CN114921706B - Modified nickel-base casting superalloy and preparation method thereof - Google Patents

Modified nickel-base casting superalloy and preparation method thereof Download PDF

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CN114921706B
CN114921706B CN202210442968.4A CN202210442968A CN114921706B CN 114921706 B CN114921706 B CN 114921706B CN 202210442968 A CN202210442968 A CN 202210442968A CN 114921706 B CN114921706 B CN 114921706B
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superalloy
modified
nickel
alloy
boron
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CN114921706A (en
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张军
介子奇
郭敏
刘淼楠
刘鼎元
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Northwestern Polytechnical University
Xian Technological University
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Northwestern Polytechnical University
Xian Technological University
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C30/00—Alloys containing less than 50% by weight of each constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting
    • C22C1/023—Alloys based on nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C19/00—Alloys based on nickel or cobalt
    • C22C19/03—Alloys based on nickel or cobalt based on nickel
    • C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
    • C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
    • C22C19/055—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 20% but less than 30%
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P10/00—Technologies related to metal processing
    • Y02P10/25—Process efficiency

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  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
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Abstract

The present disclosure provides a modified nickel-base cast superalloy and a method of making, wherein the modified nickel-base cast superalloy comprises: modified IN939 superalloy, the components of the modified IN939 superalloy comprising IN mass percent: 0.11-0.16% of C and 0.006-0.018% of B. The modified IN939 superalloy comprises the following components: 22.24% of Cr, 18.73% of W, 1.97% of Nb, 0.89% of Ta, 3.66% of Ti, 1.90% of Al, 0.0063% of Mo, 0.0015% of P, 0.0035% of Mn, 0.11-0.16% of C, 0.006% of Zr, 0.006-0.018% of B, 0.019% of Hf, 0.006% of V, 0.030% of Fe, less than or equal to 0.01% of impurity and the balance of Ni, wherein the percentages of the components are mass percentages.

Description

Modified nickel-base casting superalloy and preparation method thereof
Technical Field
The disclosure belongs to the field of superalloy casting, and particularly relates to a modified nickel-based casting superalloy and a preparation method thereof.
Background
The high-temperature alloy complex thin-wall casting is a key component of high-grade technical equipment of an aerospace power system, and the manufacturing capacity and the manufacturing level of the high-temperature alloy complex thin-wall casting represent the capacity and the level of manufacturing technology of one country to a certain extent. Because of the requirements for higher performance, higher reliability and weight reduction of the structure, the high-temperature alloy complex thin-wall castings represented by the guide device, the casing and the like develop towards the structure complexity, the thin-wall weight reduction and the size accuracy, and the high requirements for good mold filling, fine structure, less or no defect of the castings are provided. Meanwhile, with the continuous improvement of the efficiency and the rotating speed of the engine, the service temperature of the castings is continuously improved, and alloy with higher temperature resistance is required. However, when some nickel-based cast high-temperature alloys are used for manufacturing castings, the casting performance and repair welding performance of the nickel-based cast high-temperature alloys are poor due to high structural change degree of the castings, so that the defects of under-casting, shrinkage cavity and the like exist when the castings are formed, the yield and the usability of the castings are reduced, and the use of the castings is affected.
Disclosure of Invention
In view of the above technical problems, the present disclosure provides a modified nickel-based casting superalloy and a preparation method thereof, so as to at least partially solve the technical problems.
In order to solve the above technical problems, as one aspect of the present disclosure, there is provided a modified nickel-based casting superalloy, wherein the modified nickel-based casting superalloy comprises: modified IN939 superalloy;
the modified IN939 superalloy comprises the following components IN percentage by mass: 0.11-0.16% of C and 0.006-0.018% of B.
According to an embodiment of the present disclosure, the components of the modified IN939 superalloy described above include: 22.24% of Cr, 18.73% of W, 1.97% of Nb, 0.89% of Ta, 3.66% of Ti, 1.90% of Al, 0.0063% of Mo, 0.0015% of P, 0.0035% of Mn, 0.11-0.16% of C, 0.006% of Zr, 0.006-0.018% of B, 0.019% of Hf, 0.006% of V, 0.030% of Fe, less than or equal to 0.01% of impurity and the balance of Ni, wherein the percentages of the components are mass percentages.
IN accordance with embodiments of the present disclosure, the flow line length of the modified IN939 superalloy described above IN a flow test conducted at a casting temperature of 1450 ℃ and a mold shell temperature of 900 ℃ includes: 369-546mm.
According to embodiments of the present disclosure, the liquidus temperature of the modified IN939 superalloy is greater than 1330 ℃; the operating temperatures used for the modified IN939 superalloy include: 0-870 ℃.
