CN113186430A - Nickel-based alloy material for gas valve and preparation method thereof - Google Patents
Nickel-based alloy material for gas valve and preparation method thereof Download PDFInfo
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- CN113186430A CN113186430A CN202010035300.9A CN202010035300A CN113186430A CN 113186430 A CN113186430 A CN 113186430A CN 202010035300 A CN202010035300 A CN 202010035300A CN 113186430 A CN113186430 A CN 113186430A
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- 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%
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- 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
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/002—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working by rapid cooling or quenching; cooling agents used therefor
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/10—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of nickel or cobalt or alloys based thereon
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Abstract
The invention relates to a nickel-based alloy material for a gas valve, which comprises the following elements in percentage by weight: c: 0.05-0.10%; cr: 20.0 to 23.0 percent; mo: 0.15 to 1.0 percent; al: 1.00-1.90%; ti: 1.80-2.80%; fe is less than or equal to 1.0 percent; co is less than or equal to 2.0 percent; s is less than or equal to 0.004 percent; p is less than or equal to 0.007 percent; si is less than or equal to 0.40 percent; mn is less than or equal to 0.35 percent; zr is less than or equal to 0.05 percent; less than or equal to 0.008 percent of B, and the balance of nickel and inevitable impurities. Compared with the prior art, the invention has the advantages that the stability of the M23C6 phase is improved by adjusting the content of C, Mo, Cr and other elements and combining a certain manufacturing method, the dual control is carried out by the M23C6 phase and the M7C3 phase, the function of pinning the grain boundary is realized, and the requirement that the high-temperature solid solution grain structure is not grown and still maintained at 5 grade or finer is realized.
Description
Technical Field
The invention belongs to the relevant field of high-temperature alloy manufacturing, and particularly relates to the relevant technical field of manufacturing of nickel-based alloy for an air valve of an automobile or ship engine.
Background
The high-temperature alloy is called as thermal strength alloy, heat-resistant alloy or superalloy, and can work for a long time at a high temperature of more than 600 ℃ under the action of certain stress. It has high-temperature strength, excellent antioxidant and hot corrosion resisting performance, excellent fatigue performance, excellent plasticity and other comprehensive performance. Based on the performance characteristics, the high-temperature alloy is widely applied to the fields of aerospace, electric power, oil gas, vehicles and the like. The alloy material can be divided into nickel-based, iron-based and cobalt-based alloy materials.
The N80A (or NiCr20TiAl) alloy is a nickel-based aging-strengthened high-temperature alloy, and is widely applied to key components such as aeroengine blades, fasteners, air valves and the like due to excellent high-temperature strength and good high-temperature corrosion resistance. In recent years, with the continuous development of the automobile industry, some nickel-based high-temperature alloys represented by N80A are applied and popularized in automobile engine valves. Although the valve is applied to the civil field, the valve has a harsh working environment, is not only subjected to the scouring of high-temperature and high-pressure gas, but also bears great thermal stress and mechanical stress. Therefore, the valve has high corrosion resistance and high-temperature strength and good fatigue performance in order to resist gas corrosion.
Due to the harsh use environment, the high requirements on the use performance of the valve material are also provided. At present, the requirement of the air valve on the grain size of the nickel-based alloy bar reaches 5 levels or finer, and particularly, after the bar is subjected to solution treatment at 1050-. According to the second phase grain control principle, in order to ensure that the crystal grain structure of the 1050-1080 ℃ heat preservation is not coarsened, the second phase grains are required to control the grains. In the N80A alloy, the M23C6 phase can be completely dissolved at 1020 ℃, and the grain growth at the solid solution temperature of 1050-. Although the M7C3 phase belongs to a stable phase at high temperature, the M7C3 phase is precipitated in an irregular block shape, is unevenly distributed, is easily grown in a strip shape, is difficult to block grain boundary migration during high-temperature solid solution, and cannot effectively control grain growth.
