CN108796324A - A kind of room temperature high-ductility magnesium-tin-yttrium-zircaloy and preparation method thereof - Google Patents
A kind of room temperature high-ductility magnesium-tin-yttrium-zircaloy and preparation method thereof Download PDFInfo
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- CN108796324A CN108796324A CN201810717720.8A CN201810717720A CN108796324A CN 108796324 A CN108796324 A CN 108796324A CN 201810717720 A CN201810717720 A CN 201810717720A CN 108796324 A CN108796324 A CN 108796324A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C23/00—Alloys based on magnesium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/03—Making non-ferrous alloys by melting using master alloys
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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
- C22C23/06—Alloys based on magnesium with a rare earth metal as the next major constituent
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/06—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
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Abstract
The present invention relates to a kind of room temperature high-ductility magnesium-tin-yttrium-zircaloys and preparation method thereof, belong to magnesium alloy technical field, which by mass percentage, is grouped as by following group：Sn 0.2-0.4%；Y 0.4-0.9%；Zr 0.4-0.6%；Inevitable impurity≤0.15%；Surplus is magnesium.By the way that Sn, Y and Zr element and the simultaneously content of three kinds of elements of control are added into magnesium alloy, it can not only ensure that there is the magnesium alloy finally prepared high-ductility, the rate of stretching to be up to 40%, it can also be ensured that the magnesium alloy possesses medium yield strength and tensile strength.When preparing the magnesium alloy, a small amount of rare earth element only need to be added, the plasticity of magnesium alloy can be significantly changed, and preparation method is simple, a conventional extruded only need to be carried out, does not need to complicated processing technology, used smelting furnace, extruder are conventional common apparatus, it is portable strong, convenient for realizing in the industry.
Description
Technical field
The invention belongs to magnesium alloy technical fields, and in particular to a kind of room temperature high-ductility magnesium-tin-yttrium-zircaloy and its system
Preparation Method.
Background technology
Magnesium and magnesium alloy have many advantages, such as low-density, high specific strength, high specific stiffness, good capability of electromagnetic shielding, are navigating
The fields such as empty space flight, automotive light weight technology, telecommunications have extremely important application value and bright prospects.
Compared with cast magnesium alloy, wrought magnesium alloy has the development potentiality of bigger, by can to the regulation and control of material structure
Obtain more excellent mechanical property.Magnesium alloy causes to process since with Patterns for Close-Packed Hexagonal Crystal structure, slip system at room temperature is few
Deformation is difficult, and therefore, wrought magnesium alloy needs to be process by thermal deformations means such as extruding, rollings, but limited sliding
So that magnesium alloy is easy to form strong basal plane texture after being plastically deformed, this strong basal plane texture will deteriorate follow-up magnesium for system
The mechanical property and room temperature forming property of sheet alloy.In recent years, researchers propose to regulate and control base using the means of alloying
Plane texture, and then improve the mechanical property and room temperature forming property of magnesium alloy.Addition rare earth element can be effective in the magnesium alloy
Reduction basal plane texture, improve the plasticity and forming property of magnesium alloy.But due to the price of rare earth element costliness, force research
Persons' developing low-cost high-performance magnesium-alloy.
Invention content
In view of this, one of the objects of the present invention is to provide a kind of room temperature high-ductility magnesium-tin-yttrium-zircaloys；Purpose it
Two are to provide a kind of preparation method of room temperature high-ductility magnesium-tin-yttrium-zircaloy.
In order to achieve the above objectives, the present invention provides the following technical solutions：
1, a kind of room temperature high-ductility magnesium-tin-yttrium-zircaloy, by mass percentage, the magnesium alloy by organizing grouping as follows
At：Sn 0.2-0.4%；Y 0.4-0.9%；Zr 0.4-0.6%；Inevitable impurity≤0.15%；Surplus is magnesium.
Preferably, by mass percentage, the magnesium alloy is grouped as by following group：Sn 0.21%；Y 0.41%；Zr
0.46%；Inevitable impurity≤0.15%；Surplus is magnesium.
Preferably, by mass percentage, the magnesium alloy is grouped as by following group：Sn 0.38%；Y 0.90%；Zr
0.52%；Inevitable impurity≤0.15%；Surplus is magnesium.
