CN114703411A - Mg-Sn series magnesium alloy and preparation method thereof - Google Patents
Mg-Sn series magnesium alloy and preparation method thereof Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C23/00—Alloys based on magnesium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/03—Making non-ferrous alloys by melting using master alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C23/00—Alloys based on magnesium
- C22C23/02—Alloys based on magnesium with aluminium as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C23/00—Alloys based on magnesium
- C22C23/04—Alloys based on magnesium with zinc or cadmium as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/002—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working by rapid cooling or quenching; cooling agents used therefor
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/06—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
Abstract
The invention provides an Mg-Sn series magnesium alloy and a preparation method thereof, belonging to the technical field of magnesium alloy materials. The Mg-Sn magnesium alloy provided by the invention comprises the following components in percentage by mass: sn 2-5%, Al 1.5-4.0%, Zn1.0-2.0%, Mn0.3-0.5% and the balance Mg. The Mg-Sn magnesium alloy provided by the invention can effectively promote the cooperative strengthening mechanism of each alloying element by regulating and controlling the variety and the content of each alloying element, thereby effectively improving the mechanical property and the processing efficiency of the Mg-Sn magnesium alloy.
Description
Technical Field
The invention relates to the technical field of magnesium alloy materials, in particular to an Mg-Sn series magnesium alloy and a preparation method thereof.
Background
The magnesium alloy is used as a metal structure material with the lightest weight, can meet the requirements of light weight of aerospace, automobiles and electronic products due to high specific strength and good impact resistance, and can reduce energy consumption and environmental pollution, so the magnesium alloy becomes one of the materials with the fastest growth in the middle and high-end manufacturing industry.
In order to improve the comprehensive performance of cast magnesium alloy and wrought magnesium alloy, most of the current magnesium alloy research and development ideas are similar to those of aluminum alloy, and the microstructure, strengthening and plastic deformation mechanisms are mainly regulated and controlled through alloying design. At present, Mg-Al series, Mg-Zn series and Mg-RE series magnesium alloys have been developed, but the Mg-Al series and the Mg-Zn series magnesium alloys have the problems of poor formability and the like, and the Mg-RE series magnesium alloys have higher preparation cost due to the use of rare earth elements, so that the further development and application of the magnesium alloys are limited. Compared with Mg-Al alloy, the Mg-Sn magnesium alloy has the preparation cost close to that of the Mg-Al alloy, but the microscopic strengthening and toughening mechanism of the Mg-Sn alloy mainly relates to the solid solution strengthening of Sn alloy elements and the solid solution strengthening of Mg2The intermetallic compounds such as Sn and the like have multiple strengthening mechanisms such as second phase precipitation strengthening, dispersion strengthening and the like, the structure is not easy to regulate and control, the influence on the plastic deformation process is large, and the problems of low room temperature strength, low work hardening response speed and the like still exist.
Therefore, it is highly desirable to provide an Mg — Sn magnesium alloy having excellent mechanical properties and high processing efficiency.
Disclosure of Invention
The invention aims to provide an Mg-Sn magnesium alloy and a preparation method thereof, and the Mg-Sn magnesium alloy provided by the invention has excellent mechanical property and higher processing efficiency.
In order to achieve the above object, the present invention provides the following technical solutions:
the invention provides an Mg-Sn magnesium alloy which comprises the following components in percentage by mass: 2-5% of Sn, 1.5-4.0% of Al, 1.0-2.0% of Zn, 0.3-0.5% of Mn and the balance of Mg.
Preferably, the Mg-Sn magnesium alloy comprises the following components in percentage by mass: 2.2-4.8% of Sn2, 1.8-3.8% of Al, 1.2-1.8% of Zn, 0.32-0.48% of Mn and the balance of Mg.
Preferably, the Mg-Sn magnesium alloy comprises the following components in percentage by mass: 2.5-4.5% of Sn2, 2-3.5% of Al, 1.4-1.6% of Zn, 0.35-0.45% of Mn and the balance of Mg.