As another aspect of the present disclosure, there is also provided a method of preparing a modified nickel-base cast superalloy, comprising:
placing the additive and the unmodified nickel-based casting superalloy into a vacuum induction melting furnace for melting to obtain the modified nickel-based casting superalloy;
wherein the unmodified nickel-base casting superalloy comprises: unmodified IN939 superalloy.
According to an embodiment of the present disclosure, the above-described additive includes: boron particles and carbon powder.
According to an embodiment of the present disclosure, the amounts of the above boron particles relative to 2000g of unmodified IN939 alloy include: 3-30g;
the amounts of the above carbon powders include: 0-100g.
According to an embodiment of the present disclosure, the components IN the unmodified IN939 superalloy described above include:
22.24% of Cr, 18.73% of W, 0.89% of Ta, 1.24% of Ti, 1.9% of Al, 0.0063% of Mo, 0.0015% of P, 0.0035% of Mn, 0.11% of C, 0.006% of Zr, 0.0042% of B, 0.019% of Hf, 0.006% of V, 0.030% of Fe, less than or equal to 0.01% of impurities and the balance of Ni, wherein the percentages of the components are in mass percent.
According to an embodiment of the present disclosure, the vacuum pressure of the above-mentioned process includes: 6X 10 -2 MPa; the smelting temperature includes: 1550-1600 ℃.
According to an embodiment of the present disclosure, the time of smelting includes: 10-30 min.
Based on the above technical scheme, the modified nickel-based casting superalloy and the preparation method provided by the present disclosure have the beneficial effects that at least one of the following is included:
(1) IN the embodiment of the disclosure, the IN939 cast by nickel is a high-temperature alloy with higher alloying degree and wider solidification interval, the modified IN939 high-temperature alloy is prepared by regulating the content of boron and carbon components IN the IN939 high-temperature alloy, and the boron and carbon atoms have larger atomic radius, so that the boron components of the modified IN939 high-temperature alloy are difficult to enter into the octahedral gaps of gamma dendrites of a face-centered cubic structure IN the solidification process; and the modified IN939 superalloy is continuously displaced into the residual liquid during solidification, a boron-rich film is formed at the front edge of the solid/liquid interface, and the thicker the thickness of the boron-rich film is with the increase of the boron and carbon content, the migration rate of the boron atoms and the carbon atoms is reduced, the growth rate of gamma dendrites is slowed down, and the phenomenon of dendrite bridging occurs later, so that the fluidity of the modified IN939 superalloy is improved.
(2) In the embodiments of the present disclosure, boron and carbon have a positive adsorption effect as surface active elements, and are easily adsorbed on interfaces or surfaces, so that the concentration of boron and carbon elements on the surface of the melt is greater than that in the interior of the melt, so that the tension on the surface of the alloy melt is reduced, thereby improving the fluidity of the alloy.
(3) IN embodiments of the present disclosure, the modified IN939 superalloy may strengthen grain boundaries upon segregation of boron and carbon component content at the grain boundaries, and when the boron and carbon component content exceeds its solubility, particulate boride and carbide may precipitate along the grain boundaries, may pin the grain boundaries, impede slip deformation of the grain boundaries, thereby serving to strengthen the grain boundaries, improve alloy tensile, durability, and creep properties.
(4) The present disclosure provides a simpler method for preparing modified nickel-based cast IN939 superalloy, by modulating boron and carbon component content IN unmodified IN939 superalloy, the flow properties of modified IN939 superalloy can be improved without reducing the mechanical properties of the alloy.
Drawings
FIG. 1A is a pictorial view of an unmodified IN939 superalloy of comparative example 1 of the present disclosure;
FIGS. 1B-F are graphical illustrations of the effect of varying amounts of carbon and boron components on the fluidity of a modified IN939 superalloy IN an embodiment of the present disclosure;
FIG. 2 is a graph showing the effect of varying amounts of boron and carbon components IN examples 1-5 of the present disclosure on the surface tension at different temperatures for the preparation of modified IN939 superalloys.
Detailed Description
For the purposes of promoting an understanding of the principles and advantages of the disclosure, reference will now be made in detail to the embodiments.
