CN114150241B - Heat treatment method for regulating microstructure of magnesium-gadolinium alloy - Google Patents
Heat treatment method for regulating microstructure of magnesium-gadolinium alloy Download PDFInfo
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Abstract
A heat treatment method for regulating and controlling a microstructure of a magnesium-gadolinium alloy belongs to the technical field of heat treatment, and comprises the following components of 6-15 wt.% of Gd, 0-5 wt.% of Zn, 0-5 wt.% of Er and 0.1-0.6 wt.% of Zr, wherein the mass percent of Zn/RE (Gd, Er) is 0.03-0.85, and the balance is magnesium. And carrying out alternate circulating cold and hot treatment of furnace temperature heat preservation and air cooling maintenance for many times. The alloy treated by the technology has excellent room temperature/high temperature mechanical property, and can be used in a plurality of advanced technical fields with higher requirements on alloy products.
Description
Technical Field
The invention relates to a heat treatment method for regulating and controlling the microstructure of an alloy, and the alloy treated by the technology has excellent room temperature/high temperature mechanical properties and can be used in a plurality of top-end technical fields with higher requirements on alloy products.
Background
At present, magnesium alloy is the third kind of metal structural material with the lowest density among metal structural materials developed after steel and aluminum alloy, and is called green engineering material of 21 century. Moreover, the magnesium resource is rich in China, the magnesium mineral reserves are the first world, the magnesium metal yields are the first world, and the use of magnesium and magnesium alloy products is more and more emphasized in China. The magnesium alloy is used in the field of industrial products, not only can reduce the weight of equipment, but also can reduce energy consumption and improve the operation efficiency of equipment. Therefore, magnesium alloy is one of the most potential metal materials for research and development.
However, the mechanical properties of magnesium and most magnesium alloys are not high, and cannot meet the use requirements of part of equipment. In order to improve the mechanical property of the alloy, an alloying method is often adopted to improve the mechanical property of the magnesium alloy, the improvement of the mechanical property of the magnesium alloy is mainly due to four strengthening effects of solid solution, precipitation, dispersion, fine grain and the like, wherein the second phase plays a main strengthening effect. At present, the main strengthening phases of the magnesium alloy are mainly generated in the second aging process, the types are more, the precipitation temperature range is generally between 100-250 ℃, metastable Mg-Zn, Mg-Al and Mg-RE which mainly have strengthening effects are equal, the phases are more reported at present, belong to the main strengthening phases commonly reported in the magnesium alloy, and have remarkable effect on improving the strength of the alloy. These precipitates can be defined as low temperature aged precipitates, which are essentially the predominant strengthening phases common in current magnesium alloys.
In addition, in addition to the above age-precipitated phases generated during the heat treatment, there are many second phases formed during solidification, such as a W phase (Mg) 3 Zn 3 RE 2 ) Phase I (Mg) 3 Zn 6 RE 1 )、Mg 5 RE、Mg 12 ZnRE、Mg 10 ZnRE and other coarse second phases, which are generally stable, need to be subjected to solution treatment under certain high-temperature conditions to be dissolved or converted into other second phases. Generally, W phase, Mg 10 ZnRE is relatively stable, and even at higher temperature (more than or equal to 500 ℃), dissolution is difficult to realize smoothly, and Mg 12 The ZnRE phase can be converted into Mg under certain conditions 10 A ZnRE phase.
The comparison shows that the heat treatment technology and the related alloy related in the patent have remarkable characteristics, and different types of second phases in the alloy can be desolventized and precipitated at high temperature through the technology and can be uniformly distributed; the newly generated second phase is different from the reported second phase, belongs to a high-temperature precipitated phase, has obvious advantages in improving the strength, particularly the high-temperature strength of the alloy, belongs to a high-temperature alloy material with excellent mechanical property, and can be used in a plurality of advanced technical fields with higher requirements on alloy products, such as aerospace and the like.
Disclosure of Invention
Aiming at the defect that the high-temperature mechanical property of the existing magnesium alloy is generally not high, the invention provides a heat treatment technology suitable for Mg-Gd-Er-Zn-Zr alloy, which can realize the regulation and control of different conventional second phases in the alloy, and can obtain an ideal second phase structure in the same alloy by controlling the technical parameters such as temperature, heat preservation time and the like, thereby realizing the improvement of the mechanical property of the alloy material at room temperature/high temperature.