The invention also provides a preparation method of the Mg-Sn series magnesium alloy, which comprises the following steps:
(1) sequentially smelting and casting the alloy raw materials to obtain an alloy ingot;
(2) carrying out post-treatment on the alloy ingot obtained in the step (1) to obtain Mg-Sn magnesium alloy; the post-treatment includes one or more of solution treatment, extrusion, and aging treatment.
Preferably, the temperature for casting in the step (1) is 680-700 ℃.
Preferably, the solution treatment in the step (2) comprises a primary solution treatment and a secondary solution treatment which are sequentially carried out; the heat preservation temperature of the primary solution treatment is 390-410 ℃, and the heat preservation time of the primary solution treatment is 10-12 h; the heat preservation temperature of the secondary solution treatment is 440-460 ℃, and the heat preservation time of the secondary solution treatment is 14-16 h.
Preferably, the extrusion temperature in the step (2) is 390-400 ℃, and the extrusion speed is 0.3-3 m/min.
Preferably, the pressure for extrusion in the step (2) is 130-180 MPa.
Preferably, the extrusion ratio in the extrusion in the step (2) is 8-22.
Preferably, the heat preservation temperature of the aging treatment in the step (2) is 170-200 ℃, and the heat preservation time of the aging treatment is 0-900 h.
The invention provides an Mg-Sn magnesium alloy which comprises the following components in percentage by mass: 2-5% of Sn, 1.5-4.0% of Al, 1.0-2.0% of Zn, 0.3-0.5% of Mn and the balance of Mg. The invention adds Sn element and controls the content thereof, regulates and controls Mg in the alloy2The quantity and distribution of the Sn strengthening phase are that part of Sn element is dissolved in Mg matrix in solid solution during solidification, and the other part is Mg2The Sn phase forms nuclei and grows, shows the appearance of dissimilarity eutectic crystal and is in the extrusion deformation processDynamic precipitation of large amounts of Mg2Sn strengthening phase, nanophase Mg at grain boundaries2Sn is distributed in a dispersing way, so that dislocation movement can be effectively hindered, and grain boundaries can be pinned, so that crystal grains are refined, and the mechanical property and the processing efficiency of the magnesium alloy are effectively improved; the invention also forms a B2-AlMnFe intermetallic compound by adding Mn element to extract Fe impurity, simultaneously adds Al element and regulates and controls the content ratio of the two elements, can form fine AlMn phase particles in the aging process, and passes through AlMn phase and Mg phase2The Sn phase is synergistically precipitated, so that the comprehensive mechanical property of the magnesium alloy is further improved; and part of Al element exists in a matrix in a solid solution form, and the mechanical property of the magnesium alloy is improved by a solid solution strengthening mechanism; the addition of Zn element can effectively improve the age hardening response efficiency of the magnesium alloy, the Zn element is easy to be segregated near the precipitated strengthening phase, the size of the precipitated phase is refined, various precipitated strengthening phases can be uniformly dispersed in the magnesium alloy matrix, and the mechanical property and the processing efficiency of the magnesium alloy are greatly improved.
Experimental results show that the extruded Mg-Sn magnesium alloy obtained by solid solution and extrusion of the Mg-Sn magnesium alloy has the tensile strength of 294MPa, the yield strength of 201MPa and the elongation of 18 percent, and has excellent room-temperature mechanical properties; the hardness of the alloy after aging can reach 69HV, and the hardness is improved by about 38% compared with the hardness of the alloy in the initial solid solution state; compared with AZ31 and Mg-Al-Ca alloy, the Mg-Sn magnesium alloy provided by the invention has the highest power dissipation factor which can reach 36 percent and shows more excellent hot working performance; in addition, compared with the traditional commercial magnesium alloy AZ31, the recrystallization rate is improved by nearly 20 percent in the hot working process, the work hardening and dynamic recovery speed is higher, and the processing efficiency is obviously superior to that of the traditional Mg-Al alloy.
