CN110724885B - Preparation method of large-size light magnesium-aluminum-based amorphous alloy - Google Patents
Preparation method of large-size light magnesium-aluminum-based amorphous alloy Download PDFInfo
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Abstract
The invention belongs to the field of amorphous alloys, and particularly relates to a preparation method of a large-size light magnesium-aluminum-based amorphous alloy. Weighing powdery magnesium-based amorphous alloy and powdery aluminum-based amorphous alloy according to the proportion of the target alloy components, and uniformly mixing to obtain magnesium-aluminum-based amorphous alloy mixed powder; the supercooled liquid phase regions of the components of the magnesium-based amorphous alloy and the aluminum-based amorphous alloy are overlapped; the magnesium-aluminum based amorphous alloy is prepared by a powder sintering process or a laser additive manufacturing technology. The invention improves the room temperature plasticity of the magnesium-based amorphous alloy by using the aluminum-based amorphous as the toughening phase or improves the strength of the aluminum-based amorphous alloy by using the magnesium-based amorphous as the reinforcing phase, and prepares the large-size light high-strength magnesium-aluminum-based amorphous alloy by adopting a powder sintering process or a laser additive manufacturing technology, thereby solving the technical problems that the prepared composite material has low performance because the crystal second phase and the internal structure of the amorphous matrix have large difference, the deformation mode has large difference, and the interface metallurgical bonding is difficult to realize in the prior art.
Description
Technical Field
The invention belongs to the field of amorphous alloys, and particularly relates to a preparation method of a large-size light magnesium-aluminum-based amorphous alloy.
Background
The novel light high-strength material is widely applied to the fields of aerospace, automobile lightweight, national defense equipment, large-scale sea-crossing bridges, high-rise buildings and the like. The titanium, magnesium and aluminum are common light structural materials at present due to the abundant reserves, low density and good strength performance. The strength of the magnesium-based and aluminum-based amorphous alloy is 3-5 times that of the traditional magnesium alloy and aluminum alloy materials, and the magnesium-based and aluminum-based amorphous alloy has good corrosion resistance, wear resistance and high-temperature thermoplastic formability, and is a novel light high-strength structural material with application prospect. But the preparation of the amorphous alloy needs a faster cooling rate, the size and the shape of parts are greatly limited, meanwhile, the room temperature plasticity is generally poor, particularly, the magnesium-based amorphous alloy shows complete brittle fracture at room temperature, and great potential safety hazards exist in the actual service process. The aluminum-based amorphous alloy has relatively good room temperature plasticity, but has poor amorphous forming capability, the critical forming size is generally smaller than 1mm, the forming difficulty is high, and the application is difficult.
The limitations of the size and shape of the amorphous alloy component can be broken through to a certain extent by powder sintering and additive manufacturing, and the purpose of strengthening or toughening an amorphous matrix is achieved by adopting a crystalline material such as high-melting-point ceramic or metal as a second phase at present. The second phase of the crystal is greatly different from the internal structure of the amorphous matrix, the deformation mode is greatly different, the interface metallurgical bonding is difficult to realize, and the performance of the prepared composite material is not high.
Disclosure of Invention
Aiming at the defects or improvement requirements in the prior art, the invention provides a preparation method of a large-size light magnesium-aluminum-based amorphous alloy, which utilizes aluminum-based amorphous as a toughening phase to improve the room temperature plasticity of the magnesium-based amorphous alloy or utilizes the magnesium-based amorphous as a reinforcing phase to improve the strength of the aluminum-based amorphous, and adopts a powder sintering process or a laser additive manufacturing technology to prepare the large-size light high-strength magnesium-aluminum-based amorphous alloy, thereby solving the technical problems that the prepared composite material has low performance due to the fact that the crystal second phase is greatly different from the internal structure of a non-crystal matrix, the deformation mode is greatly different, and the interface metallurgical bonding is difficult to realize in the prior art.