In order to achieve the purpose, the invention adopts the following technical scheme:
a heat treatment method for regulating and controlling the microstructure of a magnesium-gadolinium alloy is characterized in that the magnesium-gadolinium alloy is subjected to multiple times of furnace temperature heat preservation-air cooling maintenance alternating cycle cold-heat treatment, namely furnace temperature heat preservation-air cooling maintenance-furnace temperature heat preservation-air cooling maintenance … …, and finally quenched; wherein the furnace temperature heat preservation-air cooling is kept as a cycle, the main parameters are the conditions of heat preservation temperature, heat preservation time, air cooling time and the like, wherein the furnace temperature constant temperature heat preservation temperature range of each time is 300-550 ℃, the furnace temperature heat preservation time is 5-100 h, and the air cooling time is 5-30 min; typically 1-5 cycles are performed.
When the cycle number n is more than 1, the heat preservation temperature of the next time is lower than the heat preservation temperature of the adjacent previous time, preferably lower by 15-25 ℃, the heat preservation time is 5-10 hours shorter than the heat preservation time of the adjacent previous time, and the air cooling time is kept unchanged.
The magnesium-gadolinium alloy comprises the following components of 6-15 wt.% of Gd, 0-5 wt.% of Zn, 0-5 wt.% of Er and 0.1-0.6 wt.% of Zr, wherein the mass percent of Zn/RE (total Gd and Er) is 0.03-0.85, and the balance is magnesium.
The microstructure can be effectively regulated, so that the second-phase morphology features can be divided into five types, alloys are divided into five types according to the second-phase morphology features, the first type is mainly alloy with a short rod-shaped phase, the second type is mainly alloy with a fine needle-shaped phase, the third type is mainly alloy with a massive multilayer structure phase, the fourth type is mainly alloy with a long rod-shaped phase, and the fifth type is mainly alloy with a point-shaped phase.
The invention is different from the reported low-temperature aging technology, the low-temperature aging technology is carried out at a lower temperature, and the types of the second phases are not changed abundantly, and only the second phases are converted from one phase (immature or metastable) to the other phase (more mature or stable); in the present application, the second phase is rich in variety, which can be as many as five, and there is no direct correlation between the phases and no mutual transformation or transition.
The massive multilayer structure phase in the alloy has a fine structure, the grain structure of the massive multilayer structure phase is between 5 and 20mm, the massive multilayer structure phase has high room temperature/high temperature mechanical property, the strength of the massive multilayer structure phase at room temperature can reach 200 to 450MPa, and the elongation is 10 to 25 percent; the strength can reach between 150 and 400MPa at the high temperature of between 150 and 350 ℃, and the elongation rate reaches more than 25 percent.
The invention has the substantive characteristics and remarkable progress that:
(1) a new heat treatment technology is developed, which is obviously different from the prior low-temperature aging treatment technology.
(2) The new technology has the technical characteristics of multiple cycles and cold-hot alternation, and can realize the diversified control of the type of the second phase in the alloy.
(3) The technique realizes the variety transformation of the second phase in the Mg-Gd-Er-Zn-Zr alloy, and can reach more than five types.
(4) The alloy obtained by the technology has excellent room temperature/high temperature mechanical properties.
(5) The technology can improve the mechanical property of the alloy, the strength of the alloy can reach 200-450 MPa at room temperature, and the elongation is 10-25%; the strength can reach between 150 and 400MPa at the high temperature of between 150 and 350 ℃, and the elongation rate reaches more than 25 percent.
Drawings
FIG. 1 is a diagram of a plurality of long, dry second phases in an alloy;
FIG. 2 is a view of a large number of short rod-like second phases in the alloy;
FIG. 3 is a view of a plurality of bulk multi-layer structural phases in the alloy;
FIG. 4 is a view of a large number of fine needle-like second phases in the alloy;
FIG. 5 is a view showing a large number of second phases dotted in the alloy.
Detailed Description
The present invention will be further illustrated with reference to the following examples, but the present invention is not limited to the following examples.
Example 1
The Mg-15Gd-5Er-5Zn-0.5Zr alloy is subjected to heat preservation for 100 hours at 550 ℃, then is subjected to air cooling for 30 minutes, and then is placed into a furnace for secondary heat preservation treatment, the heat preservation temperature is 525 ℃, the heat preservation time is 90 hours, and then is subjected to air cooling for 30 minutes, a large number of long rod-shaped phases are formed in the alloy, the room temperature strength of the alloy is 450MPa, the elongation is 25%, the strength of the alloy is 260MPa at 350 ℃, and the elongation is 35%.
Example 2
The Mg-15Gd-5Er-5Zn-0.2Zr alloy is subjected to heat preservation for 36 hours at the temperature of 550 ℃, then air cooling is carried out for 10 minutes, then the Mg-15Gd-5Er-5Zn-0.2Zr alloy is placed into a furnace to be subjected to heat preservation treatment for the second time, the heat preservation temperature is 525 ℃, the heat preservation time is 26 hours, then air cooling is carried out for 10 minutes, then heat preservation treatment for the third time is carried out, the heat preservation temperature is 510 ℃, the heat preservation time is 20 hours, a large amount of long rod-shaped phases are formed in the alloy (shown in figure 1), the room temperature strength of the alloy is 420MPa, the elongation is 21%, the strength of the alloy is 270MPa at the temperature of 350 ℃, and the elongation is 15%.