Drawings
FIG. 1 is a photograph of an as-cast alloy sample obtained in step (1) of example 1 of the present invention;
FIG. 2 is a scanning electron micrograph of an as-cast alloy obtained in step (1) of example 1 of the present invention;
FIG. 3 is a high power scanning electron micrograph of a detached eutectic phase in the as-cast alloy of example 1;
FIG. 4 is a high power scanning electron micrograph of the τ -AlMn phase in the as-cast alloy of example 1;
FIG. 5 shows Al in the as-cast alloy of example 18Mn5Scanning electron microscope images with high magnification;
FIG. 6 is a high power scanning electron micrograph of the β -Mn phase in the as-cast alloy of example 1;
FIG. 7 is a graph of the rheology of the magnesium alloy of example 1 of the present invention in a hot compaction test at different temperatures;
FIG. 8 is a thermal processing diagram obtained after completion of the thermal compression experiment in example 1 of the present invention;
FIG. 9 is a scanning electron microscope photograph of an extruded alloy of example 2 of the present invention;
FIG. 10 is an IPF Z pole diagram and a (0001) pole diagram of the extruded magnesium alloy of example 2;
FIG. 11 is a scanning electron micrograph of a solid solution alloy according to example 3 of the present invention and an aged alloy according to examples 3 to 5; wherein FIG. 11(a) is a scanning electron micrograph of the alloy in the solid solution state of example 3, FIG. 11(b) is a scanning electron micrograph of the alloy in the aged state of example 3, FIG. 11(c) is a scanning electron micrograph of the alloy in the aged state of example 4, and FIG. 11(d) is a scanning electron micrograph of the alloy in the aged state of example 5;
FIG. 12 is a stress-strain curve of the as-cast alloy obtained in step (1) and the as-extruded alloy obtained in step (2) of example 2, the solid-solution alloy obtained in step (1) and the aged alloy obtained in step (2) of example 3, and the aged alloy obtained in examples 4 to 5, according to the present invention;
FIG. 13 is a graph showing the hardness change of the sample according to the invention in example 5 at the aging treatment holding temperature of 180 ℃ with the time of the aging holding time.
Detailed Description
The invention provides an Mg-Sn magnesium alloy which comprises the following components in percentage by mass: 2-5% of Sn, 1.5-4.0% of Al, 1.0-2.0% of Zn, 0.3-0.5% of Mn and the balance of Mg.
The Mg-Sn magnesium alloy provided by the invention comprises 2-5% of Sn, preferably 2.2-4.8%, more preferably 2.5-4.5%, and most preferably 3-4% in percentage by mass. The invention adds Sn element and controlsThe content of Mg in the alloy of the invention is regulated and controlled2The quantity and distribution of Sn strengthening phases, during the solidification process, part of Sn element is dissolved in Mg matrix in solid solution, and the other part is Mg2Sn phase nucleation and growth, which presents an exotic eutectic appearance, and a large amount of Mg is dynamically separated out in the extrusion deformation process2Sn strengthening phase, nanophase Mg at grain boundaries2Sn is distributed in a dispersing way, so that dislocation movement can be effectively hindered, and crystal boundaries can be pinned, thereby refining crystal grains and effectively improving the mechanical property and the processing efficiency of the magnesium alloy.
The Mg-Sn magnesium alloy provided by the invention comprises 1.5-4.0% of Al, preferably 1.8-3.8%, more preferably 1.4-1.6%, and most preferably 1.5% by mass. The Al element is added and the content of the Al element is regulated, so that the Al element and the Mn element can form fine AlMn phase particles, and the AlMn phase and the Mg phase are passed2The Sn phase is synergistically precipitated, so that the mechanical property and the processing efficiency of the magnesium alloy are further improved; and part of Al element exists in a matrix in a solid solution form, and the mechanical property of the magnesium alloy is improved by a solid solution strengthening mechanism.
The Mg-Sn magnesium alloy provided by the invention comprises 1.0-2.0% of Zn, preferably 1.2-1.8%, and more preferably 1.4-1.6% by mass. According to the invention, the age hardening response efficiency of the magnesium alloy can be effectively improved by adding Zn and regulating the content of Zn.