The existing nickel-based cast high-temperature alloy has the defects of under-casting, shrinkage cavity and the like during casting, the yield and the service performance of the casting are reduced, the forming capacity of the casting is closely related to the casting process and alloy materials, and the fluidity of the alloy is directly related to the metal filling capacity in theory. At present, a casting process with higher casting temperature and mould shell temperature is often adopted in the production process to improve the fluidity of the alloy, but the method can enlarge the grain structure of the solidified alloy and reduce the mechanical property of the casting. Therefore, in the casting process, besides the characteristics of the alloy, how to improve the fluidity of the alloy on the premise of not reducing the mechanical property of the casting (alloy) is needed, so that a well-formed complete casting is obtained, defect generation is reduced, grains can be refined indirectly, the comprehensive performance of the casting is improved, and the method has important significance for the forming quality of large and complex thin-wall castings. However, the composition of different elements and the mechanism of action of the elements in alloy systems with different compositions are different, and the influence of the components on the structure and the performance of the specific alloy system needs to be explored and clarified so as to be convenient for practical application. Therefore, the present disclosure is directed to the investigation of nickel-base cast IN939 superalloy, and proposes a method for improving the fluidity of superalloy by regulating the composition of nickel-base superalloy without changing the mechanical properties of nickel-base cast superalloy, so as to meet the requirements of practical application.
The present disclosure provides a modified nickel-base cast superalloy, wherein the modified nickel-base cast superalloy comprises: modified IN939 superalloy, the components of the modified IN939 superalloy comprising IN mass percent: 0.11-0.16% of C and 0.006-0.018% of B.
According to embodiments of the present disclosure, the components of the modified IN939 superalloy include: 22.24% of Cr, 18.73% of W, 1.97% of Nb, 0.89% of Ta, 3.66% of Ti, 1.90% of Al, 0.0063% of Mo, 0.0015% of P, 0.0035% of Mn, 0.11-0.16% of C, 0.006% of Zr, 0.006-0.018% of B, 0.019% of Hf, 0.006% of V, 0.030% of Fe, less than or equal to 0.01% of impurity and the balance of Ni, wherein the percentages of the components are mass percentages.
According to the embodiment of the disclosure, the content of the C component is 0.11-0.16%, wherein the C component can be 0.11%, 0.15%, 0.16% or the like; the content of the component B is 0.006-0.018%, wherein the component B can be selected from 0.006%, 0.01%, 0.014%, 0.018% and the like.
IN accordance with embodiments of the present disclosure, IN a flowability test conducted at a casting temperature of 1450 ℃ and a mold form temperature of 900 ℃, the streamline length of the modified IN939 superalloy comprises: 369-546mm.
According to embodiments of the present disclosure, the liquidus temperature of the modified IN939 superalloy is greater than 1330 ℃, wherein the liquidus temperature range includes 1330-1341 ℃, more preferably 1340-1341 ℃; the working temperatures suitable for use with the modified IN939 superalloy include 0-870 ℃.
The embodiment of the disclosure also provides a preparation method of the modified nickel-based casting superalloy, which comprises the following steps: placing the additive and the unmodified nickel-based casting superalloy into a vacuum induction melting furnace for melting to obtain the modified nickel-based casting superalloy, wherein the unmodified nickel-based casting superalloy comprises: unmodified IN939 superalloy.
According to an embodiment of the present disclosure, the additive comprises: boron particles and carbon powder.
According to an embodiment of the present disclosure, the amounts of boron particles relative to 2000g of unmodified IN939 alloy include: 3-30g, wherein the dosage of the boron particles is selected from 3, 5, 10, 15, 20, 25, 30g and the like;
the amounts of carbon powder relative to 2000g of unmodified IN939 alloy included: 0-100g, wherein 0, 20, 40, 60, 80, 100g, etc. are selected.
According to embodiments of the present disclosure, the components IN the unmodified IN939 superalloy include:
22.24% of Cr, 18.73% of W, 0.89% of Ta, 1.24% of Ti, 1.9% of Al, 0.0063% of Mo, 0.0015% of P, 0.0035% of Mn, 0.11% of C, 0.006% of Zr, 0.0042% of B, 0.019% of Hf, 0.006% of V, 0.030% of Fe, less than or equal to 0.01% of impurities and the balance of Ni, wherein the percentages of the components are in mass percent.
According to an embodiment of the present disclosure, the vacuum pressure of smelting includes: 6X 10 -2 MPa。
According to an embodiment of the present disclosure, the temperature of smelting includes: 1550-1600 ℃, wherein 1550, 1575 and 1600 ℃ are selected.
According to an embodiment of the present disclosure, the time of smelting includes: 10-30 min, wherein 10, 15, 20, 25, 30min and the like can be selected.
In order to make the objects, technical solutions and advantages of the present disclosure clearer, the technical solutions and principles of the present disclosure are further explained below by specific embodiments in combination with the accompanying drawings. It should be noted that the following specific examples are given by way of illustration only, and the scope of the present disclosure is not limited thereto.
