北京钢研高纳科技股份有限公司 | 1100 ℃ high-temperature-resistant antioxidant combustion chamber alloy and preparation method thereof |
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