The Mg-Sn magnesium alloy provided by the invention comprises 0.3-0.5% of Mn, preferably 0.32-0.48% of Mn, and more preferably 0.35-0.45% of Mn in percentage by mass. According to the invention, by adding Mn element and regulating the content of Mn element, Fe impurity can be extracted by forming B2-AlMnFe intermetallic compound, and various Al-Mn phases such as Al are introduced8Mn5And tau-AlMn is equal, and can be uniformly dispersed in the magnesium alloy matrix, thereby effectively improving the mechanical property and the processing efficiency of the magnesium alloy.
According to the mass percentage, the Mg-Sn series magnesium alloy provided by the invention comprises the balance of Mg.
The Mg-Sn magnesium alloy provided by the invention can effectively regulate and control the strengthening mechanism of each alloy element by regulating and controlling the variety and the content of each alloy element, thereby effectively improving the mechanical property and the processing efficiency of the Mg-Sn magnesium alloy.
The invention also provides a preparation method of the Mg-Sn series magnesium alloy, which comprises the following steps:
(1) sequentially smelting and casting the alloy raw materials to obtain an alloy ingot;
(2) carrying out post-treatment on the alloy ingot obtained in the step (1) to obtain Mg-Sn magnesium alloy; the post-treatment includes one or more of solution treatment, extrusion, and aging treatment.
The alloy raw materials are sequentially smelted and cast to obtain the alloy ingot.
In the present invention, the kinds of the alloy raw materials preferably include pure Mg ingots, pure Sn chunks, pure Al chunks, pure Zn chunks, and Al-20% Mn master alloys. The invention has no special requirement on the source of the alloy raw materials, and the raw material source of the magnesium alloy or a commercial product which is well known to a person skilled in the art can be adopted.
In the invention, the smelting temperature is preferably 710-740 ℃. The invention has no special requirement on the smelting time, and the smelting time known by the technical personnel in the field can ensure that the alloy raw materials are completely molten.
In the invention, after the smelting is finished, the smelting preferably comprises the steps of introducing argon for refining and introducing CO sequentially2Deslagging with mixed protective gas of SF 6; the refining temperature is preferably 715-725 ℃, and the refining time is preferably 9-11 min. The invention can effectively remove impurities in the melt by refining and deslagging, improves the purity of the melt, reduces ingot defects, improves the uniformity of alloy structure, and is more favorable for improving the mechanical property and the processing efficiency of the alloy.
In the invention, the casting temperature is preferably 680-700 ℃. The present invention can reduce casting defects and improve the uniformity of alloy structure by controlling the casting temperature within the above range.
After the alloy ingot is obtained, the alloy ingot is subjected to post-treatment to obtain the Mg-Sn magnesium alloy.
In the present invention, the post-treatment includes one or more of solution treatment, extrusion and aging treatment; preferably, the solution treatment, or the solution treatment and the extrusion performed in this order, or the solution treatment and the aging treatment performed in this order are performed.
In the invention, when the post treatment is preferably solid solution treatment, the uniformity of an ingot structure can be effectively improved, more intermetallic compounds are re-dissolved in a matrix, and the mechanical property and the processing efficiency of the alloy are improved mainly through solid solution strengthening.
In the present invention, when the post-treatment is preferably solution treatment and extrusion performed in sequence, coarse dendrites can be effectively crushed by extrusion deformation, and the grain size can be further refined by dynamic recrystallization of deformation, that is, the mechanical properties and the processing efficiency of the alloy can be effectively improved by fine grain strengthening. Meanwhile, the dynamic precipitated phase which is dispersed and distributed in the extrusion process can promote the formation of dynamic recrystallization and further improve the microstructure of crystal grains, thereby improving the mechanical property and the processing efficiency of the alloy by utilizing precipitation strengthening and fine grain strengthening together.