In order to achieve the above object, according to an aspect of the present invention, there is provided a method for preparing a magnesium-aluminum based amorphous alloy, comprising the steps of:
(1) weighing powdery magnesium-based amorphous alloy and powdery aluminum-based amorphous alloy according to the proportion of the target alloy components, and uniformly mixing to obtain magnesium-aluminum-based amorphous alloy mixed powder; the supercooled liquid phase regions of the components of the magnesium-based amorphous alloy and the aluminum-based amorphous alloy are overlapped;
(2) and preparing the magnesium-aluminum-based amorphous alloy from the magnesium-aluminum-based amorphous alloy mixed powder by a powder sintering process or a laser additive manufacturing technology.
Preferably, the selection criteria of the magnesium-based amorphous alloy and the aluminum-based amorphous alloy in the step (1) are as follows: critical forming size of amorphous alloy componentLess than 0.1mm, difference delta T between upper limit and lower limit of supercooled liquid phase temperature rangexGreater than 20K and a thermoplastic forming ability index S > 0.15.
Preferably, the difference between the upper limit and the lower limit of the overlapping interval of the supercooled liquid region of the components of the magnesium-based amorphous alloy and the aluminum-based amorphous alloy is not less than 5K.
Preferably, the powdered magnesium-based amorphous alloy and aluminum-based amorphous alloy of step (1) are obtained by the following method: preparing the magnesium-based amorphous alloy and the aluminum-based amorphous alloy into amorphous alloy powder with micron-sized or nano-sized particle diameter by adopting an air atomization method, a mechanical ball milling method, a plasma ball milling method or a plasma rotating electrode method.
Preferably, the step (1) adopts ball milling to uniformly mix the powdery magnesium-based amorphous alloy and the powdery aluminum-based amorphous alloy; the technological parameters of the ball milling process are as follows: the grinding balls are made of hard alloy, stainless steel or agate, the rotating speed is 100-800 r/min, the ball-material ratio is 30: 1-3: 1, and the ball-milling time is 10 min-24 h.
Preferably, the temperature adopted in the powder sintering process in the step (2) is in an overlapping interval of supercooled liquid phase regions of the magnesium-based amorphous alloy and the aluminum-based amorphous alloy, the powder sintering temperature rise rate is 10K/min-500K/min, the powder sintering pressure is 30 MPa-5 GPa, sintering is carried out in a vacuum degree of less than 10Pa or in an inert gas protection environment, and the forming time is shorter than the minimum crystallization starting time of the magnesium-based amorphous alloy and the aluminum-based amorphous alloy at the adopted sintering temperature.
Preferably, the temperature adopted in the powder sintering process in the step (3) is within an overlapping interval of supercooled liquid phase regions of the magnesium-based amorphous alloy and the aluminum-based amorphous alloy, and is not lower than an intermediate temperature value of the overlapping interval, the particle size of the magnesium-aluminum-based amorphous alloy mixed powder is less than 1um, the powder sintering temperature rise rate is 10K/min-500K/min, the powder sintering pressure is more than 1GPa, and the vacuum degree is less than 1 × 10-4Pa or sintering in inert gas protection environment, and the forming time is shorter than the minimum crystallization starting time of the components of the magnesium-based amorphous alloy and the aluminum-based amorphous alloy at the adopted sintering temperature.
Preferably, the laser additive manufacturing process parameters in step (3) are as follows: the temperature of a laser melting pool is in an overlapping interval of supercooled liquid phase regions of magnesium-based amorphous alloy and aluminum-based amorphous alloy components, the laser power is 500W-20000W, the scanning speed is 60 mm/min-3000 mm/min, the laser spot diameter is 0.1 mm-5 mm, and additive manufacturing is carried out in a vacuum degree of less than 10Pa or in an inert gas protection environment; the forming time is shorter than the minimum crystallization starting time of the components of the magnesium-based amorphous alloy and the aluminum-based amorphous alloy at the adopted sintering temperature.
Preferably, the laser additive manufacturing process parameters in the step (3) are that the temperature of a laser melting pool is within an overlapping interval of supercooled liquid phase regions of the magnesium-based amorphous alloy and the aluminum-based amorphous alloy, and is not lower than an intermediate temperature value of the overlapping interval, the laser power is 500W-20000W, the scanning speed is 60 mm/min-3000 mm/min, the diameter of a laser spot is 0.1 mm-0.5 mm, and the vacuum degree is less than 1 × 10-4Pa or performing additive manufacturing in an inert gas protection environment; the particle size of the magnesium-aluminum-based amorphous alloy mixed powder is less than 1 um; the forming time is shorter than the minimum crystallization starting time of the components of the magnesium-based amorphous alloy and the aluminum-based amorphous alloy at the adopted sintering temperature.