Example 3
The Mg-12Gd-1Er-1Zn-0.3Zr alloy is subjected to heat preservation for 10 hours at 500 ℃, then air-cooled for 10 minutes, then placed into a furnace for secondary heat preservation treatment, the heat preservation temperature is 475 ℃, the heat preservation time is 5 hours, then air-cooled for 10 minutes, the alloy contains a large amount of long rod-shaped phases, the room temperature strength of the alloy is 400MPa, the elongation is 18%, the strength of the alloy is 220MP at 250 ℃, and the elongation is 23%.
Example 4
The Mg-12Gd-1Er-1Zn-0.5Zr alloy is subjected to heat preservation for 36 hours at 515 ℃, then is subjected to air cooling for 15 minutes, and then is placed into a furnace for secondary heat preservation treatment, the heat preservation temperature is 500 ℃, the heat preservation time is 26 hours, and then is subjected to air cooling for 15 minutes, wherein the alloy contains a large number of long rod-shaped phases, the room temperature strength of the alloy is 430MPa, the elongation of the alloy is 15%, the strength of the alloy is 260MPa at 250 ℃, and the elongation of the alloy is 23%.
Example 5
The Mg-10Gd-2Er-3Zn-0.5Zr alloy is subjected to heat preservation for 8 hours at the temperature of 350 ℃, then air cooling is carried out for 10 minutes, then the Mg-10Gd-2Er-3Zn-0.5Zr alloy is placed into a furnace for secondary heat preservation treatment, the heat preservation temperature is 325 ℃, the heat preservation time is 3 hours, then air cooling is carried out for 10 minutes, the alloy contains a large number of short rod-shaped phases, the room temperature strength of the alloy is 280MPa, the elongation is 12%, the strength of the alloy is 180MPa at the temperature of 250 ℃, and the elongation is 25%.
Example 6
The Mg-8Gd-3Er-1Zn-0.1Zr alloy is subjected to heat preservation for 10 hours at the temperature of 400 ℃, then air-cooled for 10 minutes, then placed into a furnace for secondary heat preservation treatment, the heat preservation temperature is 385 ℃, the heat preservation time is 5 hours, then air-cooled for 15 minutes, the alloy contains a large number of short rod-shaped phases, the room-temperature strength of the alloy is 290MPa, the elongation is 10%, the strength at the temperature of 250 ℃ is 150MPa, and the elongation is 25%, and is shown in figure 2.
Example 7
The Mg-12Gd-1Er-1Zn-0.4Zr alloy is subjected to heat preservation for 24 hours at 515 ℃, then air-cooled for 10 minutes, then placed in a furnace for secondary heat preservation treatment, the heat preservation temperature is 490 ℃, the heat preservation time is 19 hours, then air-cooled for 10 minutes, the alloy contains a large amount of short rod-shaped phases, the room temperature strength of the alloy is 312MPa, the elongation is 8%, the strength of the alloy is 176MPa at 250 ℃, and the elongation is 12%.
Example 8
The Mg-8Gd-1Er-1Zn-0.2Zr alloy is subjected to heat preservation for 10 hours at the temperature of 325 ℃, then air-cooled for 5 minutes, then placed in a furnace for secondary heat preservation treatment, the heat preservation temperature is 310 ℃, the heat preservation time is 5 hours, then air-cooled for 5 minutes, the alloy contains a large number of short rod-shaped phases, the room temperature strength of the alloy is 260MPa, the elongation is 11%, the strength of the alloy is 140MPa at the temperature of 200 ℃, and the elongation is 30%.
Example 9
The Mg-12Gd-1Zn-4Er-0.5Zr alloy is kept warm for 24h at 515 ℃, then the alloy contains a large amount of long rod-shaped phases after air cooling for 5min, the room temperature strength of the alloy is 456MPa, the elongation is 9 percent, the strength of the alloy is 236MPa at 350 ℃, and the elongation is 17 percent.
Example 10
The Mg-12Gd-1Zn-0.5Zr alloy is kept warm for 26h at 500 ℃, then is air-cooled for 5min, and then is subjected to secondary heat preservation treatment, wherein the alloy at 475 ℃ contains a large amount of blocky multilayer structure phases, the strength of the alloy at room temperature is 386MPa, the elongation is 6%, the strength of the alloy at 200 ℃ is 167MPa, and the elongation is 19%, as shown in figure 3.