In the invention, when the post-treatment is preferably solution treatment and aging treatment which are sequentially carried out, coarse intermetallic compounds are re-dissolved through the solution treatment, the structure preparation is carried out for the subsequent aging treatment, and then the uniform precipitation of each precipitated phase is effectively promoted through the aging treatment, so that the mechanical property and the processing efficiency of the alloy are effectively improved.
In the present invention, the solution treatment preferably includes a primary solution treatment and a secondary solution treatment performed in this order.
In the invention, the heat preservation temperature of the primary solution treatment is preferably 390-410 ℃, and more preferably 400 ℃; the heat preservation time of the primary solution treatment is preferably 10-12 hours, and more preferably 11 hours.
In the present invention, it is preferable to continue the temperature rise to the holding temperature of the secondary solution treatment after the primary solution treatment is completed.
In the invention, the heat preservation temperature of the secondary solution treatment is preferably 440-460 ℃, and more preferably 450 ℃; the heat preservation time of the secondary solution treatment is preferably 14-16 h, and more preferably 15 h. The invention can ensure that more coarse precipitated phases are dissolved in the matrix again by controlling the heat preservation temperature and the heat preservation time of the primary solution treatment, and is more favorable for realizing the solid solution strengthening and improving the performance of the alloy.
In the present invention, the cooling method after the completion of the solution treatment is preferably air-cooled to room temperature or water-cooled to room temperature.
In the invention, the extrusion temperature is preferably 390-400 ℃; the extrusion speed is preferably 0.3-3 m/min, more preferably 0.5-2.5 m/min, and most preferably 1-2 m/min. According to the invention, by controlling the extrusion temperature and the extrusion speed within the above range, the deformation resistance of the alloy can be reduced, the problem of cracking or cracking of the alloy can be reduced, and the crushing of coarse dendritic crystals in the alloy matrix through extrusion is facilitated.
In the present invention, the pressure of the extrusion is preferably 130 to 180MPa, more preferably 140 to 160MPa, and most preferably 150 MPa.
In the invention, the extrusion ratio in the extrusion is preferably 8-22, more preferably 10-20, and most preferably 12-18. The present invention is more advantageous for refining the grain size by controlling the extrusion pressure and the extrusion ratio within the above ranges.
In the invention, the heat preservation temperature of the aging treatment is preferably 170-200 ℃, and more preferably 180-190 ℃; the heat preservation time of the aging treatment is preferably 0-900 h, more preferably 80-700 h, and most preferably 100-500 h. According to the invention, by controlling the heat preservation temperature and the heat preservation time of the aging treatment within the above ranges, the precipitation of each precipitated phase can be effectively promoted, and the precipitation strengthening is realized to improve the mechanical property and the processing efficiency of the alloy.
In the present invention, the cooling method after the completion of the aging treatment is preferably air-cooled to room temperature.
The preparation method provided by the invention has various optional post-treatment combination modes, can obtain the magnesium alloy with excellent mechanical property and processing efficiency, and has the advantages of simple process, easily-controlled parameters and low cost.
The technical solution of the present invention will be clearly and completely described below with reference to the embodiments of the present invention. It is to be understood that the described embodiments are merely exemplary of the invention, and not restrictive of the full scope of the invention. All other embodiments, which can be derived by a person skilled in the art from the embodiments given herein without making any creative effort, shall fall within the protection scope of the present invention.
Example 1
The Mg-Sn magnesium alloy provided in this embodiment is composed of the following components in percentage by mass: 3.8% of Sn3, 2.82% of Al, 1.39% of Zn, 0.61% of Mn and the balance of Mg.
The preparation method of the Mg-Sn series magnesium alloy comprises the following specific steps:
(1) sequentially smelting and casting the alloy raw materials to obtain an alloy ingot; specifically, the method comprises the following steps: pure Mg ingot, pure Sn, Al and Zn blocks and Al-20% Mn intermediate alloy are taken as raw materials, added into a smelting furnace to be smelted at 740 ℃, the melt is kept at the temperature of 720 ℃ after smelting is finished, argon is introduced to carry out refining for 10min, and then CO is introduced2Standing the mixture with SF6 for 1h, and removing slag; and finally, cooling to 690 ℃ for semi-continuous casting to obtain an alloy ingot.