In general, compared with the prior art, the above technical solution contemplated by the present invention can achieve the following beneficial effects:
(1) the invention provides a preparation method of a magnesium-aluminum based dual-phase amorphous composite material aiming at respective characteristics of magnesium-based and aluminum-based amorphous alloys, wherein aluminum-based amorphous is used as a toughening phase to improve room temperature plasticity of the magnesium-based amorphous alloy or the magnesium-based amorphous is used as a reinforcing phase to improve strength of the aluminum-based amorphous. Compared with the traditional mode of adopting crystal materials such as high-melting-point ceramics or metals and the like as the second phase, the structure of the two-phase amorphous phase is the same, the deformation mechanism is similar, the deformation coordination is better, the two phases are both in a supercooled liquid phase region during forming, the viscosity is lower, the atomic diffusion and movement capability are strong, the interface bonding strength is high, and the better reinforcing/toughening effect can be achieved. Meanwhile, the invention can realize the flexible design and preparation of the components of the light magnesium-aluminum-based amorphous alloy by adjusting the proportion of magnesium and aluminum.
(2) The invention can obtain the single-phase magnesium-aluminum-based amorphous composite material by controlling the powder sintering process parameters or the laser additive manufacturing process parameters, so the invention provides a novel amorphous alloy component design and preparation method, and particularly realizes the full kneading of two amorphous alloy components by utilizing the atom diffusion homogenization effect in the powder sintering process and the superplasticity of the amorphous alloy in a supercooled liquid region, thereby preparing the magnesium-aluminum-based amorphous alloy with a single amorphous phase. Compared with the traditional amorphous alloy component research and development mode, the method can realize the integration of flexible design, preparation and formation of the amorphous alloy components, simultaneously solves the problem of size and shape limitation of amorphous alloy preparation by using a powder sintering or additive manufacturing technology, and avoids the problems of component change and potential safety hazard caused by extremely easy volatilization and oxidation of magnesium during magnesium-aluminum-based amorphous smelting.
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FIG. 1 is a flow chart of a large-size light magnesium-aluminum-based amorphous alloy and a preparation method thereof.
Detailed Description
In order to make the objects, technical solutions and advantages of the present invention more apparent, the present invention is described in further detail below with reference to the accompanying drawings and embodiments. It should be understood that the specific embodiments described herein are merely illustrative of the invention and are not intended to limit the invention. In addition, the technical features involved in the embodiments of the present invention described below may be combined with each other as long as they do not conflict with each other.
The invention provides a preparation method of a large-size light magnesium-aluminum-based amorphous alloy, aiming at the application bottleneck of magnesium-based and aluminum-based amorphous alloys and the manufacturing requirement of novel light high-strength structural materials.
The preparation method of the magnesium-aluminum-based amorphous alloy, as shown in figure 1, comprises the following steps:
(1) weighing powdery magnesium-based amorphous alloy and powdery aluminum-based amorphous alloy according to the proportion of the target alloy components, and uniformly mixing to obtain magnesium-aluminum-based amorphous alloy mixed powder; the supercooled liquid phase regions of the components of the magnesium-based amorphous alloy and the aluminum-based amorphous alloy are overlapped;
(2) and preparing the magnesium-aluminum-based amorphous alloy from the magnesium-aluminum-based amorphous alloy mixed powder by a powder sintering process or a laser additive manufacturing technology.
According to the performance requirement of the target amorphous alloy, in order to obtain the magnesium-aluminum-based amorphous alloy with stronger amorphous forming capability, in some embodiments, the selection criteria of the magnesium-based amorphous alloy and the aluminum-based amorphous alloy in the step (1) are as follows: the critical forming size of the amorphous alloy components is not less than 0.1mm, and the difference delta T between the upper limit and the lower limit of the supercooled liquid phase temperature rangexGreater than 20K and a thermoplastic forming ability index S > 0.15. The supercooled liquid phase temperature interval is determined by the crystallization starting temperature T of the amorphous alloyxAnd glass transition temperature TgTemperature interval formed, in which crystallization initiation temperature TxAs the upper limit of the interval, the glass transition temperature TgAs the lower limit of this interval. The amorphous component can be selected by a theoretical criterion method, a high-throughput experiment method, an element substitution method, machine learning, neural network prediction and other methods.