The method selects the non-modified IN939 superalloy cast by nickel base for exploration, and can improve the flow property of the IN939 superalloy by adjusting and controlling the contents of boron and carbon components under the premise of not influencing the mechanical property of the IN939 superalloy. It should be noted that the unmodified IN939 superalloy selected for use IN the present disclosure is only for illustrating that the method of the present disclosure may achieve the improvement of the flow properties of the IN939 superalloy by controlling the boron and carbon component contents IN the unmodified IN939 superalloy, and may also improve the flow properties of the IN939 superalloy by adjusting the carbon and boron component contents for the unmodified IN939 superalloy that is cast by nickel base with other component contents, although the scope of the disclosure is not limited thereto.
The performance test method of the IN939 superalloy related IN the embodiment of the disclosure is as follows:
flow performance test:
the spiral flow shuttering with the thickness of 3mm and the height of 10mm is heated to 900 ℃ and kept for 4 hours. And (3) placing the obtained IN939 high-temperature alloy with different boron and carbon component contents into a vacuum induction melting furnace for melting, after the IN939 high-temperature alloy is completely melted, preserving heat for 2min at 1550 ℃, and casting the IN939 high-temperature alloy liquid into a preheated spiral type fluidity mould shell at a casting speed of 0.5kg/s when the obtained IN939 high-temperature alloy liquid is cooled to 1450 ℃. Naturally cooling the mould shell after casting the alloy liquid to room temperature, knocking out the spiral type fluidity model, taking out a cooled spiral type IN939 superalloy sample, and measuring the streamline length of the sample so as to determine the fluidity of the superalloy, wherein the IN939 superalloy comprises: modified IN939 superalloys and unmodified IN939 superalloys.
The heat treatment process for the IN939 superalloy sample test is as follows:
placing the obtained IN939 superalloy sample IN a heat treatment furnace for 4 steps of heat treatment such as solid solution and aging, wherein the specific processes and parameters IN the related heat treatment process comprise:
a. solution heat treatment: preserving heat at 1160 ℃ for 4 hours, and then rapidly cooling to room temperature by air;
b. aging heat treatment: firstly preserving heat at 1000 ℃ for 6 hours, and then rapidly cooling to room temperature by air; preserving heat at 900 ℃ for 24 hours, and then cooling with air; finally, the temperature is kept at 700 ℃ for 16 hours, and then the mixture is cooled to room temperature by air rapidly.
Finally, the IN939 superalloy sample after the heat treatment is subjected to strain rate of 2X 10 -3 And under the condition of/s, carrying out room temperature stretching experiments by adopting a universal stretching tester, and measuring the tensile strength, the yield strength and the elongation of the IN939 superalloy.
Examples
IN the embodiment of the disclosure, a preparation method of a modified nickel-based cast IN939 superalloy involves the following specific steps:
s1, proportioning: weighing carbon powder, boron particles and unmodified IN939 high-temperature alloy according to the designed boron and carbon components IN the modified IN939 high-temperature alloy;
s2, vacuum melting: the unmodified IN939 superalloy was placed IN a vacuum induction melting furnace for melting, and after complete melting of the unmodified IN939 superalloy, the amounts of boron particles required relative to 2000g of unmodified IN939 alloy included: the dosage of 3-30g and the required carbon powder comprises: weighing the ingredients according to the proportion of 0-100g, adding the ingredients into a crucible through a charging bin of a vacuum induction melting furnace, and repeatedly melting for 5 times, so as to reduce macrosegregation and uniformly distribute added boron and carbon components IN the modified IN939 superalloy, thereby obtaining modified IN939 superalloy samples with different boron and carbon component contents.
Smelting conditions to which the present disclosure relates include: a.6X10 -2 Vacuum state of MPa; b. the smelting temperature is 1550-1600 ℃; c. electromagnetic stirring is adopted in the smelting process; d. the smelting time is 15min.
Example 1
Example 1 is a modified IN939 superalloy composed of C content of 0.11%, B content of 0.006% and other component content, wherein the modified IN939 superalloy is formulated as shown IN table 1 with reference numeral 1 IN the accompanying drawings.
TABLE 1
Cr(％) Co(％) W(％) Nb(％) Ta(％) Ti(％) Al(％)
22.24 18.73 1.97 0.89 1.24 3.66 1.90
Mo(％) P(％) Mn(％) C(％) Zr(％) B(％) Ni(％)
0.0063 0.0015 0.0035 0.11 0.006 0.006 Allowance of
Hf(％) V(％) Fe(％) Impurity (%)
0.019 0.006 0.030 ≤0.01
Example 2
Example 2 is a modified IN939 superalloy composed of C content of 0.11%, B content of 0.01% and other component content, wherein the formulation of the modified IN939 superalloy is shown IN table 2, numbered 2 IN the accompanying drawings.