(2) Carrying out post-treatment on the alloy ingot obtained in the step (1) to obtain Mg-Sn magnesium alloy; wherein the post-treatment is solid solution treatment, specifically primary solid solution treatment and secondary solid solution treatment which are sequentially carried out; more specifically: and (3) carrying out primary solution treatment on the alloy ingot at 400 ℃ for 10h, then continuously heating to 450 ℃ for secondary solution treatment for 16h, finally discharging from the furnace and air-cooling to room temperature.
A photograph of an as-cast alloy sample obtained in step (1) of example 1 of the present invention is shown in FIG. 1.
As can be seen from FIG. 1, the as-cast alloy obtained by casting was smooth in appearance and free of defects.
The microstructure of the as-cast alloy obtained in the step (1) of example 1 was observed by a scanning electron microscope, and the observation results are shown in fig. 2 to 6. Wherein, FIG. 2 is a scanning electron micrograph of an as-cast alloy obtained in example 1; FIG. 3 is a high power scanning electron micrograph of a detached eutectic phase in the as-cast alloy of example 1; FIGS. 4 to 6 are high-power scanning electron micrographs of various AlMn phases in the as-cast alloy of example 1, respectively
As can be seen from the graphs 2-6, in the solidification process of the alloy, the primary AlMn phase takes the first time for nucleation and growth, and as the temperature is reduced, the primary Mg dendrite nucleation and eutectic reaction occur in sequence, and finally the cast microstructure presents coarse alpha-Mg matrix dendrites and dendrite separation exotic eutectic phases.
Thermal compression experiments: the Mg-Sn based magnesium alloy in a solid solution state finally obtained in example 1 was machined to obtain 5 sets of columnar test pieces having a size of phi 10 mm. times.12 mm. Before hot compression, 5 groups of samples are respectively heated to 300 ℃, 340 ℃, 380 ℃, 420 ℃ and 460 ℃ at the speed of 5 ℃/s, and stay for 120s after reaching the target temperatures, so as to ensure that the samples are uniformly heated to the target temperature integrally. Then, the 5 groups of heated samples were heated for 0.001s by using a thermocompressor-1、0.01s-1、0.1s-1、1s-1And 10s-1The sample to be detected is obtained by water-cooling quenching after the sample is compressed at the rate of-0.8, the rheological curve graph obtained after the hot compression experiment is finished is shown in figure 7, and the hot processing graph obtained after the hot compression experiment is finished is shown in figure 8.
According to the graphs in the figures 7 to 8, the Mg-Sn magnesium alloy prepared in the embodiment 1 of the invention has better machinability, and the alloy has a larger machinability range compared with AZ31 alloy through calculating the instability criterion. In addition, the alloy has higher power dissipation factor under high strain rate, and effectively improves the processing efficiency.
Example 2
Two groups of solid solution Mg-Sn series magnesium alloy samples prepared in the example 1 are extruded to obtain the extruded Mg-Sn series magnesium alloy in the example 2, wherein the parameters of the extrusion in the example 2 are shown in the table 1.
Table 1 parameters for extrusion in example 2
| Blank temperature/. degree.C | Extrusion barrel temperature/° c | Mold temperature/. degree.C | Pressure of equipment/MPa | Extrusion speed/m/min | Extrusion ratio | |
| Example 2 | 400 | 400 | 400 | 140 | 1.0 | 22:1 |
The microstructure of the extruded Mg-Sn magnesium alloy of example 2 was observed by a scanning electron microscope, and the microstructure obtained by the observation is shown in FIG. 9.
According to the graph 9, in the extrusion process, the crystal grains are refined in the dynamic recrystallization process of the alloy, a large amount of dynamic precipitated phases are distributed in the crystal interior and the crystal boundary, and after the extrusion is finished, the fine grain strengthening and the second phase dispersion strengthening are performed, so that the mechanical property of the Mg-Sn series magnesium alloy is effectively improved.
