CN113528877A - Method for preparing high-modulus high-strength magnesium-based composite material by selective laser melting technology - Google Patents

Method for preparing high-modulus high-strength magnesium-based composite material by selective laser melting technology Download PDF

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CN113528877A
CN113528877A CN202110825148.9A CN202110825148A CN113528877A CN 113528877 A CN113528877 A CN 113528877A CN 202110825148 A CN202110825148 A CN 202110825148A CN 113528877 A CN113528877 A CN 113528877A
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CN113528877B (en
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吴玉娟
武千业
邓庆琛
薛艳婷
陈凯
常治宇
宿宁
彭立明
丁文江
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Shanghai Jiaotong University
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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
    • C22C1/04—Making non-ferrous alloys by powder metallurgy
    • C22C1/0408—Light metal alloys
    • B—PERFORMING OPERATIONS; TRANSPORTING
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    • B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
    • B22F10/20—Direct sintering or melting
    • B22F10/28—Powder bed fusion, e.g. selective laser melting [SLM] or electron beam melting [EBM]
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B33—ADDITIVE MANUFACTURING TECHNOLOGY
    • B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C23/00—Alloys based on magnesium
    • C22C23/06—Alloys based on magnesium with a rare earth metal as the next major constituent
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    • 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
    • C22F1/06—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of magnesium or alloys based thereon
    • 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
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Abstract

The invention provides a method for preparing a high-modulus high-strength magnesium-based composite material by a selective laser melting technology, which comprises the following steps: A. preparing magnesium alloy spherical powder by a gas atomization method; B. carrying out physical premixing on magnesium alloy spherical powder and reinforcing phase powder; C. the premixed mixed powder is subjected to mechanical modification and fusion treatment, so that the surface of the magnesium alloy powder is coated with the reinforcing phase powder; D. c, drying the powder treated in the step C; E. and carrying out selective laser melting molding on the dried powder to obtain the high-modulus high-strength magnesium-based composite material. The invention regulates and controls the mechanical property of the alloy by a physical powder coating method, process parameters (laser power, scanning speed and scanning distance) for regulating and controlling selective laser melting and a subsequent heat treatment process, and prepares the high-modulus high-strength magnesium-based composite material by using the selective laser melting process for the first time.

Description

Method for preparing high-modulus high-strength magnesium-based composite material by selective laser melting technology
Technical Field
The invention relates to the technical field of non-ferrous metal alloy preparation, in particular to a method for preparing a high-modulus high-strength magnesium-based composite material by a selective laser melting technology.
Background
The density of magnesium metal is only 1.8g/cm3It is the lightest metal structural material. The magnesium alloy also has high specific strength, specific rigidity, shock absorption, recyclability, good heat conductivity and electrical conductivity and the like, is beneficial to industrial processing and forming, and is called as '21 st century green engineering metal'. Therefore, as one of engineering materials with excellent performance, the material is widely applied to the fields of military weapons, transportation, electronic communication, medical health and the like. However, the magnesium alloy has a low elastic modulus of only 45GPa, and the further expansion of the application of the magnesium alloy in the engineering field is greatly hindered by the defect that the requirement on rigidity of a new generation of engineering components is higher and higher. Under the condition that the alloy components are unchanged, the influence of the microstructure on the modulus is small, and the grain size has no obvious influence on the modulus. The modulus of the multi-phase alloy depends on the volume fraction and distribution of the second phase and can be calculated approximately as a weighted average of the volume proportions of the two-phase mixture. Studies with other alloys have shown that second phase particles with high modulus can increase the elastic modulus of the alloy. So that the group of the substrates is selectedAfter that, it is difficult to further achieve a large increase in the elastic modulus by a method of forming a continuous solid solution, but if a second phase having a high melting point is present in the alloy, it is possible to increase the elastic modulus greatly. Therefore, the magnesium-based composite material is prepared by adding the nano reinforcing phase into the magnesium alloy matrix, and the elastic modulus of the magnesium alloy can be effectively improved.
Compared with the traditional metal material, the metal-based composite material has excellent mechanical and physical properties and higher material design freedom, and is gradually a key subject of research of domestic and foreign material workers. After the aluminum-based composite material, the magnesium-based composite material is a competitive light metal-based composite material and has good application prospect in the fields of aerospace, automobiles, nuclear industry, electronic packaging and the like.
Selective Laser Melting (SLM) is currently the most widely used metal additive manufacturing technique. The SLM is used for directly forming a fully-compact metal part with good performance in one step by selectively and locally melting a metal powder bed and cladding and stacking layer by layer, and the product performance of the part exceeds that of a cast part. At present, the metal materials commonly used in SLM technology are: stainless steel, nickel-based alloys, titanium alloys, and the like. Compared with the traditional machining means, the SLM material increase manufacturing technology provides extremely high design freedom degree and optimization and integration of functional characteristics, can realize near-net shaping of high-complexity components, can produce small-batch products at a reasonable price, and can be applied to the fields of aerospace, biomedical treatment and the like in a larger range. With the continuous development of the aerospace industry, the requirements on the complexity and the performance of structural components are more and more stringent, the structural components of the aircraft are continuously developed towards the goals of light weight and integration, and meanwhile, the high reliability and the long service life are ensured.
At present, few studies on SLM forming manufacturing of magnesium-based composite materials at home and abroad are reported. The magnesium-based composite material with high elastic modulus is expected to be developed, and theoretical support is provided for magnesium alloy parts in the fields of aerospace, automobiles and the like.
The inventor's prior patent document CN110681869A describes a method for preparing high-toughness magnesium rare earth alloy by selective laser melting additive manufacturing technology, but the magnesium alloy prepared by the method has poor elastic modulus.
Disclosure of Invention
The invention aims to fill the blank of the preparation field of the selective laser melting manufacturing technology of the existing high-modulus high-strength magnesium-based composite material, and provides a method for preparing the high-modulus high-strength magnesium-based composite material by the selective laser melting manufacturing technology.
The purpose of the invention is realized by the following technical scheme:
the invention provides a method for preparing a high-modulus high-strength magnesium-based composite material by a selective laser melting technology, which comprises the following steps:
A. preparing magnesium alloy spherical powder by a gas atomization method;
B. carrying out physical premixing on magnesium alloy spherical powder and reinforcing phase powder;
C. the premixed mixed powder is subjected to mechanical modification and fusion treatment, so that the surface of the magnesium alloy powder is coated with the reinforcing phase powder;
D. c, drying the powder treated in the step C;
E. carrying out selective laser melting molding on the dried powder to obtain a high-modulus high-strength magnesium-based composite material;
in step B, the reinforcing phase is selected from W, Co and TiB2、Ti3N4、MgO、ZrO2At least one of;
in the step C, the mechanical modification fusion treatment adopts the following specific parameters: the power is 1.5-2.0 kw, the current is 8-9.8A, and the rotation speed is 1400-2000 rpm.