2, the preparation method of a kind of room temperature high-ductility magnesium-tin-yttrium-zircaloy, described method includes following steps：
(1) melting：Under protective atmosphere, pure magnesium ingot is heated to 670-700 DEG C, is beaten after the pure magnesium ingot all fusing
Slag then heats to 710-730 DEG C, and pure tin ingot, magnesium yttrium intermediate alloy and Mg-Zr intermediate alloy is added, is sufficiently stirred melting, in
Magnesium alloy melt is obtained after keeping the temperature 20-30min at 710-730 DEG C；
(2) it casts：By moulding by casting after the magnesium alloy melt slag hitting obtained in step (1), ingot casting is obtained after air-cooled；
(3) it machines：It will be spare after the ingot casting sawing obtained in step (2), railway carriage；
(4) Homogenization Treatments；
(5) it squeezes.
Preferably, in step (1), the protective atmosphere is CO2And SF6By volume 99：1 mixed gas formed.
Preferably, in step (1), the mass percent of the magnesium yttrium intermediate alloy yttrium is 28-30%.
Preferably, in step (1), the mass percent of the Mg-Zr intermediate alloy zirconium is 28-30%.
Preferably, in step (1), the concrete mode that pure tin ingot, magnesium yttrium intermediate alloy and Mg-Zr intermediate alloy is added
For：After pure tin ingot fusing, magnesium yttrium intermediate alloy is added after standing 5min, then after magnesium yttrium intermediate alloy fusing,
Mg-Zr intermediate alloy is added after standing 5min again.
Preferably, in step (4), the Homogenization Treatments are specially to keep the temperature 12-24h at 350-370 DEG C.
Preferably, in step (5), the extruding is specially：By extrusion die and the ingot casting handled through step (4) in 350-
It is 350-370 DEG C squeezing temperature after preheating 1-2h at 370 DEG C, extrusion speed 6-10mmin-1, extrusion ratio 33-55:1
Under the conditions of carry out.
The beneficial effects of the present invention are：The present invention provides a kind of room temperature high-ductility magnesium-tin-yttrium-zircaloy and its systems
Preparation Method can not only be ensured most by the way that Sn, Y and Zr element and the simultaneously content of three kinds of elements of control are added into magnesium alloy
The magnesium alloy prepared eventually has high-ductility, and the rate of stretching is up to 40%, it can also be ensured that the magnesium alloy possess medium yield strength and
Tensile strength.It is most of to be solid-solution in magnesium-based the reason is that, the content of the three kinds of elements added in pure magnesium is few, cause the
The formation of two-phase is largely reduced, so these second rare phases are just not enough to become stretching in drawing process
Formation of crack, and then ensure that the alloy finally prepared has high-ductility, show as that there is higher elongation percentage.Additionally, due to Y element
Mainly exist in the form of being solid-solubilized in magnesium matrix, promotes the formation of rare earth texture in extrusion process, the basal plane for weakening alloy is knitted
Structure promotes the unlatching of basal slip in stretcher strain, substantially increases the plasticity of alloy.In addition, being solid-solubilized in the three of magnesium matrix
Kind element can play the effect of solution strengthening to a certain extent, wherein Zr elements exist in fusion process in the form of α-Zr
And as equiax crystal, the crystallite dimension of cast alloy is refined, so that the crystallite dimension of As-extruded alloy is more tiny, promote
Into the raising of alloy tensile intensity.Three kinds of elements for being solid-solution in magnesium matrix are enriched in grain boundaries in an atomic fashion, one side energy
The effective movement for hindering crystal boundary improves tensile strength, and on the one hand two can improve the binding ability of crystal boundary again, brilliant when preventing from stretching
The generation of limiting fissure line has the plasticity that can increase considerably alloy to improve to a certain extent while alloy strength.It is making
Used cost of material is low when the standby magnesium alloy, and a small amount of rare earth element only need to be added, can significantly change the modeling of magnesium alloy
Property, and preparation method is simple, only need to carry out a conventional extruded, does not need to complicated processing technology, used melting
Stove, extruder are conventional common apparatus, portable strong, convenient for realizing in the industry.