TABLE 2
Cr(％) Co(％) W(％) Nb(％) Ta(％) Ti(％) Al(％)
22.24 18.73 1.97 0.89 1.24 3.66 1.90
Mo(％) P(％) Mn(％) C(％) Zr(％) B(％) Ni(％)
0.0063 0.0015 0.0035 0.11 0.006 0.01 Allowance of
Hf(％) V(％) Fe(％) Impurity (%)
0.019 0.006 0.030 ≤0.01
Example 3
Example 3 is a modified IN939 superalloy composed of 0.11% C, 0.014% B and other component content, wherein the modified IN939 superalloy is formulated as shown IN table 3, with reference numeral 3 IN the drawing.
TABLE 3 Table 3
Cr(％) Co(％) W(％) Nb(％) Ta(％) Ti(％) Al(％)
22.24 18.73 1.97 0.89 1.24 3.66 1.90
Mo(％) P(％) Mn(％) C(％) Zr(％) B(％) Ni(％)
0.0063 0.0015 0.0035 0.11 0.006 0.014 Allowance of
Hf(％) V(％) Fe(％) Impurity (%)
0.019 0.006 0.030 ≤0.01
Example 4
Example 4 is a modified IN939 superalloy composed of C content of 0.11%, B content of 0.018%, and other component content, wherein the modified IN939 superalloy is formulated as shown IN table 4, reference numeral 4 IN the accompanying drawings.
TABLE 4 Table 4
Cr(％) Co(％) W(％) Nb(％) Ta(％) Ti(％) Al(％)
22.24 18.73 1.97 0.89 1.24 3.66 1.90
Mo(％) P(％) Mn(％) C(％) Zr(％) B(％) Ni(％)
0.0063 0.0015 0.0035 0.11 0.006 0.018 Allowance of
Hf(％) V(％) Fe(％) Impurity (%)
0.019 0.006 0.030 ≤0.01
Example 5
Example 5 is a modified IN939 superalloy composed of 0.16% C, 0.014% B and other component content, wherein the modified IN939 superalloy is formulated as shown IN table 5, numbered 5 IN the accompanying figures.
TABLE 5
Cr(％) Co(％) W(％) Nb(％) Ta(％) Ti(％) Al(％)
22.24 18.73 1.97 0.89 1.24 3.66 1.90
Mo(％) P(％) Mn(％) C(％) Zr(％) B(％) Ni(％)
0.0063 0.0015 0.0035 0.16 0.006 0.014 Allowance of
Hf(％) V(％) Fe(％) Impurity (%)
0.019 0.006 0.030 ≤0.01
Comparative example
Comparative example 1
The unmodified IN939 superalloy of comparative example 1 was prepared IN the same manner as IN the examples, except that no boron particles and no carbon powder were added.
The compositions of the components of the unmodified IN939 superalloy of comparative example 1, IN which the percentages are mass percentages, were shown IN table 6, with a C content of 0.11% and a B content of 0.0042%.
TABLE 6
Cr(％) Co(％) W(％) Nb(％) Ta(％) Ti(％) Al(％)
22.24 18.73 1.97 0.89 1.24 3.66 1.90
Mo(％) P(％) Mn(％) C(％) Zr(％) B(％) Ni(％)
0.0063 0.0015 0.0035 0.11 0.006 0.0042 Allowance of
Hf(％) V(％) Fe(％) Impurity (%)
0.019 0.006 0.030 ≤0.01
FIG. 1A is a pictorial view of an unmodified IN939 superalloy of comparative example 1 of the present disclosure; FIGS. 1B-F are graphical representations of the effect of varying amounts of carbon and boron components on the fluidity of modified IN939 superalloy IN the examples of the present disclosure.
The IN939 superalloy of the above examples and comparative examples was tested for fluidity and tensile properties at a casting temperature of 1450 ℃ and a mold shell temperature of 900 ℃ using a spiral fluidity test model to determine the length of a streamline of the liquid superalloy as it solidifies IN the model to characterize its fluidity, wherein the IN939 superalloy comprises: modified IN939 superalloys and unmodified IN939 superalloys.
Table 7 shows the flow performance test results for the disclosed examples and comparative example IN939 superalloys.