After searching key words of nickel-based alloy, air valves and the like, 5 invention patents and 2 utility model patents are found to be related to the key words. The 2 utility model patents are relevant valve structural design and are irrelevant with this patent material. In the patent of 5 inventions, ZL201610749580.3 introduces a welding method of valve surfacing, which is irrelevant to the patent; the components of the nickel-based alloy material for the ZL201210247887.5 valve are 77-82% of nickel, 2.2-3.4% of iron, 9.5-12.5% of chromium, 0.1-0.5% of carbon, 3.5-4.2% of silicon and 2.0-2.5% of boron, and the nickel-based alloy material has larger difference with the alloy components in the patent; the patent ZL201210085856.4 discloses a novel nickel-based alloy for an exhaust valve of an internal combustion engine, which comprises the following components: 0.02-0.05%, Cr: 21.0-25.0%, Ti: 2.4-3.0%, Al: 1.6-2.2%, Fe: 3.0-5.0%, Co: 0-3%, Nb: 0.02-0.5%, the balance being Ni and inevitable impurities, which are different from the components of the alloy; patent ZL201510163235.7 relates to a method for forming an annular valve seat area in an exhaust valve for an internal combustion engine, and patent ZL201610557469.4 relates to a welding process for welding nickel-based alloy on a sealing surface of a gas valve of a marine low-speed engine in a build-up welding mode. The patents referred to are not relevant to this patent.
Disclosure of Invention
The invention aims to provide a high-performance nickel-based alloy material for an engine valve and a preparation method thereof. By adjusting the content of elements such as C, Mo and Cr and combining a certain manufacturing method, the M23C6 phase and the M7C3 phase are adopted for dual control, the function of pinning the grain boundary is achieved, and the requirement that the high-temperature solid solution crystal grains are not coarsened is met. Meanwhile, the obtained material has excellent performance and meets the use requirement of the engine valve.
The invention is realized by the following technical scheme:
the invention provides a nickel-based alloy material for a gas valve, which comprises the following elements in percentage by weight:
c: 0.05-0.10%; cr: 20.0 to 23.0 percent; mo: 0.15 to 1.0 percent; al: 1.00-1.90%; ti: 1.80-2.80%; fe is less than or equal to 1.0 percent; co is less than or equal to 2.0 percent; s is less than or equal to 0.004 percent; p is less than or equal to 0.007 percent; si is less than or equal to 0.40 percent; mn is less than or equal to 0.35 percent; zr is less than or equal to 0.05 percent; less than or equal to 0.008 percent of B, and the balance of nickel and inevitable impurities.
The following description is made of the ranges of the key elements in the alloy of the present invention and the reasons for controlling the ranges:
1)C：0.05-0.10％；
c is an essential element for carbide formation in nickel-base superalloys. By reasonably controlling the chemical composition and the hot working process, three carbides of MC, M23C6 and M7C3 can be obtained in the alloy. When the C content is less than 0.05%, it is difficult to generate sufficient M23C6 and M7C3 phases to pin the grain boundaries, and the grain size is coarse. Too high carbon content will form too much carbide to cause the excessive inclusion and segregation problems, resulting in non-uniform crystal grains and poor alloy plasticity. Therefore, the C content needs to be controlled within the range of 0.05-0.10%.
2)Cr：20.0-23.0％；
Cr is a matrix element in the alloy, and is dissolved in the matrix to mainly increase the oxidation resistance and the corrosion resistance of the alloy. Meanwhile, the precipitation of the carbide M23C6 and M7C3 phases can be promoted, the stability of the M23C6 phase can be improved by increasing the Cr content, and the quantity of the M23C6 and M7C3 phases can be increased. When the Cr content is lower, less carbide is separated out; when the Cr content is too high, the formation of M7C3 is suppressed, and the range of M7C3 precipitation is narrowed, which is disadvantageous in grain structure control. Therefore, the Cr content is comprehensively considered to be controlled to be 20.0-23.0%.
3)Mo：0.15-1.0％；
Mo mainly plays a role in solid solution strengthening and participating in carbide reaction in the alloy. Mo replaces Cr in M23C6 to influence the precipitation of an M23C6 phase, the stability of the M23C6 phase can be improved along with the increase of the Mo content, and the tendency of aggregation and growth of the M7C3 phase is reduced. When the Mo content is low, the stability of M23C6 is low, and the Mo content is difficult to play a role in pinning grain boundaries during high-temperature solid solution; too high Mo content results in a decrease in the amount of M7C3 phase, while precipitation of μ phase in the matrix tends to impair the durability of the alloy and also increases the cost. Therefore, the Mo content is controlled to be 0.15-1.0 percent by comprehensive consideration.