Preferably, the mixing time for the mechanical modification fusion treatment is more than 2 minutes; more preferably, the mixing time is 10 to 30 min.
Preferably, in the step A, the magnesium alloy is Mg-Gd (Y) -Zn-Zr/Mn alloy, and comprises the following elements in percentage by weight: gd: 5-20 wt.%; y: 0-5 wt.%; zn: 0-5 wt.%; mn: 0-2 wt.%; zr: 0-2 wt.%; less than 0.02% total impurities; the balance being Mg.
Preferably, the magnesium alloy comprises the following elements in percentage by weight: gd: 10-15 wt.%; y: 0-3 wt.%; zn: 0.75-1 wt.%; mn: 0-0.5 wt.%; zr: 0-0.4 wt.%; and (3) reinforcing phase: 0.1-15 wt.%; less than 0.02% total impurities; the balance being Mg.
More preferably, the magnesium alloy includes at least one of Mg-10Gd-3Y-1Zn-0.4Zr, Mg-11Gd-2Y-1Zn-0.5Mn, Mg-14.41Gd-0.75Zn-0.36Zr, but is not limited thereto. Most preferably, the magnesium alloy is Mg-11Gd-2Y-1Zn-0.5 Mn.
Preferably, the reinforcing phase powder is a nano reinforcing phase powder, and the content of the reinforcing phase in the prepared high-modulus high-strength magnesium-based composite material is 0.1-15 wt.%, more preferably 1-5 wt.%, and most preferably 2.5-5 wt.%.
Preferably, the reinforcing phase is selected from Co, TiB2、Ti3N4At least one of; more preferably TiB2、Ti3N4At least one of (1).
Preferably, in the step B, a three-dimensional mixer is adopted for physical premixing, and the premixing time is 4-24 hours.
Preferably, in the step D, the drying treatment is carried out under vacuum, the drying temperature is 140-180 ℃, and the drying time is 1-2 hours.
Preferably, in the step E, when the selective laser melting molding is performed, preheating is performed before printing, and the preheating temperature is 100-200 ℃.
Preferably, in the step E, when the selective laser melting molding is performed, the printing parameters adopted are as follows: the power is 80-160 w, the scanning distance is 50-100 mu m, the scanning speed is 400-1200 mm/s, the laser scanning strategy is a strip scanning strategy, the width of each strip is 5-10mm, and the interlayer rotation angle is 80-90 degrees.
Preferably, the method further comprises the step of subjecting the high modulus, high strength magnesium-based composite prepared in step E to solution and/or aging treatment.
Preferably, the conditions of the solution treatment are: the solid solution temperature is 380-525 ℃, and the time is 0.5-12 h; quenching is carried out after the solution treatment, and the quenching temperature is 25-100 ℃.
The aging treatment conditions are as follows: the aging temperature is 175-225 ℃, and the time is 0-512 h.
The invention also provides a high-modulus high-strength magnesium-based composite material prepared by the method, which comprises the following elements in percentage by weight: gd: 5-20 wt.%; y: 0-5 wt.%; zn: 0-5 wt.%; mn: 0-2 wt.%; zr: 0-2 wt.%; and (3) reinforcing phase: 0.1-15 wt.%; less than 0.02% total impurities; the balance being Mg;
the reinforcing phase is selected from W, Co and TiB2、Ti3N4、MgO、ZrO2At least one of (1).
Preferably, the reinforcing phase is present in an amount of 1 to 5 wt.%, most preferably in an amount of 2.5 to 5 wt.%.
Preferably, the reinforcing phase is selected from Co, TiB2、Ti3N4At least one of; more preferably TiB2、Ti3N4At least one of (1).
Preferably, the magnesium alloy comprises the following elements in percentage by weight: gd: 10-15 wt.%; y: 0-3 wt.%; zn: 0.75-1 wt.%; mn: 0-0.5 wt.%; zr: 0-0.4 wt.%; and (3) reinforcing phase: 0.1-15 wt.%; less than 0.02% total impurities; the balance being Mg.
Compared with the prior art, the invention has the following beneficial effects:
1. according to the high-modulus high-strength magnesium-based composite material prepared by the invention, the nano reinforcing phase particles can be uniformly coated on the surface of Mg-Gd (Y) -Zn-Zr/Mn alloy powder by using the mechanical modification fusion machine, the nano reinforcing phase can be uniformly distributed in the magnesium alloy matrix in the selective laser melting forming process, and the elastic modulus of the SLM magnesium-based composite material can be improved to be as high as 60 GPa.
2. The SLM-state magnesium alloy sample prepared by the invention has good mechanical properties, such as: mg-14.41Gd-0.75Zn-0.36Zr-3.5TiB2(wt.%) the room-temperature tensile strength of the alloy in the SLM state is 331MPa, and the elastic modulus can reach 60 GPa; the SLM-state room-temperature tensile strength of the Mg-11.19Gd-1.73Y-1.07Zn-0.53Zr-2.5Co (wt.%) alloy is 333MPa, and the elastic modulus can reach 50 GPa.
3. After the SLM-state magnesium alloy sample prepared by the invention is subjected to aging treatment directly, the material strength is greatly improved, such as Mg-14.41Gd-0.75Zn-0.36Zr-3.5TiB2(wt.%) the elastic modulus of the alloy can reach 60GPa, the tensile strength at room temperature in the T5 state is 372MPa, and compared with the SLM state, the tensile strength in the SLM-T5 state is respectively improved by 12%.
4. After the SLM-state sample prepared by the invention is subjected to solid solution and aging treatment, the material strength is greatly improved, such as Mg-14.41Gd-0.75Zn-0.36Zr-3.5TiB2(wt.%) the room temperature tensile strength of the alloy in the T6 state was 386MPa, which was a 17% improvement in tensile strength in the T6 state over the SLM state, respectively.
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 shows Mg-10Gd-3Y-1Zn-0.4Zr-2.5Ti prepared using a mechanically modified fusion machine in example 1 of the present invention3N4(wt.%) energy spectrum of the mixed powder, wherein fig. 1(a) is N element, fig. 1(b) is Ti element;
FIG. 2 shows SLM state Mg-10Gd-3Y-1Zn-0.4Zr-2.5Ti prepared in example 1 of the present invention3N4(wt.%) TEM micrograph of magnesium-based composite.