Description of the drawings
In order to keep the purpose of the present invention, technical solution and advantageous effect clearer, the present invention provides following attached drawing and carries out
Explanation：
Fig. 1 is the XRD diagram of the magnesium-tin-yttrium-zircaloy plank prepared in embodiment 1, embodiment 2 and comparative example；
((a), (b), (c) are followed successively by the XRD of the magnesium-tin-yttrium-zircaloy plank prepared in embodiment 1, embodiment 2 and comparative example
Figure)
Fig. 2 is the scanning electron microscope (SEM) photograph of the magnesium-tin-yttrium-zircaloy plank prepared in embodiment 1；
Fig. 3 is the scanning electron microscope (SEM) photograph of the magnesium-tin-yttrium-zircaloy plank prepared in embodiment 2；
Fig. 4 is the scanning electron microscope (SEM) photograph of the magnesium-tin-yttrium-zircaloy plank prepared in comparative example；
Fig. 5 is that magnesium alloy plate in comparative example is stretched to sweeping for magnesium-tin-yttrium-zircaloy plank after 10% strain
Retouch electron microscope；
Fig. 6 is the tissue of the magnesium-tin-yttrium-zircaloy plank prepared in embodiment 1, embodiment 2 and comparative example and knits
Composition.(magnesium-tin-yttrium-zircaloy plank that (a), (b), (c) are prepared in embodiment 1, embodiment 2 and comparative example successively
IPF schemes；(d), magnesium-tin-yttrium-zircaloy plank that (e), (f) are prepared in embodiment 1, embodiment 2 and comparative example successively
(0002) microcosmic pole figure)
Specific implementation mode
The preferred embodiment of the present invention will be described in detail below.
Embodiment 1
A kind of room temperature high-ductility magnesium-tin-yttrium-zircaloy, by mass percentage, which is grouped as by following group：
Sn 0.21%；Y 0.41%；Zr 0.46%；Inevitable impurity≤0.15%；Surplus is magnesium.
The preparation method of the room temperature high-ductility magnesium-tin-yttrium-zircaloy is as follows：
(1) melting：In CO2And SF6By volume 99：Under 1 mixed gas formed, pure magnesium ingot is heated to 670 DEG C, is waited for
Slag hitting after the pure magnesium ingot all melts, then heats to 720 DEG C, is firstly added pure tin ingot, after the fusing of pure tin ingot, stands
5min adds magnesium yttrium intermediate alloy, after the fusing of magnesium yttrium intermediate alloy, then stands 5min, is eventually adding Mg-Zr intermediate alloy,
It is sufficiently stirred melting, obtains magnesium alloy melt after keeping the temperature 20min at 720 DEG C, the quality hundred of yttrium wherein in magnesium yttrium intermediate alloy
Divide than being 28%；The mass percent of Mg-Zr intermediate alloy zirconium is 30%.
(2) it casts：By moulding by casting after the magnesium alloy melt slag hitting obtained in step (1), ingot casting is obtained after air-cooled；
(3) it machines：By the ingot casting sawing obtained in step (2), railway carriage to a diameter of 70mm, the spindle of a height of 60mm is standby
With；
(4) Homogenization Treatments：It will treated that ingot casting keeps the temperature 12h at 350 DEG C through step (3).
(5) it squeezes：By extrusion die and after the ingot casting of step (4) processing preheats 1.5h at 350 DEG C, temperature is being squeezed
It is 350 DEG C, extrusion speed 6mmin-1, extrusion ratio 33:It is squeezed under the conditions of 1, magnesium-tin-yttrium-airconium alloy plates is made
Material.
Embodiment 2
A kind of room temperature high-ductility magnesium-tin-yttrium-zircaloy, by mass percentage, which is grouped as by following group：
Sn 0.38%；Y 0.90%；Zr 0.52%；Inevitable impurity≤0.15%；Surplus is magnesium.
The preparation method of the room temperature high-ductility magnesium-tin-yttrium-zircaloy is as follows：
(1) melting：In CO2And SF6By volume 99：Under 1 mixed gas formed, pure magnesium ingot is heated to 700 DEG C, is waited for
Slag hitting after the pure magnesium ingot all melts, then heats to 730 DEG C, is firstly added pure tin ingot, after the fusing of pure tin ingot, stands
5min adds magnesium yttrium intermediate alloy, after the fusing of magnesium yttrium intermediate alloy, then stands 5min, is eventually adding Mg-Zr intermediate alloy,
It is sufficiently stirred melting, obtains magnesium alloy melt after keeping the temperature 30min at 730 DEG C, the quality hundred of yttrium wherein in magnesium yttrium intermediate alloy
Divide than being 30%；The mass percent of Mg-Zr intermediate alloy zirconium is 28%.