TABLE 7
As can be seen from Table 7, by using the method provided by the present disclosure, the modified IN939 superalloy was prepared by increasing the contents of boron and carbon elements, and the fluidity of the modified IN939 superalloy was improved by 21-79% when the mass percentages of the boron and carbon components were 0.006-0.018% and 0.11-0.16%, respectively, as compared to the unmodified IN939 superalloy, without decreasing the mechanical properties of the superalloy, and particularly when the contents of the boron and carbon components were 0.14% and 0.16%, respectively, the fluidity of the prepared modified IN939 superalloy was improved by 79% as compared to the fluidity of the unmodified IN939 superalloy.
Comparative example 2
Comparative example 2 is a modified IN939 superalloy composed of C content of 0.18%, B content of 0.20% and other component content, and the formulation of the modified IN939 superalloy is shown IN table 8.
TABLE 8
Cr(％) Co(％) W(％) Nb(％) Ta(％) Ti(％) Al(％)
22.24 18.73 1.97 0.89 1.24 3.66 1.90
Mo(％) P(％) Mn(％) C(％) Zr(％) B(％) Ni(％)
0.0063 0.0015 0.0035 0.18 0.006 0.20 Allowance of
Hf(％) V(％) Fe(％) Impurity (%)
0.019 0.006 0.030 ≤0.01
The modified IN939 superalloy solidification temperature interval related data was obtained by DSC experiments (differential scanning calorimetry) and JMatPro software calculations on the modified IN939 superalloy prepared from the components IN table 8. Experimental results show that the solidification temperature interval in comparative example 2 is increased by about 10 ℃ compared with the range of the solidification temperature interval in the embodiment of the disclosure, and the larger the solidification interval of the superalloy is, the worse the fluidity is. Accordingly, for the modified IN939 superalloy, the fluidity thereof becomes worse beyond the content range of the carbon and boron components provided IN the present disclosure, wherein the solidification temperature interval IN examples 1 to 5 of the present disclosure is 92 to 98 ℃ and the solidification temperature interval IN comparative example 2 is 108 ℃.
Meanwhile, since the contents of the carbon and boron components are further increased, a low melting point phase such as boride is easily formed, and the initial melting temperature is reduced by about 10 ℃ compared with the alloy of the range of examples of the present disclosure, resulting in reduced hot workability and use temperature of the alloy, wherein the initial melting temperature of examples 1 to 5 of the present disclosure ranges from 1223 to 1216 ℃ and the initial melting temperature of comparative example 2 is 1206 ℃.
The fluidity of the IN939 superalloy can be changed by changing the contents of the boron and carbon components IN the IN939 superalloy mainly by:
(1) The IN939 superalloy is a nickel-based cast superalloy, belongs to an alloy with a wide crystallization temperature range, has slow solidification process for a superalloy with a larger solidification zone, is easy to form a large number of dendrites, and the dendrites grow and are connected into a network, so that the flow of alloy liquid is blocked, the liquid alloy can not heal a torn liquid film between dendrite grain boundaries, and solidification cracks are formed. IN embodiments of the present disclosure, the flow is stopped because IN939 superalloy grows with dendrites as the solidification process proceeds, and as the viscosity of the alloy liquid increases and the flow rate slows, the alloy liquid flow is stopped when dendrites IN the IN939 superalloy overlap each other to form a continuous network and the pressure of the alloy liquid cannot overcome the resistance of the network at that time. Thus, delaying dendrite bridging of the IN939 superalloy may increase the fluidity of the IN939 superalloy, while the rate of dendrite bridging of the IN939 superalloy is primarily affected by the growth rate of gamma dendrites. According to the theory of crystal growth, the growth rate of gamma dendrites in an alloy can be expressed by the following formula:
V＝δ(R S - R l ) (1)
in formula (1), δ is a typical atomic distance, R s R is the rate of transition of atoms from liquid to solid phase l Is the rate at which atoms transition from a solid phase to a liquid phase.
In the solidification process of the superalloy, since boron and carbon atoms are difficult to enter into octahedral gaps of gamma dendrites of a face-centered cubic structure in the solidification process, as the solidification process proceeds, the boron and carbon atoms are continuously displaced into residual liquid, a boron-rich film is formed at the front edge of a solid/liquid interface, and as the content of boron and carbon components increases, the film thickness of the boron-rich film becomes thicker gradually, thereby reducing the rate R of transition of atoms from a liquid phase to a solid phase s And a rate of transition from solid to liquid R l The growth rate V of gamma dendrites in the alloy is reduced from 0.09 to 0.083, so that the phenomenon of gamma dendrite lap joint appears later, and the fluidity of the high-temperature alloy is improved.
In addition, the smaller the supercooling degree of the alloy, the smaller the growth rate of gamma dendrites when the alloy is solidified. The supercooling degree of the modified IN939 superalloy IN the embodiment of the disclosure is reduced from 11 ℃ to 3 ℃ along with the increase of the boron and carbon content, so that the growth rate of gamma dendrites is reduced, and the phenomenon of gamma dendrite lap joint is caused to occur later, thereby improving the fluidity of the alloy.