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.
Example 1:
the embodiment provides a high-modulus high-strength magnesium-based composite material and a preparation method thereof, and the preparation method specifically comprises the following steps:
1) the high-modulus high-strength magnesium-based composite material comprises the following components in percentage by mass: gd: 10 wt.%; y: 3 wt.%; zn: 1 wt.%; zr: 0.4 wt.%, naRice reinforcing phase: ti3N4: 2.5 wt.%; the balance being Mg and unavoidable impurities.
2) Preparing Mg-10Gd-3Y-1Zn-0.4Zr (wt.%) magnesium alloy spherical powder by a conventional gas atomization method; then Mg-10Gd-3Y-1Zn-0.4Zr (wt.%) magnesium alloy powder and nano-grade Ti with the mass fraction of 2.5 wt.%3N4Mixing the powder, and physically premixing for 10 hours by using a three-dimensional mixer;
3) carrying out mechanical modification and fusion treatment on the obtained premixed powder by using a mechanical modification and fusion machine to enable the surface of the magnesium alloy powder to be coated with the reinforcing phase powder; the power of the mechanical modification fusion machine is 1.7kw, the current is 9.0A, the rotating speed is 1500rpm, and the powder mixing time is 20 min;
4) mixing the powder obtained in the step 3) (prepared Mg-10Gd-3Y-1Zn-0.4Zr-2.5 Ti)3N4(wt.%) energy spectrum of the mixed powder is shown in fig. 1) is dried at 150 ℃ for 2 h;
5) filling the dried mixed powder into a powder bed of SLM printing equipment, and introducing inert gas into a cavity of the equipment for protection until the oxygen content is reduced to 50 ppm; the substrate was heated to 100 ℃ and pre-heated before printing was started. The specific parameters of selective laser melting molding are as follows: the laser power is 160W, the scanning speed is 1200mm/s, the molten pool interval is 50 μm, the scanning strategy is a strip scanning strategy, the width of a zonal strip is 5mm, and the interlayer rotation angle is 85 degrees.
6) Carrying out artificial aging T5 treatment on the magnesium alloy in the T4 state prepared in the 5) in a constant-temperature oil bath furnace, and adopting single-step aging treatment: the aging temperature is 200 ℃ and the time is 32h, and then the magnesium alloy is quenched in cold water at 25 ℃ to obtain the magnesium alloy in the T5 state.
The SLM-state magnesium alloy (shown in a TEM structural diagram in FIG. 2) prepared by the embodiment has an elastic modulus of 55GPa at room temperature, a tensile strength of 327MPa and a tensile strength of 362MPa at room temperature of the T5-state magnesium alloy.
Example 2:
the embodiment provides a high-modulus high-strength magnesium-based composite material and a preparation method thereof, and the preparation method specifically comprises the following steps:
1) the high-modulus high-strength magnesium-based composite material comprises the following components in percentage by mass: gd: 10 wt.%; y: 3 wt.%; zn: 1 wt.%; zr: 0.4 wt.%, nanoreinforcement phase Co: 2.5 wt.%; the balance being Mg and unavoidable impurities.
2) Preparing Mg-10Gd-3Y-1Zn-0.4Zr (wt.%) magnesium alloy spherical powder by a conventional gas atomization method; then mixing Mg-10Gd-3Y-1Zn-0.4Zr (wt.%) magnesium alloy powder with nano-grade Co powder with the mass fraction of 2.5 wt.%, and carrying out physical premixing for 10 hours by using a three-dimensional mixer;
3) carrying out mechanical modification and fusion treatment on the obtained premixed powder by using a mechanical modification and fusion machine to enable the surface of the magnesium alloy powder to be coated with the reinforcing phase powder; the power of the mechanical modification fusion machine is 1.7kw, the current is 9.0A, the rotating speed is 1500rpm, and the powder mixing time is 20 min;
4) drying the mixed powder in the step 3) at 150 ℃ for 2 h;
5) filling the dried mixed powder into a powder bed of SLM printing equipment, and introducing inert gas into a cavity of the equipment for protection until the oxygen content is reduced to 50 ppm; the substrate was heated to 100 ℃ and pre-heated before printing was started. The specific parameters of selective laser melting molding are as follows: the laser power is 160W, the scanning speed is 1200mm/s, the molten pool interval is 50 μm, the scanning strategy is a strip scanning strategy, the width of a zonal strip is 5mm, and the interlayer rotation angle is 85 degrees.
6) Carrying out artificial aging T5 treatment on the magnesium alloy in the T4 state prepared in the 5) in a constant-temperature oil bath furnace, and adopting single-step aging treatment: the aging temperature is 200 ℃ and the time is 32h, and then the magnesium alloy is quenched in cold water at 25 ℃ to obtain the magnesium alloy in the T5 state.
The SLM-state magnesium alloy prepared by the embodiment has the elasticity modulus of 54GPa at room temperature, the tensile strength of 319MPa and the room-temperature tensile strength of 350 MPa.
Example 3:
the embodiment provides a high-modulus high-strength magnesium-based composite material and a preparation method thereof, and the preparation method specifically comprises the following steps:
1) the high-modulus high-strength magnesium-based composite material comprises the following components in percentage by mass: gd: 10 wt.%; y: 3 wt.%; zn: 1 wt.%; zr: 0.4 wt.%, nanoreinforcement phase Co: 5 wt.%; the balance being Mg and unavoidable impurities.
2) Preparing Mg-10Gd-3Y-1Zn-0.4Zr (wt.%) magnesium alloy spherical powder by a conventional gas atomization method; then mixing Mg-10Gd-3Y-1Zn-0.4Zr (wt.%) magnesium alloy powder with nano-grade Co powder with the mass fraction of 5 wt.%, and carrying out physical premixing for 10 hours by using a three-dimensional mixer;
3) carrying out mechanical modification and fusion treatment on the obtained premixed powder by using a mechanical modification and fusion machine to enable the surface of the magnesium alloy powder to be coated with the reinforcing phase powder; the power of the mechanical modification fusion machine is 1.7kw, the current is 9.0A, the rotating speed is 1500rpm, and the powder mixing time is 20 min;
4) drying the mixed powder in the step 3) at 150 ℃ for 2 h;
5) filling the dried mixed powder into a powder bed of SLM printing equipment, and introducing inert gas into a cavity of the equipment for protection until the oxygen content is reduced to 50 ppm; the substrate was heated to 100 ℃ and pre-heated before printing was started. The specific parameters of selective laser melting molding are as follows: the laser power is 160W, the scanning speed is 1200mm/s, the molten pool interval is 50 μm, the scanning strategy is a strip scanning strategy, the width of a zonal strip is 5mm, and the interlayer rotation angle is 85 degrees.