The grain orientation distribution of the as-extruded Mg — Sn magnesium alloy of example 2 was characterized by back scattered electron diffraction (EBSD), and its IPF-Z inverse pole figure and (0001) pole figure are shown in fig. 10.
According to fig. 10, the extruded Mg-Sn alloy has a typical magnesium alloy extruded wire texture, and plays a role in texture strengthening on the alloy, and further improves the mechanical properties of the alloy by combining fine grain strengthening and dispersion strengthening.
Example 3
The post-treatment of step (2) in example 1 was replaced by the following post-treatment process: sequentially carrying out solid solution treatment and aging treatment on the alloy ingot obtained in the step (1), and more specifically: carrying out primary solution treatment on the alloy ingot at 400 ℃ for 10h, then continuing to heat to 450 ℃ for secondary solution treatment for 16h, and finally discharging from the furnace and cooling to room temperature by water; then carrying out aging treatment, wherein the process system is to keep the temperature at 180 ℃ for 50 h.
Example 4
The heat preservation time of the aging treatment in the step (2) of the example 3 is replaced by 100 h.
Example 5
The heat preservation time of the aging treatment in the step (2) of the example 3 is replaced by 300 h.
The microstructure of the solid-solution alloy of example 3 and the aged alloy finally obtained in examples 3 to 5 was observed by a scanning electron microscope, and the observed results are shown in fig. 11. FIG. 11(a) is a scanning electron micrograph of the alloy in the solid solution state of example 3, FIG. 11(b) is a scanning electron micrograph of the alloy in the aged state of example 3, FIG. 11(c) is a scanning electron micrograph of the alloy in the aged state of example 4, and FIG. 11(d) is a scanning electron micrograph of the alloy in the aged state of example 5.
As can be seen from FIG. 11, the Mg-Sn alloy had a small amount of residual AlMn and Mg after the solution treatment2The Sn phase is not dissolved completely, a large amount of dispersed precipitated phases appear in the crystal along with the aging process, semicontinuous distributed precipitated phases appear in the crystal boundary, the number density of the precipitated phases is continuously increased along with the prolonging of the aging time, and the sizes of the precipitated phases are gradually coarsened.
According to the standard of national standard GBT228-2002, the cast alloy obtained in the step (1) of example 2, the extruded alloy obtained in the step (2), the solid solution alloy obtained in the step (1) of example 3, the aged alloy obtained in the step (2), and the aged alloy obtained in examples 4 to 5 are processed into standard tensile samples by wire cutting, and tensile test is performed on the standard tensile samples, wherein the tensile samples are round rods, and the axial direction of the tensile samples is parallel to the extrusion direction, and the tensile test results of the obtained samples are shown in FIG. 12.
As can be seen from fig. 12, the extruded Mg — Sn magnesium alloy obtained in example 2 of the present invention has a tensile strength of 294MPa, a yield strength of 201MPa, and an elongation of 18%, and has excellent room-temperature mechanical properties.
And (3) hardness testing: the samples of example 5 aged at 180 ℃ for different periods of time were subjected to an aged hardness test using a model HV-1000TPTA Vickers, and Vickers Vi.
As can be seen from FIG. 13, the Mg-Sn series magnesium alloy finally prepared by the invention has obvious aging strengthening effect, the hardness of the alloy is continuously improved from the solid solution state of 50HV through the increase of the aging time, the peak hardness reaches to 69HV after 300h, the hardness is improved by nearly 38%, and the hardness is not reduced after the aging time is further prolonged.
The foregoing is only a preferred embodiment of the present invention, and it should be noted that, for those skilled in the art, various modifications and decorations can be made without departing from the principle of the present invention, and these modifications and decorations should also be regarded as the protection scope of the present invention.