4)Al：1.00-1.90％；
Al is a main element of a gamma ' phase in the nickel-based alloy, a certain amount of gamma ' structures can be precipitated by controlling a proper aluminum element, and the gamma ' structures and a matrix gamma solid solution form a coherent or semi-coherent relationship to form reinforcement. Meanwhile, the addition of Al obviously improves the oxidation resistance of the alloy, and a layer of compact oxide film is formed at high temperature to protect the alloy. The higher the Al content, the greater the precipitation amount of the gamma' phase, but too high Al increases the difficulty of hot working of the alloy, making the material susceptible to cracking. Therefore, Al is controlled to be 1.00-1.90%.
5)Ti：1.80-2.80％；
The alloy contains higher Ti because Ti in the alloy is easily dissolved into a gamma' phase and can also be used as a main forming element. After Ti enters gamma ', the precipitation of the gamma' is slowed down, and the over-aging is prevented, so that the alloy is suitable for being used in a high-temperature working environment for a long time. However, excessive Ti addition results in Ni3Ti (eta phase), while Ni3Ti phase has no age hardening capacity, so that the Ti content of the alloy is controlled within the range of 1.80-2.80%.
As a preferred scheme, the weight percentages of the elements are respectively as follows:
c: 0.06-0.08%; cr: 21.0 to 22.5 percent; mo: 0.30-0.80%; al: 1.00-1.90%; ti: 1.80-2.80%; fe is less than or equal to 1.0 percent; co is less than or equal to 2.0 percent; s is less than or equal to 0.004 percent; p is less than or equal to 0.007 percent; si is less than or equal to 0.40 percent; mn is less than or equal to 0.35 percent; zr is less than or equal to 0.05 percent; less than or equal to 0.008 percent of B, and the balance of nickel and inevitable impurities.
The preparation method of the nickel-based alloy material for the gas valve comprises the following steps:
after proportioning according to the element components, carrying out vacuum induction melting and casting molding to obtain an electrode;
carrying out electroslag remelting on the electrode to obtain an electroslag ingot;
carrying out hot forging cogging on the electroslag ingot to obtain a nickel-based alloy material bar;
and sequentially carrying out solid solution treatment and aging treatment on the nickel-based alloy material bar.
After solution treatment (1080 ℃ multiplied by 1h), the grain structure is not grown and still maintained at grade 5 or finer. After the nickel-based alloy material with the composition range is subjected to proper solution treatment and aging treatment, the tensile strength at room temperature is greater than 1200MPa, the yield strength is between 860 and 920MPa, the elongation at break is greater than 20%, the reduction of area is greater than 25%, and the room-temperature rotational bending fatigue limit (107 weeks) is between 480 and 520 MPa.
Preferably, the hot forging method comprises the following steps:
keeping the temperature of the electroslag ingot at 1150-1170 ℃ for at least 3h, upsetting to 1/3-1/2 of the original length, drawing to the original length, annealing at 1150-1170 ℃ for 2h, drawing to a bar with a diameter of 300, annealing at 1070-1130 ℃ under the protection of heat-insulating cotton to obtain a bar blank;
and (3) preserving the temperature of the bar blank at 1080-1120 ℃ for 5-8h, drawing out the bar material until the bar material is phi 200, forging, air cooling, and controlling the finish forging temperature to be not lower than 1000 ℃.
Preferably, the temperature of the solution treatment is 1070-.
Preferably, the temperature of the aging treatment is 700-720 ℃, the time is 16h, and the air cooling treatment is carried out.
The method of the invention has the main advantages that:
compared with the prior art, the invention has the advantages that the stability of the M23C6 phase is improved by adjusting the content of C, Mo, Cr and other elements and combining a certain manufacturing method, the dual control is carried out by the M23C6 phase and the M7C3 phase, the function of pinning the grain boundary is realized, and the requirement that the high-temperature solid solution grain structure is not grown and still maintained at 5 grade or finer is realized. Meanwhile, the obtained material has excellent performance and meets the use requirement of the engine valve.