6) Carrying out artificial aging T5 treatment on the magnesium alloy in the T4 state prepared in the 5) in a constant-temperature oil bath furnace, and adopting single-step aging treatment: the aging temperature is 200 ℃ and the time is 32h, and then the magnesium alloy is quenched in cold water at 25 ℃ to obtain the magnesium alloy in the T5 state.
The SLM-state magnesium alloy prepared by the embodiment has the elasticity modulus of 60GPa at room temperature, the tensile strength of 334MPa and the room-temperature tensile strength of 358 MPa.
Example 4:
the embodiment provides a high-modulus high-strength magnesium-based composite material and a preparation method thereof, and the preparation method specifically comprises the following steps:
1) the high-modulus high-strength magnesium-based composite material comprises the following components in percentage by mass: gd: 11 wt.%; y: 2 wt.%; zn: 1 wt.%; mn: 0.5 wt.%, nanoreinforcement phase Co: 2.5 wt.%; the balance being Mg and unavoidable impurities.
2) Preparing Mg-11Gd-2Y-1Zn-0.5Mn (wt.%) magnesium alloy spherical powder by a conventional gas atomization method; then mixing Mg-11Gd-2Y-1Zn-0.5Mn (wt.%) magnesium alloy powder with 2.5 wt.% nanoscale Co powder, and physically premixing for 10 hours by using a three-dimensional mixer;
3) carrying out mechanical modification and fusion treatment on the obtained premixed powder by using a mechanical modification and fusion machine to enable the surface of the magnesium alloy powder to be coated with the reinforcing phase powder; the power of the mechanical modification fusion machine is 1.7kw, the current is 9.0A, the rotating speed is 1500rpm, and the powder mixing time is 20 min;
4) drying the mixed powder in the step 3) at 150 ℃ for 2 h;
5) filling the dried mixed powder into a powder bed of SLM printing equipment, and introducing inert gas into a cavity of the equipment for protection until the oxygen content is reduced to 50 ppm; the substrate was heated to 100 ℃ and pre-heated before printing was started. The specific parameters of selective laser melting molding are as follows: the laser power is 160W, the scanning speed is 1200mm/s, the molten pool interval is 50 μm, the scanning strategy is a strip scanning strategy, the width of a zonal strip is 5mm, and the interlayer rotation angle is 85 degrees.
6) Carrying out artificial aging T5 treatment on the SLM-state magnesium alloy prepared in the step 5) in a constant-temperature oil bath furnace, and adopting single-step aging treatment: the aging temperature is 200 ℃ and the time is 32h, and then the magnesium alloy is quenched in cold water at 25 ℃ to obtain the magnesium alloy in the T5 state.
The SLM-state magnesium alloy prepared by the embodiment has the elasticity modulus of 55GPa at room temperature, the tensile strength of 313MPa, and the room-temperature tensile strength of 342 MPa.
Example 5:
the embodiment provides a high-modulus high-strength magnesium-based composite material and a preparation method thereof, and the preparation method specifically comprises the following steps:
1) the high-modulus high-strength magnesium-based composite material comprises the following components in percentage by mass: gd: 11 wt.%; y: 2 wt.%; zn: 1 wt.%; mn: 0.5 wt.%, nanoreinforcement phase Co: 2.5 wt.%; the balance being Mg and unavoidable impurities.
2) Preparing Mg-11Gd-2Y-1Zn-0.5Mn (wt.%) magnesium alloy spherical powder by a conventional gas atomization method; then mixing Mg-11Gd-2Y-1Zn-0.5Mn (wt.%) magnesium alloy powder with 2.5 wt.% nanoscale Co powder, and physically premixing for 10 hours by using a three-dimensional mixer;
3) carrying out mechanical modification and fusion treatment on the obtained premixed powder by using a mechanical modification and fusion machine to enable the surface of the magnesium alloy powder to be coated with the reinforcing phase powder; the power of the mechanical modification fusion machine is 1.7kw, the current is 9.0A, the rotating speed is 1500rpm, and the powder mixing time is 20 min;
4) drying the mixed powder in the step 3) at 150 ℃ for 2 h;
5) filling the dried mixed powder into a powder bed of SLM printing equipment, and introducing inert gas into a cavity of the equipment for protection until the oxygen content is reduced to 50 ppm; the substrate was heated to 100 ℃ and pre-heated before printing was started. The specific parameters of selective laser melting molding are as follows: the laser power is 160W, the scanning speed is 1200mm/s, the molten pool interval is 50 μm, the scanning strategy is a strip scanning strategy, the width of a zonal strip is 5mm, and the interlayer rotation angle is 85 degrees.
6) Carrying out solution treatment on the SLM-state magnesium alloy prepared in the step 5): in an air resistance furnace: keeping the temperature at 480 ℃ for 4h, and then quenching in hot water at 90 ℃;
7) carrying out subsequent aging T6 treatment on the magnesium alloy in the T4 state prepared in the 6) in a constant-temperature oil bath furnace, and adopting single-step aging treatment: the aging temperature is 200 ℃ and the time is 32h, and then the magnesium alloy is quenched in cold water at 25 ℃ to obtain the magnesium alloy in the T6 state.
The SLM-state magnesium alloy prepared by the embodiment has the elasticity modulus of 55GPa at room temperature, the tensile strength of 313MPa, and the room-temperature tensile strength of the T6-state magnesium alloy of 368 MPa.
Example 6:
the embodiment provides a high-modulus high-strength magnesium-based composite material and a preparation method thereof, and the preparation method specifically comprises the following steps:
1) the high-modulus high-strength magnesium-based composite material comprises the following components in percentage by mass: gd: 11 wt.%; y: 2 wt.%; zn: 1 wt.%; mn: 0.5 wt.%, nanoreinforcement phase Co: 5 wt.%; the balance being Mg and unavoidable impurities.