Example 11
The Mg-12Gd-1Zn-4Er-0.5Zr alloy is subjected to heat preservation at 475 ℃ for 16h, then air cooling is carried out for 15min, further secondary heat preservation treatment is carried out, the temperature is 450 ℃, the heat preservation time is 8h, the alloy contains a large number of fine needle-like phases, the strength of the alloy at room temperature is 396MPa, the elongation is 5%, the strength of the alloy at 200 ℃ is 198MPa, and the elongation is 13%, as shown in figure 4.
Example 12
The Mg-12Gd-1Zn-0.5Zr alloy is kept warm for 24h at 520 ℃ and then is air-cooled for 15min, the alloy contains a large amount of punctiform phases, the strength of the alloy at room temperature is 280MPa, the elongation is 12 percent, the strength of the alloy at 200 ℃ is 128MPa, and the elongation is 23 percent, as shown in figure 5.
Claims (1)
1. A heat treatment method for regulating and controlling the microstructure of a magnesium-gadolinium alloy is characterized in that the magnesium-gadolinium alloy is subjected to alternating cycle cold-heat treatment of furnace temperature heat preservation and air cooling maintenance for 1-5 times, namely furnace temperature heat preservation, air cooling maintenance, furnace temperature heat preservation and air cooling maintenance … …, and finally quenched; wherein the furnace temperature heat preservation-air cooling is kept as a cycle, the main parameters are the conditions of heat preservation temperature, heat preservation time, air cooling time and the like, wherein the furnace temperature constant temperature heat preservation temperature range of each time is 300-550 ℃, the furnace temperature heat preservation time is 5-100 h, and the air cooling time is 5-30 min;
the magnesium-gadolinium alloy comprises the following components of 6-15 wt.% of Gd, 1-5wt.% of Zn, 1-5wt.% of Er and 0.1-0.6 wt.% of Zr, wherein the mass percent of Zn/(the mass percent of Gd and the mass percent of Er) is within the range of 0.03-0.85, and the balance is magnesium;
effective regulation and control of microstructure are realized, so that the second-phase morphology features are divided into five types, alloys are divided into five types according to the second-phase morphology features, the first type is an alloy with a short rod-shaped phase as a main part, the second type is an alloy with a fine needle-shaped phase as a main part, the third type is an alloy with a massive multilayer structure phase as a main part, the fourth type is an alloy with a long rod-shaped phase as a main part, and the fifth type is an alloy with a point-shaped phase as a main part;
when the circulation frequency is more than 1, the heat preservation temperature of the next time is 15-25 ℃ lower than that of the previous time, the heat preservation time is 5-10h shorter than that of the previous time, and the air cooling time is kept unchanged.
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Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104178713A (en) * | 2014-07-17 | 2014-12-03 | 北京工业大学 | Regulation and preparation method of LPSO phase in Mg-Gd-Er-Zn-Zr alloy |
| CN107022707A (en) * | 2017-03-23 | 2017-08-08 | 中南大学 | A kind of big component Technology for Heating Processing of strong high temperature resistant magnesium alloy of superelevation |
| CN109112450A (en) * | 2018-09-07 | 2019-01-01 | 中国兵器科学研究院宁波分院 | A kind of heat resistance casting magnesium alloy material heat treatment method |
| CN110819863A (en) * | 2019-12-02 | 2020-02-21 | 北京工业大学 | Low-rare earth high-thermal conductivity magnesium alloy and preparation method thereof |
| CN112746208A (en) * | 2021-02-01 | 2021-05-04 | 太原理工大学 | Low-rare earth high-content high-toughness magnesium alloy and preparation method thereof |
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Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104178713A (en) * | 2014-07-17 | 2014-12-03 | 北京工业大学 | Regulation and preparation method of LPSO phase in Mg-Gd-Er-Zn-Zr alloy |
| CN107022707A (en) * | 2017-03-23 | 2017-08-08 | 中南大学 | A kind of big component Technology for Heating Processing of strong high temperature resistant magnesium alloy of superelevation |
| CN109112450A (en) * | 2018-09-07 | 2019-01-01 | 中国兵器科学研究院宁波分院 | A kind of heat resistance casting magnesium alloy material heat treatment method |
| CN110819863A (en) * | 2019-12-02 | 2020-02-21 | 北京工业大学 | Low-rare earth high-thermal conductivity magnesium alloy and preparation method thereof |
| CN112746208A (en) * | 2021-02-01 | 2021-05-04 | 太原理工大学 | Low-rare earth high-content high-toughness magnesium alloy and preparation method thereof |
Non-Patent Citations (1)
| Title |
|---|
| Cooling rate controlled basal precipitates and age hardening response of solid-soluted Mg-Gd-Er-Zn-Zr alloy;Jinlong Fu等;《Journal of Magnesium and Alloys》;20201017;第9卷;第1261-1271页 * |
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