The supercooled liquid regions of the two matrix amorphous alloy components should overlap to a certain extent, and in some preferred embodiments, the difference between the upper limit and the lower limit of the overlapping region of the supercooled liquid regions of the components of the magnesium-based amorphous alloy and the aluminum-based amorphous alloy is not less than 5K.
In the step (1) of the invention, the powder preparation technology can be adopted to obtain the micron-scale or nano-scale magnesium-based and aluminum-based amorphous alloy powder. In some embodiments, in the step (1), the magnesium-based amorphous alloy and the aluminum-based amorphous alloy are prepared into the amorphous alloy powder with the grain size of micron or nanometer by using an air atomization method, a mechanical ball milling method, a plasma ball milling method or a plasma rotating electrode method.
In the step (2), various powder mixing methods can be adopted to uniformly mix the magnesium-based amorphous alloy powder and the aluminum-based amorphous alloy powder. In some embodiments, step (2) employs a ball milling process to mix the two powders. The technological parameters of the ball milling process are as follows: the grinding balls are made of hard alloy, stainless steel or agate, the rotating speed is 100-800 r/min, the ball-material ratio is 30: 1-3: 1, and the ball-milling time is 10 min-24 h.
In some embodiments, in order to obtain large-size light high-strength magnesium-aluminum-based dual-phase or single-phase bulk amorphous alloy, the temperature adopted in the powder sintering process in the step (3) is within the overlapping interval of supercooled liquid phase regions of magnesium-based amorphous alloy and aluminum-based amorphous alloy components, the powder sintering temperature rise rate is 10-500K/min, the powder sintering pressure is 30-5 GPa, the vacuum degree is less than 10Pa or the powder sintering process is carried out in an inert gas protection environment, and the forming time is shorter than the minimum crystallization starting time of the magnesium-based amorphous alloy and the aluminum-based amorphous alloy components at the adopted sintering temperature.
For example, in some embodiments, the temperature adopted in the step (3) in the powder sintering process is controlled to be within an overlapping interval of supercooled liquid phase regions of the magnesium-based amorphous alloy and the aluminum-based amorphous alloy, and is not lower than an intermediate temperature value of the overlapping interval, the particle size of the magnesium-aluminum-based amorphous alloy mixed powder is less than 1um, the powder sintering temperature rise rate is 10K/min-500K/min, the powder sintering pressure is more than 1GPa, and the vacuum degree is less than 1 × 10-4Pa or in inert gas protection environment, and the forming time is shorter than the minimum crystallization starting time of the components of the magnesium-based amorphous alloy and the aluminum-based amorphous alloy at the adopted sintering temperature, so that the single amorphous phase magnesium-aluminum-based amorphous alloy is obtained.
In some embodiments, in order to obtain large-size light high-strength magnesium-aluminum-based dual-phase or single-phase bulk amorphous, the laser additive manufacturing process parameters in step (3) are as follows: the temperature of a laser melting pool is in an overlapping interval of supercooled liquid phase regions of the components of the magnesium-based amorphous alloy and the aluminum-based amorphous alloy, the laser power is 500W-20000W, the scanning speed is 60 mm/min-3000 mm/min, the laser spot diameter is 0.1 mm-5 mm, and the vacuum degree is less than 10Pa or the laser melting pool is carried out in an inert gas protection environment; the forming time is shorter than the minimum crystallization starting time of the components of the magnesium-based amorphous alloy and the aluminum-based amorphous alloy at the adopted sintering temperature.
For example, in some embodiments, the laser additive manufacturing process parameters of the step (3) are that the laser melting bath temperature is within the overlapping interval of the supercooled liquid phase regions of the magnesium-based amorphous alloy and the aluminum-based amorphous alloy, and is not lower than the intermediate temperature value of the overlapping interval, the laser power is 500W-20000W, the scanning speed is 60 mm/min-3000 mm/min, the laser spot diameter is 0.1 mm-0.5 mm, and the vacuum degree is less than 1 × 10- 4Pa or in an inert gas protective environment; the particle size of the magnesium-aluminum-based amorphous alloy mixed powder is less than 1 um; the forming time is shorter than the minimum crystallization starting time of the components of the magnesium-based amorphous alloy and the aluminum-based amorphous alloy at the adopted sintering temperature, and the single amorphous phase magnesium-aluminum-based amorphous alloy is obtained.