2) Preparing Mg-11Gd-2Y-1Zn-0.5Mn (wt.%) magnesium alloy spherical powder by a conventional gas atomization method; then mixing Mg-11Gd-2Y-1Zn-0.5Mn (wt.%) magnesium alloy powder with nano-grade Co powder with the mass fraction of 5 wt.%, and carrying out physical premixing for 10 hours by using a three-dimensional mixer;
3) carrying out mechanical modification and fusion treatment on the obtained premixed powder by using a mechanical modification and fusion machine to enable the surface of the magnesium alloy powder to be coated with the reinforcing phase powder; the power of the mechanical modification fusion machine is 1.7kw, the current is 9.0A, the rotating speed is 1500rpm, and the powder mixing time is 20 min;
4) drying the mixed powder in the step 3) at 150 ℃ for 2 h;
5) filling the dried mixed powder into a powder bed of SLM printing equipment, and introducing inert gas into a cavity of the equipment for protection until the oxygen content is reduced to 50 ppm; the substrate was heated to 100 ℃ and pre-heated before printing was started. The specific parameters of selective laser melting molding are as follows: the laser power is 160W, the scanning speed is 1200mm/s, the molten pool interval is 50 μm, the scanning strategy is a strip scanning strategy, the width of a zonal strip is 5mm, and the interlayer rotation angle is 85 degrees.
6) Carrying out artificial aging T5 treatment on the SLM-state magnesium alloy prepared in the step 5) in a constant-temperature oil bath furnace, and adopting single-step aging treatment: the aging temperature is 200 ℃ and the time is 32h, and then the magnesium alloy is quenched in cold water at 25 ℃ to obtain the magnesium alloy in the T5 state.
The SLM-state magnesium alloy prepared by the embodiment has the elasticity modulus of 60GPa at room temperature, the tensile strength of 333MPa, and the tensile strength of 380MPa at room temperature of T5-state magnesium alloy.
Example 7:
the embodiment provides a high-modulus high-strength magnesium-based composite material and a preparation method thereof, and the preparation method specifically comprises the following steps:
1) the high-modulus high-strength magnesium-based composite material comprises the following components in percentage by mass: gd: 14.41 wt.%; zn: 0.75 wt.%; zr: 0.36 wt.%, nanoenhanced phase TiB2: 3.5 wt.%; the balance being Mg and unavoidable impurities.
2) Prepared by a conventional gas atomization methodMg-14.41Gd-0.75Zn-0.36Zr (wt.%) magnesium alloy spherical powder; then Mg-14.41Gd-0.75Zn-0.36Zr (wt.%) magnesium alloy powder and nano-TiB with the mass fraction of 3.5 wt.%2Mixing the powder, and physically premixing for 10 hours by using a three-dimensional mixer;
3) carrying out mechanical modification and fusion treatment on the obtained premixed powder by using a mechanical modification and fusion machine to enable the surface of the magnesium alloy powder to be coated with the reinforcing phase powder; the power of the mechanical modification fusion machine is 1.7kw, the current is 9.0A, the rotating speed is 1500rpm, and the powder mixing time is 20 min;
4) drying the mixed powder in the step 3) at 150 ℃ for 2 h;
5) filling the dried mixed powder into a powder bed of SLM printing equipment, and introducing inert gas into a cavity of the equipment for protection until the oxygen content is reduced to 50 ppm; the substrate was heated to 100 ℃ and pre-heated before printing was started. The specific parameters of selective laser melting molding are as follows: the laser power is 160W, the scanning speed is 1200mm/s, the molten pool interval is 50 μm, the scanning strategy is a strip scanning strategy, the width of a zonal strip is 5mm, and the interlayer rotation angle is 85 degrees.
6) Carrying out artificial aging T5 treatment on the SLM-state magnesium alloy prepared in the step 5) in a constant-temperature oil bath furnace, and adopting single-step aging treatment: the aging temperature is 200 ℃ and the time is 32h, and then the magnesium alloy is quenched in cold water at 25 ℃ to obtain the magnesium alloy in the T5 state.
The SLM-state magnesium alloy prepared by the embodiment has the elasticity modulus of 58GPa at room temperature, the tensile strength of 331MPa, and the tensile strength of 379MPa at room temperature of the T5-state magnesium alloy.
Example 8:
the embodiment provides a high-modulus high-strength magnesium-based composite material and a preparation method thereof, and the preparation method specifically comprises the following steps:
1) the high-modulus high-strength magnesium-based composite material comprises the following components in percentage by mass: gd: 14.41 wt.%; zn: 0.75 wt.%; zr: 0.36 wt.%, nanoenhanced phase TiB2: 3.5 wt.%; the balance being Mg and unavoidable impurities.
2) Preparing Mg-14.41Gd-0.75Zn-0.36Zr (wt.%) magnesium alloy spherical powder by a conventional gas atomization method;then Mg-14.41Gd-0.75Zn-0.36Zr (wt.%) magnesium alloy powder and nano-TiB with the mass fraction of 3.5 wt.%2Mixing the powder, and physically premixing for 10 hours by using a three-dimensional mixer;
3) carrying out mechanical modification and fusion treatment on the obtained premixed powder by using a mechanical modification and fusion machine to enable the surface of the magnesium alloy powder to be coated with the reinforcing phase powder; the power of the mechanical modification fusion machine is 1.7kw, the current is 9.0A, the rotating speed is 1500rpm, and the powder mixing time is 20 min;
4) drying the mixed powder in the step 3) at 150 ℃ for 2 h;
5) filling the dried mixed powder into a powder bed of SLM printing equipment, and introducing inert gas into a cavity of the equipment for protection until the oxygen content is reduced to 50 ppm; the substrate was heated to 100 ℃ and pre-heated before printing was started. The specific parameters of selective laser melting molding are as follows: the laser power is 160W, the scanning speed is 1200mm/s, the molten pool interval is 50 μm, the scanning strategy is a strip scanning strategy, the width of a zonal strip is 5mm, and the interlayer rotation angle is 85 degrees.
6) Carrying out solution treatment on the SLM-state magnesium alloy prepared in the step 5): in an air resistance furnace: keeping the temperature at 480 ℃ for 4h, and then quenching in hot water at 90 ℃;
7) carrying out subsequent aging T6 treatment on the magnesium alloy in the T4 state prepared in the 6) in a constant-temperature oil bath furnace, and adopting single-step aging treatment: the aging temperature is 200 ℃ and the time is 32h, and then the magnesium alloy is quenched in cold water at 25 ℃ to obtain the magnesium alloy in the T6 state.
The SLM-state magnesium alloy prepared by the embodiment has the elasticity modulus of 58GPa at room temperature, the tensile strength of 331MPa and the room-temperature tensile strength of 382 MPa.
Example 9
The embodiment provides a high-modulus high-strength magnesium-based composite material and a preparation method thereof, and the specifically adopted steps are basically the same as those in embodiment 1, and the difference is only that: in the step 3), the power of the mechanical modification fusion machine is 2.0kw, the current is 9.8A, the rotating speed is 2000rpm, and the powder mixing time is 20 min.