(2) Surface tension also has an important effect in the flow of superalloy liquids. IN the flowing process of the IN939 high-temperature alloy liquid, the generated surface tension is the pressure pointing to the interior of the alloy melt, so that the surface of the alloy melt is promoted to shrink, the larger the surface tension is, the larger the generated pressure is, the larger the resistance to the fluidity of the high-temperature alloy is, and the fluidity of the high-temperature alloy is reduced. The alloy surface tension to the melt can be expressed by the following formula:
in formula (2), Γ is the mass (mol/m) of solute that is more adsorbed per unit liquid metal surface area than inside -3 ) The method comprises the steps of carrying out a first treatment on the surface of the R is Boltzmann constant; t is the thermodynamic temperature (K); c (C) i Dσ/(d) for solute concentration Ci ) The surface tension of the alloy is characterized.
Boron and carbon elements are used as surface active elements, have positive adsorption effect and can be enriched in a residual liquid phase. Therefore, it is easily adsorbed on the interface or surface, resulting in the concentration of boron and carbon elements at the surface of the alloy melt being greater than those at the inside of the melt, so that Γ is positive, -C i With negative/RT, dσ/(d) Ci ) Is negative.
FIG. 2 is a graph showing the effect of varying amounts of boron and carbon components IN examples 1-5 of the present disclosure on the surface tension at different temperatures for the preparation of modified IN939 superalloys.
As shown IN FIG. 2, the effect of varying levels of boron and carbon components IN the examples on the surface tension of the modified IN939 superalloy prepared using the JMatPro software was investigated at varying temperatures as the levels of boron and carbon IN the alloy increased, solute concentration C i The increased surface tension of the alloy melt decreases, resulting IN a reduced flow resistance IN the die cavity, thereby improving the fluidity of the modified IN939 superalloy.
Table 9 is the results of testing the tensile properties of the modified IN939 superalloy IN examples 2, 5 of the present disclosure and the IN939 superalloy IN comparative example 1.
TABLE 9
Alloy species Tensile strength (MPa) Yield strength (MPa) Elongation (%)
Comparative example 1 810.5 653.8 3.41
Example 2 916.5 711.6 5.75
Example 5 900.9 827.5 5.69
As can be seen from Table 9, the appropriate increase of the boron component content and the boron and carbon component content IN the IN939 superalloy can effectively improve the tensile property, creep deformation and durability of the alloy. The main reasons are as follows: boron and carbon components in the nickel-based superalloy, by changing the concentration of valence electrons at the grain boundary region and forming strong metal bonds, which tend to fill in the grain boundary defects, can block migration and diffusion of grain boundaries, improve the bonding force of the grain boundaries, reduce the formation rate of grain boundary voids in the endurance process, and thereby improve the tensile, creep and endurance properties of the alloy. In addition, boron and carbon precipitate along the grain boundary after the segregation of the grain boundary exceeds the solubility of the boron and carbon, and the grain boundary can be pinned and the slip deformation of the grain boundary can be blocked from the granular boride and carbide precipitated along the grain boundary, so that the grain boundary is strengthened, and the tensile, lasting and creep performances of the alloy are improved. However, when the content of boron and carbon components IN the IN939 superalloy is excessive, boride or carbide IN the alloy may be precipitated IN a block or lamellar form, and there is a problem of difficulty IN deformation during permanent fracture of the alloy, which easily results IN formation of micropores and connection, deteriorating tensile and durability properties of the alloy.
Therefore, under the consideration of the influence of boron and carbon components on the comprehensive performance of the modified IN939 superalloy, the flow performance of the modified IN939 superalloy can be improved on the premise of not reducing the mechanical performance by controlling the content of the boron and carbon components within the range of 0.006-0.018% and 0.11-0.16% respectively so as to meet the requirements of advanced aeroengine castings.
While the foregoing is directed to embodiments of the present disclosure, other and further details of the invention may be had by the present application, it is to be understood that the foregoing description is merely exemplary of the present disclosure and that no limitations are intended to the scope of the disclosure, except insofar as modifications, equivalents, improvements or modifications may be made without departing from the spirit and principles of the present disclosure.