Drawings
Other features, objects and advantages of the invention will become more apparent upon reading of the detailed description of non-limiting embodiments with reference to the following drawings:
FIG. 1 is a metallographic photograph (magnified 100 times) of the center (scale 6.0 to 5.0) of a bar (in a solid solution state) obtained in example 5 of the present invention;
FIG. 2 is a photomicrograph (at 100 times magnification) of the bar (in a solid solution state) at R/2 (6.0-5.5 grade) obtained in example 5 of the present invention;
FIG. 3 is a metallographic photograph (magnified 100 times) of the edge (7.0 to 6.0 grade) of the bar (in a solid solution state) obtained in example 5 of the present invention;
FIG. 4 is a metallographic photograph (magnified 100 times) of the center (2-5 levels) of a comparative alloy bar (solid solution state);
FIG. 5 is a metallographic photograph (magnified 100 times) of a comparative alloy bar (in a solid solution state) at R/2 (level 1-5);
FIG. 6 is a metallographic photograph (magnified 100 times) of the edge (0-5 scale) of a comparative alloy bar (solid solution state);
FIG. 7 is a heating profile of ingot forging.
Detailed Description
The present invention will be described in detail with reference to specific examples. The following examples will assist those skilled in the art in further understanding the invention, but are not intended to limit the invention in any way. It should be noted that variations and modifications can be made by persons skilled in the art without departing from the spirit of the invention. All falling within the scope of the present invention.
The elemental composition ratios of examples 1 to 5 of the present invention and comparative alloys are shown in table 1, and the preparation methods are detailed below:
after proportioning according to the element components, carrying out vacuum induction melting and casting molding to obtain an electrode with phi 340;
carrying out electroslag remelting on the electrode to obtain an electroslag ingot of phi 430;
keeping the temperature of the electroslag ingot at 1150-1170 ℃ for at least 3h, upsetting to 1/3-1/2 of the original length, drawing to the original length, returning to the furnace at 1150-1170 ℃ for keeping the temperature for 2h, then drawing to 300 circles, returning to the furnace at 1070-1130 ℃ under the protection of heat insulation cotton to obtain a bar blank;
keeping the temperature of the bar blank at 1080-1120 ℃ for 5-8h, drawing the bar blank to 200 circles, forging, air-cooling, and controlling the finish forging temperature to be not lower than 1000 ℃ to obtain a bar, wherein the temperature curve during forging is shown in FIG. 7;
sequentially carrying out solid solution treatment and aging treatment on the nickel-based alloy material bar, wherein the temperature of the solid solution treatment is 1070 and 1090 ℃ and the time is 1h, and carrying out air cooling treatment; the temperature of the aging treatment is 700-720 ℃, the time is 16h, and the air cooling treatment is carried out.
After the solid solution treatment and the aging treatment are carried out on the examples 1 to 5 and the comparative alloy, the corresponding grain size comparison condition is shown in table 2, the performance comparison condition is shown in table 3, and the metallographic structure of the solid solution metallographic structure and the metallographic structure of the comparative alloy are shown in fig. 1 to 6 respectively by taking the example 5 as an example.
TABLE 1 chemical composition of the alloys (percent by weight)
TABLE 2 grain size rating of alloy bars (solid solution)
TABLE 3 comparison of alloy Performance data
As can be seen from the comparison of the above examples and the photographs of the relevant data of the comparative alloy, the alloy prepared according to the alloy composition control idea and the specific manufacturing method introduced in the patent of the invention has the average structure of the solid solution bar material reaching 5 grades or thinner, and has more excellent room temperature mechanical property and fatigue property compared with the existing alloy, thereby completely meeting the standard requirements of engine valve material selection.
In summary, the present invention is only a preferred embodiment, and not intended to limit the scope of the invention, and all equivalent changes and modifications in the shape, structure, characteristics and spirit of the present invention described in the claims should be included in the scope of the present invention.
Claims (8)
1. The nickel-based alloy material for the gas valve is characterized by comprising the following elements in percentage by weight:
c: 0.05-0.10%; cr: 20.0 to 23.0 percent; mo: 0.15 to 1.0 percent; al: 1.00-1.90%; ti: 1.80-2.80%; fe is less than or equal to 1.0 percent; co is less than or equal to 2.0 percent; s is less than or equal to 0.004 percent; p is less than or equal to 0.007 percent; si is less than or equal to 0.40 percent; mn is less than or equal to 0.35 percent; zr is less than or equal to 0.05 percent; less than or equal to 0.008 percent of B, and the balance of nickel and inevitable impurities.