(2) it casts：By moulding by casting after the magnesium alloy melt slag hitting obtained in step (1), ingot casting is obtained after air-cooled；
(3) it machines：By the ingot casting sawing obtained in step (2), railway carriage to a diameter of 70mm, the spindle of a height of 60mm is standby
With；
(4) Homogenization Treatments：It will treated that ingot casting is kept the temperature for 24 hours at 370 DEG C through step (3).
(5) it squeezes：By extrusion die and after the ingot casting of step (4) processing preheats 2h at 370 DEG C, it is squeezing temperature
370 DEG C, extrusion speed 10mmin-1, extrusion ratio 55:It is squeezed under the conditions of 1, magnesium-tin-yttrium-zircaloy plank is made.
Comparative example
A kind of magnesium-tin-yttrium-zircaloy of medium Sn and Y contents, by mass percentage, the magnesium alloy is by following component
Composition：Sn 2.1%；Y 2.0%；Zr 0.56%；Inevitable impurity≤0.15%；Surplus is magnesium.The preparation side of the alloy
Method is referring to embodiment 1.
Using X-ray diffractometer (Rigaku D/Max 2500) respectively in embodiment 1, embodiment 2 and comparative example
Magnesium-tin-yttrium-zircaloy plank of preparation is analyzed, and the results are shown in Figure 1, wherein (a), (b), (c) are followed successively by reality in Fig. 1
Apply the XRD diagram of the magnesium-tin-yttrium-zircaloy plank prepared in example 1, embodiment 2 and comparative example, as shown in Figure 1, embodiment 1
α-Mg matrixes are only found in magnesium-tin-yttrium-zircaloy plank of middle preparation, with the increase of Sn, Y content, embodiment 2 and comparison
There is Sn in magnesium-tin-yttrium-zircaloy plank in embodiment3Y5With MgSnY the second phases, but without finding that the element containing Zr spreading out
Penetrate peak.Judged by the peak intensity of XRD diagram and the quantity of diffraction maximum, in example 2 MgSnY in magnesium-tin-yttrium-zircaloy plank
The diffraction peak intensity of ternary phase is weak, and quantity is few, and in comparative example in magnesium-tin-yttrium-zircaloy plank the phase peak intensity
Greatly, quantity is more.Therefore, it can be deduced that Sn3Y5It is preferentially formed in alloy graining process, with the increase of Sn and Y contents, MgSnY
Ternary phase gradually forms.
Using TESCAN VEGA 3LMH scanning electron microscope respectively in embodiment 1, embodiment 2, comparative example
Magnesium-tin-yttrium-zircaloy plank of preparation and by comparative example magnesium alloy plate stretch 10% strain after magnesium-tin-yttrium-
Zircaloy plank is analyzed, as a result as shown in Fig. 2, Fig. 3, Fig. 4 and Fig. 5, wherein as shown in Figure 2, is prepared in embodiment 1
The quantity of the second phase is comparable few in magnesium-tin-yttrium-zircaloy plank, this in its XRD diagram in addition to α-Mg phases without other
The result of two-phase is consistent；As can be seen from figs. 3 and 4 magnesium-tin-yttrium-zircaloy the plank prepared in embodiment 2 and comparative example
In the quantity of the second phase gradually increase, irregular fine particle shape is presented in the pattern of the second phase, is in streamline along the direction of extrusion
Distribution, and the quantity of the second phase is much larger than prepared by embodiment 2 in the magnesium-tin-yttrium-zircaloy plank prepared in comparative example
The quantity of second phase in magnesium-tin-yttrium-zircaloy plank, and irregular second phase of more bulk occur, this also with two kinds
The result of the XRD diagram displaying of plank is consistent.