The magnesium-aluminum-based single-phase bulk amorphous alloy is an alloy system which takes magnesium and aluminum as main alloy components and has a single amorphous phase, the internal components of the alloy are uniform, and the concentration difference of macroscopic element components does not exist.
The magnesium-aluminum-based dual-phase bulk amorphous alloy is a composite material which takes one component as a matrix and the other component as a reinforcing phase or toughening phase, and has two characteristic amorphous diffraction peaks.
By adopting the preparation method of the magnesium-aluminum amorphous alloy, the room temperature plasticity of the magnesium-based amorphous alloy is improved by using the aluminum-based amorphous as a toughening phase or the strength of the aluminum-based amorphous is improved by using the magnesium-based amorphous as a reinforcing phase. Compared with the traditional mode of adopting crystal materials such as high-melting-point ceramics or metals and the like as the second phase, the structure of the two-phase amorphous phase is the same, the deformation mechanism is similar, the deformation coordination is better, the two phases are both in a supercooled liquid phase region during forming, the viscosity is lower, the atomic diffusion and movement capability are strong, the interface bonding strength is high, and the better reinforcing/toughening effect can be achieved.
On the other hand, the magnesium-aluminum-based amorphous alloy with a single amorphous phase is prepared by controlling the parameters of a powder sintering process or a laser additive manufacturing process and utilizing the atomic diffusion homogenization effect and the superplasticity of the amorphous alloy in a supercooled liquid region in the powder sintering process or the laser additive manufacturing process to realize the sufficient kneading of the two amorphous alloy components. Therefore, the preparation method of the magnesium-aluminum amorphous alloy provided by the invention can be regarded as a novel amorphous alloy component design and preparation method to a certain extent. The magnesium-aluminum based amorphous alloy with any target component can be obtained according to the requirement.
Compared with the traditional amorphous alloy component research and development mode, the method can realize the integration of flexible design, preparation and formation of the amorphous alloy components, simultaneously solves the problem of size and shape limitation of amorphous alloy preparation by using a powder sintering or additive manufacturing technology, and avoids the problems of component change and potential safety hazard caused by extremely easy volatilization and oxidation of magnesium during magnesium-aluminum-based amorphous smelting.
At present, the traditional casting method is adopted to prepare bulk Pd-based amorphous, and only cylinders with the diameter of about 80mm can be prepared at most. In addition, the amorphous forming ability of magnesium-based and aluminum-based amorphous alloys is not very good, and direct quenching by a casting method is difficult to exceed 10mm (cylindrical rod). By adopting the preparation method of the magnesium-aluminum-based single/double-phase amorphous alloy, on the basis of selecting magnesium-based and aluminum-based amorphous alloy components with stronger amorphous forming capability, the size of the magnesium-aluminum-based amorphous alloy prepared by the traditional casting method can be broken through by using powder sintering or additive manufacturing technology, for example, any two of the three-dimensional sizes of the magnesium-aluminum-based single/double-phase amorphous alloy obtained in some embodiments of the invention are larger than 10 mm.
Aiming at the application requirements of novel light high-strength structural materials, the invention provides a preparation method of a magnesium-aluminum-based single/double-phase amorphous alloy, and simultaneously provides a novel method for designing amorphous alloy components. The method comprises the steps of firstly, preferably selecting magnesium-based and aluminum-based amorphous alloy components with stronger amorphous forming capability, preparing amorphous powder with micron-sized or nano-sized particle size, weighing the powder according to the proportion of the final alloy components, uniformly ball-milling and mixing, and then sintering the powder to obtain the high-density bulk amorphous. By optimizing the sintering process parameters and utilizing the atom diffusion homogenization effect in the sintering process and the superplasticity of the amorphous alloy in the supercooled liquid phase region, the magnesium-aluminum-based double-amorphous-phase composite or single-phase amorphous material with good performance is obtained. The method can realize the flexible design and preparation of the components of the magnesium-aluminum-based amorphous alloy by adjusting the proportion of magnesium and aluminum, and simultaneously solves the problems that magnesium is extremely easy to volatilize and oxidize during the preparation and smelting of the magnesium-aluminum-based amorphous alloy.