Claims (10)
1. An Mg-Sn series magnesium alloy comprises the following components in percentage by mass: 2-5% of Sn, 1.5-4.0% of All, 1.0-2.0% of Zn, 0.3-0.5% of Mn and the balance of Mg.
2. The Mg-Sn-based magnesium alloy according to claim 1, comprising the following components in mass percent: 2.2-4.8% of Sn, 1.8-3.8% of Al, 1.2-1.8% of Zn, 0.32-0.48% of Mn and the balance of Mg.
3. The Mg-Sn-based magnesium alloy according to claim 2, comprising the following components in mass percent: 2.5-4.5% of Sn, 2-3.5% of Al, 1.4-1.6% of Zn, 0.35-0.45% of Mn and the balance of Mg.
4. A method for producing the Mg-Sn based magnesium alloy according to any one of claims 1 to 3, comprising the steps of:
(1) sequentially smelting and casting the alloy raw materials to obtain an alloy ingot;
(2) carrying out post-treatment on the alloy ingot obtained in the step (1) to obtain Mg-Sn magnesium alloy; the post-treatment includes one or more of solution treatment, extrusion, and aging treatment.
5. The method according to claim 4, wherein the temperature of the casting in the step (1) is 680 to 700 ℃.
6. The production method according to claim 4, wherein the solution treatment in the step (2) includes a primary solution treatment and a secondary solution treatment which are sequentially performed; the heat preservation temperature of the primary solution treatment is 390-410 ℃, and the heat preservation time of the primary solution treatment is 10-12 h; the heat preservation temperature of the secondary solution treatment is 440-460 ℃, and the heat preservation time of the secondary solution treatment is 14-16 h.
7. The method according to claim 4, wherein the extrusion temperature in the step (2) is 390 to 400 ℃ and the extrusion speed is 0.3 to 3 m/min.
8. The method according to claim 4 or 7, wherein the pressure for the extrusion in the step (2) is 130 to 180 MPa.
9. The method according to claim 4 or 7, wherein the extrusion ratio in the extrusion in the step (2) is 8 to 22.
10. The preparation method according to claim 4, wherein the temperature for the aging treatment in the step (2) is 170 to 200 ℃, and the time for the aging treatment is 0 to 900 hours.
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Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2007138227A (en) * | 2005-11-16 | 2007-06-07 | Sumitomo Electric Ind Ltd | Magnesium alloy material |
| CN102230118A (en) * | 2011-07-05 | 2011-11-02 | 重庆大学 | Magnesium alloy of high intensity and high yield ratio and preparation method thereof |
| KR101276665B1 (en) * | 2012-02-03 | 2013-06-19 | 한국기계연구원 | Magnesium alloy heat-treatable at high temperature |
| CN103695741A (en) * | 2013-12-16 | 2014-04-02 | 中国科学院金属研究所 | Mg-Zn-Al-Sn-Mn series magnesium alloy and preparation method thereof |
| CN107338379A (en) * | 2017-07-12 | 2017-11-10 | 北京科技大学 | A kind of magnesium Tin-zinc-aluminium manganese wrought magnesium alloy and preparation method thereof |
-
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- 2022-04-12 CN CN202210377744.XA patent/CN114703411A/en active Pending
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2007138227A (en) * | 2005-11-16 | 2007-06-07 | Sumitomo Electric Ind Ltd | Magnesium alloy material |
| CN102230118A (en) * | 2011-07-05 | 2011-11-02 | 重庆大学 | Magnesium alloy of high intensity and high yield ratio and preparation method thereof |
| KR101276665B1 (en) * | 2012-02-03 | 2013-06-19 | 한국기계연구원 | Magnesium alloy heat-treatable at high temperature |
| CN103695741A (en) * | 2013-12-16 | 2014-04-02 | 中国科学院金属研究所 | Mg-Zn-Al-Sn-Mn series magnesium alloy and preparation method thereof |
| CN107338379A (en) * | 2017-07-12 | 2017-11-10 | 北京科技大学 | A kind of magnesium Tin-zinc-aluminium manganese wrought magnesium alloy and preparation method thereof |
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