The SLM-state magnesium alloy prepared by the embodiment has the elasticity modulus of 58GPa at room temperature, the tensile strength of 334MPa and the tensile strength of 372MPa at room temperature in the T5 state.
Example 10
The embodiment provides a high-modulus high-strength magnesium-based composite material and a preparation method thereof, and the specifically adopted steps are basically the same as those in embodiment 1, and the difference is only that: in the step 3), the power of the mechanical modification fusion machine is 1.8kw, the current is 9.5A, the rotating speed is 1800rpm, and the powder mixing time is 20 min.
The SLM-state magnesium alloy prepared by the embodiment has the elasticity modulus of 56GPa at room temperature, the tensile strength of 332MPa and the tensile strength of 368MPa at room temperature in the T5 state.
Example 11
The embodiment provides a high-modulus high-strength magnesium-based composite material and a preparation method thereof, and the specifically adopted steps are basically the same as those in embodiment 1, and the difference is only that: in the step 3), the power of the mechanical modification fusion machine is 1.5kw, the current is 8A, the rotating speed is 1400rpm, and the powder mixing time is 10 min.
The SLM-state magnesium alloy prepared by the embodiment has the elasticity modulus of 53GPa at room temperature, the tensile strength of 321MPa and the room-temperature tensile strength of 359MPa at T5 state.
Example 12
The embodiment provides a high-modulus high-strength magnesium-based composite material and a preparation method thereof, and the specifically adopted steps are basically the same as those in embodiment 1, and the difference is only that: nano reinforcing phase Ti3N4Is present in an amount of 0.1 wt.%.
The SLM-state magnesium alloy prepared by the embodiment has the elasticity modulus of 46GPa at room temperature, the tensile strength of 297MPa and the room-temperature tensile strength of 335MPa at the T5 state.
Example 13
The embodiment provides a high-modulus high-strength magnesium-based composite material and a preparation method thereof, and the specifically adopted steps are basically the same as those in embodiment 1, and the difference is only that: nano reinforcing phase Ti3N4Is 1 wt.%.
The SLM-state magnesium alloy prepared by the embodiment has the elasticity modulus of 50GPa at room temperature, the tensile strength of 304MPa and the tensile strength of 342MPa at T5 state at room temperature.
Example 14
The embodiment provides a high-modulus high-strength magnesium-based composite material and a preparation method thereof, and the specifically adopted steps are basically the same as those in embodiment 1, and the difference is only that: nano reinforcing phase Ti3N4Is 15 wt.%.
The SLM-state magnesium alloy prepared by the embodiment has the elasticity modulus of 62GPa at room temperature, the tensile strength of 288MPa and the tensile strength of 301MPa at room temperature in the T5 state.
Example 15
The embodiment provides a high-modulus high-strength magnesium-based composite material and a preparation method thereof, and the preparation method specifically comprises the following steps:
1) the high-modulus high-strength magnesium-based composite material comprises the following components in percentage by mass: gd: 11 wt.%; y: 2 wt.%; zn: 1 wt.%; mn: 0.5 wt.%, nanoreinforcement phase Co: 5 wt.%; the balance being Mg and unavoidable impurities.
2) Preparing Mg-11Gd-2Y-1Zn-0.5Mn (wt.%) magnesium alloy spherical powder by a conventional gas atomization method; then mixing Mg-11Gd-2Y-1Zn-0.5Mn (wt.%) magnesium alloy powder with nano-grade Co powder with the mass fraction of 5 wt.%, and carrying out physical premixing for 4 hours by using a three-dimensional mixer;
3) carrying out mechanical modification and fusion treatment on the obtained premixed powder by using a mechanical modification and fusion machine to enable the surface of the magnesium alloy powder to be coated with the reinforcing phase powder; the power of the mechanical modification fusion machine is 1.7kw, the current is 9.0A, the rotating speed is 1500rpm, and the powder mixing time is 20 min;
4) drying the mixed powder in the step 3) at 140 ℃ (under vacuum), wherein the drying time is 1.5 h;
5) filling the dried mixed powder into a powder bed of SLM printing equipment, and introducing inert gas into a cavity of the equipment for protection until the oxygen content is reduced to 50 ppm; the substrate was heated to 100 ℃ and pre-heated before printing was started. The specific parameters of selective laser melting molding are as follows: the laser power is 80W, the scanning speed is 1000mm/s, the molten pool interval is 100 μm, the scanning strategy is a strip scanning strategy, the width of a zonal is 10mm, and the interlayer rotation angle is 90 degrees.
6) Carrying out artificial aging T5 treatment on the SLM-state magnesium alloy prepared in the step 5) in a constant-temperature oil bath furnace, and adopting single-step aging treatment: the ageing temperature was 175 ℃ for 48h, followed by quenching in cold water at 30 ℃.
The SLM-state magnesium alloy prepared by the embodiment has the elasticity modulus of 60GPa at room temperature, the tensile strength of 328MPa and the tensile strength of 362MPa at T5 state at room temperature.
Example 16
The embodiment provides a high-modulus high-strength magnesium-based composite material and a preparation method thereof, and the preparation method specifically comprises the following steps:
1) the high-modulus high-strength magnesium-based composite material comprises the following components in percentage by mass: gd: 11 wt.%; y: 2 wt.%; zn: 1 wt.%; mn: 0.5 wt.%, nanoreinforcement phase Co: 2.5 wt.%; the balance being Mg and unavoidable impurities.
2) Preparing Mg-11Gd-2Y-1Zn-0.5Mn (wt.%) magnesium alloy spherical powder by a conventional gas atomization method; then mixing Mg-11Gd-2Y-1Zn-0.5Mn (wt.%) magnesium alloy powder with 2.5 wt.% nanoscale Co powder, and physically premixing for 24 hours by using a three-dimensional mixer;
3) carrying out mechanical modification and fusion treatment on the obtained premixed powder by using a mechanical modification and fusion machine to enable the surface of the magnesium alloy powder to be coated with the reinforcing phase powder; the power of the mechanical modification fusion machine is 1.7kw, the current is 9.0A, the rotating speed is 1500rpm, and the powder mixing time is 20 min;
4) drying the powder mixed in the step 3) at 180 ℃ (under vacuum), wherein the drying time is 1 h;
5) filling the dried mixed powder into a powder bed of SLM printing equipment, and introducing inert gas into a cavity of the equipment for protection until the oxygen content is reduced to 50 ppm; the substrate was heated to 200 ℃ for preheating and then printing was started. The specific parameters of selective laser melting molding are as follows: the laser power is 100W, the scanning speed is 400mm/s, the molten pool interval is 80 μm, the scanning strategy is a belt-shaped scanning strategy, the belt width is 5mm, and the interlayer rotation angle is 80 degrees.