2. The nickel-based alloy material for the gas valve as claimed in claim 1, wherein the weight percentages of the elements are respectively as follows:
c: 0.06-0.08%; cr: 21.0 to 22.5 percent; mo: 0.30-0.80%; al: 1.00-1.90%; ti: 1.80-2.80%; fe is less than or equal to 1.0 percent; co is less than or equal to 2.0 percent; s is less than or equal to 0.004 percent; p is less than or equal to 0.007 percent; si is less than or equal to 0.40 percent; mn is less than or equal to 0.35 percent; zr is less than or equal to 0.05 percent; less than or equal to 0.008 percent of B, and the balance of nickel and inevitable impurities.
3. A method for preparing a nickel-based alloy material for a gas valve according to claim 1 or 2, comprising the steps of:
after proportioning according to the element components, carrying out vacuum induction melting and casting molding to obtain an electrode;
carrying out electroslag remelting on the electrode to obtain an electroslag ingot;
carrying out hot forging cogging on the electroslag ingot to obtain a nickel-based alloy material bar;
and sequentially carrying out solid solution treatment and aging treatment on the nickel-based alloy material bar.
4. The method for preparing the nickel-based alloy material for the gas valve as claimed in claim 3, wherein the solution treatment temperature is 1070-.
5. The method for preparing the nickel-based alloy material for the gas valve as claimed in claim 3, wherein the aging treatment temperature is 700-720 ℃ and the time is 16 h.
6. The method for preparing the nickel-based alloy material for the gas valve as claimed in claim 3, wherein the hot forging cogging method comprises:
keeping the temperature of the electroslag ingot at 1150-1170 ℃ for at least 3h, upsetting to 1/3-1/2 of the original length, drawing to the original length, annealing at 1150-1170 ℃ for 2h, drawing to a bar with a diameter of 300, annealing at 1070-1130 ℃ under the protection of heat-insulating cotton to obtain a bar blank;
and (3) preserving the temperature of the bar blank at 1080-1120 ℃ for 5-8h, drawing out the bar material until the bar material is phi 200, forging, air cooling, and controlling the finish forging temperature to be not lower than 1000 ℃.
7. The method for preparing the nickel-based alloy material for the gas valve as claimed in claim 3, wherein the solution treatment is performed in air cooling at 1070-.
8. The method for preparing the nickel-based alloy material for the gas valve as claimed in claim 3, wherein the aging treatment is carried out at the temperature of 700-720 ℃ for 16h in air cooling treatment.
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Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114990385A (en) * | 2022-05-31 | 2022-09-02 | 上海康晟航材科技股份有限公司 | High-temperature alloy for turbine case of gas turbine and preparation method thereof |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101429608A (en) * | 2007-11-06 | 2009-05-13 | 江苏兴海特钢有限公司 | Heat-resistant alloy for exhaust valve and process for producing the same |
| CN104694783A (en) * | 2015-03-13 | 2015-06-10 | 江苏申源特钢有限公司 | Nickel-based air valve alloy and preparation method thereof |
| CN108796309A (en) * | 2018-08-15 | 2018-11-13 | 宝钢特钢有限公司 | A kind of engine valve nickel-base alloy and its manufacturing method |
-
2020
- 2020-01-14 CN CN202010035300.9A patent/CN113186430A/en active Pending
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101429608A (en) * | 2007-11-06 | 2009-05-13 | 江苏兴海特钢有限公司 | Heat-resistant alloy for exhaust valve and process for producing the same |
| CN104694783A (en) * | 2015-03-13 | 2015-06-10 | 江苏申源特钢有限公司 | Nickel-based air valve alloy and preparation method thereof |
| CN108796309A (en) * | 2018-08-15 | 2018-11-13 | 宝钢特钢有限公司 | A kind of engine valve nickel-base alloy and its manufacturing method |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114990385A (en) * | 2022-05-31 | 2022-09-02 | 上海康晟航材科技股份有限公司 | High-temperature alloy for turbine case of gas turbine and preparation method thereof |
| CN114990385B (en) * | 2022-05-31 | 2023-09-05 | 上海康晟航材科技股份有限公司 | High-temperature alloy for gas turbine casing and preparation method thereof |
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Application publication date: 20210730 |