The following are examples:
mg with stronger amorphous forming ability is preferably selected from developed amorphous alloy component library54Cu28Ag7Y11Magnesium-based amorphous alloy, Al87Ni3Y10The thermal physical property parameters of the aluminum-based amorphous alloy are shown in table 1. Mg (magnesium)54Cu28Ag7Y11The amorphous alloy has strong amorphous forming ability, the supercooled liquid phase temperature range reaches 70K, Al87Ni3Y10The supercooled liquid region of the amorphous alloy is 28K, the room-temperature breaking strength reaches 1140MPa, and the overlapped temperature range of the supercooled liquid regions of the two amorphous alloys reaches 10K.
TABLE 1 thermophysical properties of two amorphous alloy compositions
Weighing high-purity metal raw materials according to nominal components, preparing and screening magnesium-based and aluminum-based amorphous alloy powder with the particle size range of 100 nm-10 um by using a gas atomization technology, wherein the specific technological parameters are that the alloy superheat degree is 50-100 ℃, smelting is repeated for three times to obtain a master alloy ingot, the high-purity argon atomization pressure is 3.3MPa, the diameter of a diversion hole is 2mm, ball milling and mixing are uniform, and then hot-pressing sintering is adopted to prepare the magnesium-aluminum-based single/double-phase block amorphous alloy, the ball milling technological parameters comprise hard alloy grinding balls, the rotating speed is 300r/min, the ball-to-material ratio is 10: 1, the ball milling time is 2h, the hot-pressing sintering technological parameters comprise the temperature of 495K, the pressure of 600MPa, the time of 5min, the-3Pa. And (5) cooling the die quickly by water to obtain the block amorphous material.
Weighing high-purity metal raw materials according to nominal components, preparing and screening magnesium-based and aluminum-based amorphous alloy powder with the particle size of less than 1um by using a gas atomization technology, wherein the specific technological parameters are that the superheat degree of the alloy is 50-100 ℃, a master alloy ingot is obtained after three times of smelting, the high-purity argon atomization pressure is 3.3MPa, the diameter of a diversion hole is 1mm, ball milling and mixing are uniform, and then the magnesium-aluminum-based bulk amorphous alloy is prepared by adopting hot-pressing sintering, the ball milling technological parameters are that hard alloy grinding balls, the rotating speed is 300r/min, the ball-to-material ratio is 10: 1, the ball milling time is 2h, the hot-pressing sintering technological parameters are that the temperature is K, the pressure is 2.5GPa, the time is 5min, the heating rate is 50-3Pa, obtaining the single-phase bulk amorphous material.
It will be understood by those skilled in the art that the foregoing is only a preferred embodiment of the present invention, and is not intended to limit the invention, and that any modification, equivalent replacement, or improvement made within the spirit and principle of the present invention should be included in the scope of the present invention.