6) Carrying out solution treatment on the SLM-state magnesium alloy prepared in the step 5): in an air resistance furnace: keeping the temperature at 380 ℃ for 12h, and then quenching in hot water at 100 ℃;
7) carrying out artificial aging T6 treatment on the magnesium alloy in the T4 state prepared in the 6) in a constant-temperature oil bath furnace, and adopting single-step aging treatment: the ageing temperature was 225 ℃ and the time 18h, followed by quenching in cold water at 30 ℃.
The SLM-state magnesium alloy prepared by the embodiment has the elasticity modulus of 55GPa at room temperature, the tensile strength of 303MPa, and the room-temperature tensile strength of 373 MPa.
Comparative example 1:
the comparative example provides a method for preparing rare earth magnesium alloy by selective laser melting technology, which is basically the same as the example 1, except that: in the comparative example, nano-sized Ti was not added3N4。
The SLM-state magnesium alloy prepared by the comparative example has the elasticity modulus of 45GPa and the tensile strength of 295MPa at room temperature.
Comparative example 2:
the comparative example provides a method for preparing rare earth magnesium alloy by selective laser melting technology, which is basically the same as the example 4, except that: in the comparative example, no nanoscale Co was added.
The SLM-state magnesium alloy prepared by the comparative example has the elasticity modulus of 45GPa at room temperature and the tensile strength of 301MPa at room temperature.
Comparative example 3:
this comparative example provides a method for preparing a rare earth magnesium alloy by selective laser melting, which is substantially the same as example 7 except that: in the comparative example, no nanoscale TiB was added2。
The SLM-state magnesium alloy prepared by the comparative example has the elasticity modulus of 45GPa at room temperature and the tensile strength of 307MPa at room temperature.
Comparative example 4:
this comparative example provides a method of casting a rare earth magnesium alloy having substantially the same alloy composition as in example 1, except that: in the comparative example, nano-sized Ti was not added3N4。
The preparation method comprises the following steps:
1) removing oxide skin on the surface of the alloy raw material, putting the alloy raw material and a refining agent accounting for 2-3 wt.% of the total weight of the smelted alloy into an oven for preheating for 2 hours, and removing water vapor on the surface of the raw material and in holes;
2) uniformly coating the mixed coating of water glass and limestone on the inner surface of the steel crucible, and putting the steel crucible into a drying oven for drying;
3) taking out the crucible, putting the crucible into a resistance furnace, and putting the alloy required by smelting into the crucible. Introducing protective gas (mixed gas of CO2/SF6 with the volume ratio of 99: 1) after the temperature of the crucible is raised, and protecting the surface of the melt in the whole smelting process;
4) after all the raw materials are melted, skimming scum on the surface of the melt and then stirring for 5 min. Then reducing the temperature of the resistance furnace, adding a refining agent after the temperature of the melt is reduced to a proper temperature, stirring and refining for 5min without power failure, and fishing out the smelting impurities at the bottom of the crucible after refining is finished;
5) keeping the temperature of the melt standing for 20min, then closing the heating, and standing for cooling the melt;
6) and skimming dross on the surface of the melt when the temperature of the melt is reduced to a proper temperature, and then pouring.
The SLM-state magnesium alloy prepared by the comparative example has the elasticity modulus of 45GPa at room temperature and the tensile strength of 277MPa at room temperature.
Comparative example 5:
this comparative example provides a method of casting a rare earth magnesium alloy having substantially the same alloy composition as example 4, except that: in the comparative example, no nanoscale Co was added.
The preparation method comprises the following steps:
1) removing oxide skin on the surface of the alloy raw material, putting the alloy raw material and a refining agent accounting for 2-3 wt.% of the total weight of the smelted alloy into an oven for preheating for 2 hours, and removing water vapor on the surface of the raw material and in holes;
2) uniformly coating the mixed coating of water glass and limestone on the inner surface of the steel crucible, and putting the steel crucible into a drying oven for drying;
3) taking out the crucible, putting the crucible into a resistance furnace, and putting the alloy required by smelting into the crucible. Introducing protective gas (mixed gas of CO2/SF6 with the volume ratio of 99: 1) after the temperature of the crucible is raised, and protecting the surface of the melt in the whole smelting process;
4) after all the raw materials are melted, skimming scum on the surface of the melt and then stirring for 5 min. Then reducing the temperature of the resistance furnace, adding a refining agent after the temperature of the melt is reduced to a proper temperature, stirring and refining for 5min without power failure, and fishing out the smelting impurities at the bottom of the crucible after refining is finished;
5) keeping the temperature of the melt standing for 20min, then closing the heating, and standing for cooling the melt;
6) and skimming dross on the surface of the melt when the temperature of the melt is reduced to a proper temperature, and then pouring.
The SLM alloy prepared by the comparative example has the elasticity modulus of 45GPa at room temperature and the tensile strength of 289MPa at room temperature.
Comparative example 6:
this comparative example provides a method of casting a rare earth magnesium alloy having substantially the same alloy composition as example 7, except that: in the comparative example, no nanoscale Co was added.
The preparation method comprises the following steps:
1) removing oxide skin on the surface of the alloy raw material, putting the alloy raw material and a refining agent accounting for 2-3 wt.% of the total weight of the smelted alloy into an oven for preheating for 2 hours, and removing water vapor on the surface of the raw material and in holes;
2) uniformly coating the mixed coating of water glass and limestone on the inner surface of the steel crucible, and putting the steel crucible into a drying oven for drying;
3) taking out the crucible, putting the crucible into a resistance furnace, and putting the alloy required by smelting into the crucible. Introducing protective gas (mixed gas of CO2/SF6 with the volume ratio of 99: 1) after the temperature of the crucible is raised, and protecting the surface of the melt in the whole smelting process;
4) after all the raw materials are melted, skimming scum on the surface of the melt and then stirring for 5 min. Then reducing the temperature of the resistance furnace, adding a refining agent after the temperature of the melt is reduced to a proper temperature, stirring and refining for 5min without power failure, and fishing out the smelting impurities at the bottom of the crucible after refining is finished;
5) keeping the temperature of the melt standing for 20min, then closing the heating, and standing for cooling the melt;
6) and skimming dross on the surface of the melt when the temperature of the melt is reduced to a proper temperature, and then pouring.