Since the second phase of a large amount of small and disperseds distribution being capable of effectively pinning crystal boundary, and then the crystal grain ruler of refining alloy
It is very little, the intensity of alloy is improved, but at the same time, a large amount of irregular second phases of bulk will become tensile fractures in drawing process
Source largely reduces the plasticity of alloy.As shown in Figure 5, it gets along in bulk second and apparent crackle occurs, thus say
Bright, a large amount of irregular second phases of bulk can become tensile fractures source in drawing process so that alloy plasticity reduces.
Using JEOL JSM-7800F field emission microscopes respectively in embodiment 1, embodiment 2 and comparative example
Magnesium-tin-yttrium-zircaloy plank of preparation carries out tissue and textile analysis, and the results are shown in Figure 6, (a) in Fig. 6, (b), (c) according to
The IPF of the magnesium-tin-yttrium-zircaloy plank prepared in secondary embodiment 1, embodiment 2 and comparative example schemes, in Fig. 6 (a),
(b), (c) it is found that with Sn constituent contents increase, crystallite dimension is smaller and smaller, and average grain size drops to from~10 μm
~6 μm, since the tiny Second Phase Particle that even dispersion is distributed in matrix can effectively facilitate dynamic recrystallization in three kinds of alloys
Formation, while being pinned at crystal boundary, recrystal grain hindered to grow up, meanwhile, the second phase and crystal boundary can also hinder dislocation motion,
Play the role of pinning dislocation and make crystal grain refinement, in addition, Zr elements part in Serum Magnesium exists in the form of α-Zr, becomes
The particle of magnesium crystal forming core, refinement as cast condition magnesium-tin-yttrium-zircaloy crystallite dimension, crystal grain can be in further extrusion process
Further refined.The magnesium-that (d), (e), (f) are prepared in embodiment 1, embodiment 2 and comparative example successively in Fig. 6
(0002) microcosmic pole figure of tin-yttrium-zircaloy plank, (d), (e), (f) are it is found that three kinds of sheet alloys show in Fig. 6
Typical bimodal texturizing properties, maximum pole density appear in the positions that~20 ° of deflection occurs along the direction of extrusion, only pole density with
It the increase of Sn constituent contents and reduces.
Using CMT5105-300kN microcomputer controlled electronic universal testers to business AZ31 magnesium alloy plates, without Zr members
Magnesium-the tin-prepared in the microalloying magnesium-tin-yittrium alloy (Mg-0.4Sn-0.7Y) and embodiment 1,2 and comparative example of element
Yttrium-zircaloy plank carries out tension test, and the results are shown in Table 1.
As shown in Table 1, the microalloying magnesium-tin-yittrium alloy (Mg-0.4Sn-0.7Y) and embodiment 1,2 of Zr elements are free of
The elongation percentage of magnesium-tin-yttrium-zircaloy plank of middle preparation is apparently higher than the magnesium-tin-prepared in business AZ31 and comparative example
The elongation percentage of the magnesium alloy plate prepared in the elongation percentage of yttrium-zircaloy plank, especially embodiment 2 is up to 40.1%, and bends
It takes intensity and 180.3MPa and 300.8MPa is respectively increased in tensile strength, this excellent mechanical property and elongation percentage are conducive to
The promotion of further bending and erichsen test energy.Although containing a large amount of tiny second phases, Ke Yiming in comparative example
It is aobvious to enhance its yield strength, but apparent reduction occurs for its texture intensity, under the comprehensive function of the two, intensity is still low
The intensity of the magnesium-tin-yttrium-zircaloy plank prepared in embodiment 1,2.Further, since magnesium-tin-yttrium-zirconium in comparative example
The appearance of the second phase of bulk in sheet alloy becomes tensile fractures source in drawing process, greatly reduces its plasticity.And for
Microalloying magnesium-tin-yittrium alloy without Zr elements, even if there is higher elongation percentage, but the alloy showed bend
Intensity is taken well below the magnesium-tin-yttrium-zircaloy plank prepared in embodiment 1,2, this is because the addition of Zr elements, can have
The crystal grain thinning of effect can contribute a part of plasticity while improving the tensile strength of alloy, therefore, micro- without Zr elements
Alloyed magnesium-tin-yittrium alloy and magnesium-tin-yttrium-zircaloy of high Sn contents are not applied for actual commercial Application, and originally
Magnesium-tin-yttrium-zircaloy plank in invention can obtain magnesium-tin-of high-ductility moderate strength after a hot extrusion process
Yttrium-zircaloy plank has very high industrial application value.