Claims (5)
1. The preparation method of the magnesium-aluminum-based amorphous alloy is characterized by comprising the following steps of:
(1) weighing powdery magnesium-based amorphous alloy and powdery aluminum-based amorphous alloy according to the proportion of the target alloy components, and uniformly mixing to obtain magnesium-aluminum-based amorphous alloy mixed powder; the supercooled liquid phase regions of the components of the magnesium-based amorphous alloy and the aluminum-based amorphous alloy are overlapped;
(2) preparing the magnesium-aluminum-based amorphous alloy mixed powder into magnesium-aluminum-based amorphous alloy by a powder sintering process or a laser additive manufacturing technology;
the selection standard of the magnesium-based amorphous alloy and the aluminum-based amorphous alloy in the step (1) is as follows: the critical forming size of the amorphous alloy components is not less than 0.1mm, and the difference delta T between the upper limit and the lower limit of the supercooled liquid phase temperature rangexMore than 20K, and the thermoplastic forming ability index S is more than 0.15;
the difference value between the upper limit and the lower limit of the overlapping interval of the supercooling liquid phase regions of the components of the magnesium-based amorphous alloy and the aluminum-based amorphous alloy is not less than 5K;
the temperature adopted by the powder sintering process in the step (2) is in an overlapping interval of supercooled liquid phase regions of the components of the magnesium-based amorphous alloy and the aluminum-based amorphous alloy, the temperature rise rate of powder sintering is 10K/min-500K/min, the powder sintering pressure is 30 MPa-5 GPa, sintering is carried out in a vacuum degree of less than 10Pa or in an inert gas protection environment, and the forming time is shorter than the minimum crystallization starting time of the components of the magnesium-based amorphous alloy and the aluminum-based amorphous alloy at the adopted sintering temperature;
the laser additive manufacturing process parameters in the step (2) are as follows: the temperature of a laser melting pool is in an overlapping interval of supercooled liquid phase regions of magnesium-based amorphous alloy and aluminum-based amorphous alloy components, the laser power is 500W-20000W, the scanning speed is 60 mm/min-3000 mm/min, the laser spot diameter is 0.1 mm-5 mm, and additive manufacturing is carried out in a vacuum degree of less than 10Pa or in an inert gas protection environment; the forming time is shorter than the minimum crystallization starting time of the components of the magnesium-based amorphous alloy and the aluminum-based amorphous alloy at the adopted sintering temperature.
2. The method according to claim 1, wherein the powdered magnesium-based amorphous alloy and aluminum-based amorphous alloy of step (1) are obtained by the following method: preparing the magnesium-based amorphous alloy and the aluminum-based amorphous alloy into amorphous alloy powder with micron-sized or nano-sized particle diameter by adopting an air atomization method, a mechanical ball milling method, a plasma ball milling method or a plasma rotating electrode method.
3. The preparation method according to claim 1, wherein the powdered magnesium-based amorphous alloy and the powdered aluminum-based amorphous alloy are uniformly mixed by ball milling in the step (1); the technological parameters of the ball milling process are as follows: the grinding balls are made of hard alloy, stainless steel or agate, the rotating speed is 100-800 r/min, the ball-material ratio is 30: 1-3: 1, and the ball-milling time is 10 min-24 h.
4. The method according to claim 1, wherein the powder sintering process of step (2) is performed at a temperature in an overlapping region of supercooled liquid regions of the components of the magnesium-based amorphous alloy and the aluminum-based amorphous alloyWithin the time and not lower than the intermediate temperature value of the overlapping interval, the grain diameter of the magnalium-based amorphous alloy mixed powder is less than 1 mu m, the powder sintering temperature rise rate is 10K/min to 500K/min, the powder sintering pressure is more than 1GPa, and the vacuum degree is less than 1 × 10-4Pa or sintering in inert gas protection environment, and the forming time is shorter than the minimum crystallization starting time of the components of the magnesium-based amorphous alloy and the aluminum-based amorphous alloy at the adopted sintering temperature.
5. The preparation method of claim 1, wherein the laser additive manufacturing process parameters in the step (2) are that the temperature of a laser melting pool is within an overlapping interval of supercooled liquid phase regions of the components of the Mg-based amorphous alloy and the Al-based amorphous alloy and is not lower than an intermediate temperature value of the overlapping interval, the laser power is 500W-20000W, the scanning speed is 60 mm/min-3000 mm/min, the diameter of a laser spot is 0.1 mm-0.5 mm, and the vacuum degree is less than 1 × 10-4Pa or performing additive manufacturing in an inert gas protection environment; the particle size of the magnesium-aluminum-based amorphous alloy mixed powder is less than 1 mu m; the forming time is shorter than the minimum crystallization starting time of the components of the magnesium-based amorphous alloy and the aluminum-based amorphous alloy at the adopted sintering temperature.
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| CN104117672B (en) * | 2014-07-31 | 2017-01-18 | 华中科技大学 | Method for preparing/forming amorphous alloy and composite material of amorphous alloy |
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| CN105803236B (en) * | 2016-03-24 | 2018-02-23 | 济南大学 | A kind of aluminum matrix composite of non-crystaline amorphous metal enhancing and preparation method thereof |
| CN109465442B (en) * | 2018-11-12 | 2019-10-25 | 华中科技大学 | A kind of forging of amorphous alloy part/increasing material composite manufacturing method |
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