The SLM alloy prepared by the comparative example has the elasticity modulus of 45GPa at room temperature and the tensile strength of 263MPa at room temperature.
Comparative example 7
The comparative example provides a method for preparing rare earth magnesium alloy by selective laser melting technology, which is basically the same as the example 1, except that: in the comparative example, the power of the mechanical modification fusion machine used in step 3) was 1.2kw, the current was 9.0A, and the rotation speed was 1200 rpm.
The SLM-state magnesium alloy prepared by the comparative example has the elasticity modulus of 48GPa at room temperature and the tensile strength of 325MPa at room temperature.
Comparative example 8
The comparative example provides a method for preparing rare earth magnesium alloy by selective laser melting technology, which is basically the same as the example 1, except that: in the comparative example, the reinforcing phase added was Si3N4。
The SLM-state magnesium alloy prepared by the comparative example has the elasticity modulus of 48GPa at room temperature and the tensile strength of 328MPa at room temperature.
Comparative example 9
The comparative example provides a method for preparing rare earth magnesium alloy by selective laser melting technology, which is basically the same as the example 1, except that: in the comparative example, the angle of rotation between the layers used in step 5) was 75 °.
The SLM-state magnesium alloy prepared by the comparative example has the elasticity modulus of 49GPa at room temperature and the tensile strength of 303MPa at room temperature.
The embodiments described above are described to facilitate an understanding and use of the invention by those skilled in the art. It will be readily apparent to those skilled in the art that various modifications to these embodiments may be made, and the generic principles described herein may be applied to other embodiments without the use of the inventive faculty. Therefore, the present invention is not limited to the above embodiments, and those skilled in the art should make improvements and modifications within the scope of the present invention based on the disclosure of the present invention.

Claims (10)

1. A method for preparing high modulus and high strength magnesium-based composite material by selective laser melting technology is characterized by comprising the following steps:
A. preparing magnesium alloy spherical powder by a gas atomization method;
B. carrying out physical premixing on magnesium alloy spherical powder and reinforcing phase powder;
C. the premixed mixed powder is subjected to mechanical modification and fusion treatment, so that the surface of the magnesium alloy powder is coated with the reinforcing phase powder;
D. c, drying the powder treated in the step C;
E. carrying out selective laser melting molding on the dried powder to obtain a high-modulus high-strength magnesium-based composite material;
in step B, the reinforcing phase is selected from W, Co and TiB2、Ti3N4、MgO、ZrO2At least one of;
in the step C, the mechanical modification fusion treatment adopts the following specific parameters: the power is 1.5-2.0 kw, the current is 8-9.8A, and the rotation speed is 1400-2000 rpm.
2. The method for preparing high modulus high strength magnesium-based composite material by selective laser melting technology according to claim 1, wherein the method comprises the following steps: in the step A, the magnesium alloy is Mg-Gd (Y) -Zn-Zr/Mn alloy, and comprises the following elements in percentage by weight: gd: 5-20 wt.%; y: 0-5 wt.%; zn: 0-5 wt.%; mn: 0-2 wt.%; zr: 0-2 wt.%; less than 0.02% total impurities; the balance being Mg.
3. The method for preparing high modulus high strength magnesium-based composite material by selective laser melting technology according to claim 1, wherein the method comprises the following steps: the reinforcing phase powder is nano reinforcing phase powder, and the content of the reinforcing phase in the prepared high-modulus high-strength magnesium-based composite material is 0.1-15 wt.%.
4. The method for preparing the high modulus and high strength Mg-based composite material by the selective laser melting technology according to claim 1, wherein in the step B, a three-dimensional mixer is used for physical premixing for 4-24 hours.
5. The method for preparing the high modulus and high strength Mg-based composite material by the selective laser melting technology according to claim 1, wherein in the step D, the drying treatment is performed under vacuum at 140-180 ℃ for 1-2 h.
6. The method for preparing the high modulus and high strength Mg-based composite material by the selective laser melting technology according to claim 1, wherein in the step E, the selective laser melting molding is carried out by preheating before printing, wherein the preheating temperature is 100-200 ℃.
7. The method for preparing high modulus and high strength Mg-based composite material by selective laser melting technology according to claim 1, wherein in step E, selective laser melting molding is performed by using printing parameters as follows: the power is 80-160 w, the scanning distance is 50-100 mu m, the scanning speed is 400-1200 mm/s, the laser scanning strategy is a strip scanning strategy, the width of each strip is 5-10mm, and the interlayer rotation angle is 80-90 degrees.
8. The method for preparing high modulus high strength Mg-based composite material by selective laser melting technology according to claim 1, wherein said method further comprises the step of subjecting the high modulus high strength Mg-based composite material prepared in step E to solution treatment and/or aging treatment.
9. The method for preparing high modulus high strength Mg-based composite material by selective laser melting technology according to claim 8, wherein said solution treatment conditions are: the solid solution temperature is 380-525 ℃, and the time is 0.5-12 h; quenching is carried out after the solution treatment, and the quenching temperature is 25-100 ℃.
The aging treatment conditions are as follows: the aging temperature is 175-225 ℃, and the time is 0-512 h.
10. A high modulus, high strength magnesium based composite material prepared according to the process of any one of claims 1 to 9 comprising the following elements in weight percent: gd: 5-20 wt.%; y: 0-5 wt.%; zn: 0-5 wt.%; mn: 0-2 wt.%; zr: 0-2 wt.%; and (3) reinforcing phase: 0.1-15 wt.%; less than 0.02% total impurities; the balance being Mg;
the reinforcing phase is selected from W, Co and TiB2、Ti3N4、MgO、ZrO2At least one of (1).
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Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2003129161A (en) * 2001-08-13 2003-05-08 Honda Motor Co Ltd Heat resistant magnesium alloy
CN110681869A (en) * 2019-10-15 2020-01-14 上海交通大学 Method for preparing high-strength and high-toughness magnesium rare earth alloy by selective laser melting additive manufacturing technology
CN113073244A (en) * 2021-03-19 2021-07-06 中北大学 High-strength and high-toughness rare earth heat-resistant magnesium alloy and preparation method thereof

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2003129161A (en) * 2001-08-13 2003-05-08 Honda Motor Co Ltd Heat resistant magnesium alloy
CN110681869A (en) * 2019-10-15 2020-01-14 上海交通大学 Method for preparing high-strength and high-toughness magnesium rare earth alloy by selective laser melting additive manufacturing technology
CN113073244A (en) * 2021-03-19 2021-07-06 中北大学 High-strength and high-toughness rare earth heat-resistant magnesium alloy and preparation method thereof

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