Claims (6)

1. A modified nickel-base cast superalloy, wherein the modified nickel-base cast superalloy is a modified IN939 superalloy;
the modified IN939 superalloy comprises the following components IN percentage by mass: 0.16% C, 0.014% B or 0.11% C, 0.018% B; and
22.24% Cr, 18.73% Co, 1.97% W, 0.89% Nb, 1.24% Ta, 3.66% Ti, 1.90% Al, 0.0063% Mo, 0.0015% P, 0.0035% Mn, 0.006% Zr, 0.019% Hf, 0.006% V, 0.030% Fe, less than or equal to 0.01% impurity, and the balance Ni;
IN the flowability test at 1450℃and 900℃in the form, the modified IN939 superalloy with 0.16% C and 0.014% B had a streamline length of 546mm or the modified IN939 superalloy with 0.11% C and 0.018% B had a streamline length of 387mm.
2. The superalloy of claim 1, wherein the modified IN939 superalloy has a liquidus temperature greater than 1330 ℃;
the operating temperatures for the modified IN939 superalloy include: 0-870 ℃.
3. A method of preparing a modified nickel-base cast superalloy comprising:
placing the additive and the unmodified nickel-based casting superalloy into a vacuum induction melting furnace for melting to obtain the modified nickel-based casting superalloy;
wherein the unmodified nickel-base casting superalloy is: unmodified IN939 superalloy; the modified nickel-based casting superalloy is as follows: an IN939 superalloy, the modified IN939 superalloy comprising, IN mass percent: 0.16% C, 0.014% B or 0.11% C, 0.018% B; and
22.24% Cr, 18.73% Co, 1.97% W, 0.89% Nb, 1.24% Ta, 3.66% Ti, 1.90% Al, 0.0063% Mo, 0.0015% P, 0.0035% Mn, 0.006% Zr, 0.019% Hf, 0.006% V, 0.030% Fe, less than or equal to 0.01% impurity, and the balance Ni;
the additive comprises: boron particles and carbon powder, wherein the amounts of boron particles relative to 2000g of unmodified IN939 alloy comprise: 3-30g, wherein the dosage of the carbon powder comprises: 0-100g.
4. The method of claim 3, wherein the components IN the unmodified IN939 superalloy comprise:
22.24% of Cr, 18.73% of W, 0.89% of Ta, 1.24% of Ti, 1.9% of Al, 0.0063% of Mo, 0.0015% of P, 0.0035% of Mn, 0.11% of C, 0.006% of Zr, 0.0042% of B, 0.019% of Hf, 0.006% of V, 0.030% of Fe, less than or equal to 0.01% of impurities and the balance of Ni, wherein the percentages of the components are in mass percent.
5. The method of claim 3, wherein the vacuum pressure of smelting comprises: 6X 10 -2 MPa；
The smelting temperature includes: 1550-1600 ℃.
6. The method of claim 3, wherein the time of smelting comprises: 10-30 min.
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Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP1038983A1 (en) * 1999-03-26 2000-09-27 Howmet Research Corporation Single crystal nickel-base alloy
CN103556073A (en) * 2013-10-30 2014-02-05 西安热工研究院有限公司 High-temperature alloy cast tube material for 700 DEG C level ultra-supercritical thermal power generating unit reheater and preparation method of high-temperature alloy cast tube material

Family Cites Families (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CA1202505A (en) * 1980-12-10 1986-04-01 Stuart W.K. Shaw Nickel-chromium-cobalt base alloys and castings thereof
US20020005233A1 (en) * 1998-12-23 2002-01-17 John J. Schirra Die cast nickel base superalloy articles
US6696176B2 (en) * 2002-03-06 2004-02-24 Siemens Westinghouse Power Corporation Superalloy material with improved weldability
US8652650B2 (en) * 2009-10-22 2014-02-18 Honeywell International Inc. Platinum-modified nickel-based superalloys, methods of repairing turbine engine components, and turbine engine components
US10076811B2 (en) * 2011-11-03 2018-09-18 Siemens Energy, Inc. Structural braze repair of superalloy component
CN103924124B (en) * 2014-04-21 2016-02-10 西北工业大学 A kind of K4169 superalloy increasing boron content
CN106794519B (en) * 2014-10-14 2019-05-28 西门子能源有限公司 The laser gain material of the three-dimensional part comprising multiple material of being formed as one system manufactures
CN105506390B (en) * 2015-12-30 2017-06-23 钢铁研究总院 A kind of nickel base superalloy containing zirconium and preparation method

Patent Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP1038983A1 (en) * 1999-03-26 2000-09-27 Howmet Research Corporation Single crystal nickel-base alloy
CN103556073A (en) * 2013-10-30 2014-02-05 西安热工研究院有限公司 High-temperature alloy cast tube material for 700 DEG C level ultra-supercritical thermal power generating unit reheater and preparation method of high-temperature alloy cast tube material

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