Finally illustrate, preferred embodiment above is merely illustrative of the technical solution of the present invention and unrestricted, although logical
It crosses above preferred embodiment the present invention is described in detail, however, those skilled in the art should understand that, can be
Various changes are made to it in form and in details, without departing from claims of the present invention limited range.
Claims (10)
1. a kind of room temperature high-ductility magnesium-tin-yttrium-zircaloy, which is characterized in that by mass percentage, the magnesium alloy is by such as
The following group is grouped as：Sn 0.2-0.4%；Y 0.4-0.9%；Zr 0.4-0.6%；Inevitable impurity≤0.15%；Surplus is
Magnesium.
2. a kind of room temperature high-ductility magnesium-tin-yttrium-zircaloy as described in claim 1, which is characterized in that by mass percentage
Meter, the magnesium alloy are grouped as by following group：Sn 0.21%；Y 0.41%；Zr 0.46%；Inevitable impurity≤
0.15%；Surplus is magnesium.
3. a kind of room temperature high-ductility magnesium-tin-yttrium-zircaloy as described in claim 1, which is characterized in that by mass percentage
Meter, the magnesium alloy are grouped as by following group：Sn 0.38%；Y 0.90%；Zr 0.52%；Inevitable impurity≤
0.15%；Surplus is magnesium.
4. a kind of preparation method of room temperature high-ductility magnesium-tin-yttrium-zircaloy of claim 1-3 any one of them, feature exist
In described method includes following steps：
(1) melting：Under protective atmosphere, pure magnesium ingot is heated to 670-700 DEG C, the slag hitting after the pure magnesium ingot all fusing,
710-730 DEG C is then heated to, pure tin ingot, magnesium yttrium intermediate alloy and Mg-Zr intermediate alloy is added, melting is sufficiently stirred, in 710-
Magnesium alloy melt is obtained after keeping the temperature 20-30min at 730 DEG C；
(2) it casts：By moulding by casting after the magnesium alloy melt slag hitting obtained in step (1), ingot casting is obtained after air-cooled；
(3) it machines：It will be spare after the ingot casting sawing obtained in step (2), railway carriage；
(4) Homogenization Treatments；
(5) it squeezes.
5. method as claimed in claim 4, which is characterized in that in step (1), the protective atmosphere is CO2And SF6By volume
Than 99：1 mixed gas formed.
6. method as claimed in claim 4, which is characterized in that in step (1), the quality percentage of the magnesium yttrium intermediate alloy yttrium
Than for 28-30%.
7. method as claimed in claim 4, which is characterized in that in step (1), the quality percentage of the Mg-Zr intermediate alloy zirconium
Than for 28-30%.
8. method as claimed in claim 4, which is characterized in that in step (1), the addition pure tin ingot, magnesium yttrium intermediate alloy
Concrete mode with Mg-Zr intermediate alloy is：After pure tin ingot fusing, magnesium yttrium intermediate alloy is added after standing 5min, then wait for
After the magnesium yttrium intermediate alloy fusing, then Mg-Zr intermediate alloy is added after standing 5min.
9. method as claimed in claim 4, which is characterized in that in step (4), the Homogenization Treatments are specially in 350-
12-24h is kept the temperature at 370 DEG C.
10. method as claimed in claim 4, which is characterized in that in step (5), the extruding is specially：By extrusion die and
It is 350-370 DEG C squeezing temperature after the ingot casting of step (4) processing preheats 1-2h at 350-370 DEG C, extrusion speed 6-
10m·min-1, extrusion ratio 33-55:It is carried out under the conditions of 1.
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Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114045421A (en) * | 2021-11-22 | 2022-02-15 | 东北大学 | High-strength-plasticity high-thermal-stability Mg-Sn wrought alloy and preparation method thereof |
| CN114934217A (en) * | 2022-05-25 | 2022-08-23 | 鹤壁海镁科技有限公司 | Microalloy Mg-Sn-Bi-Gd-Zr high-plasticity magnesium alloy and preparation method thereof |
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| CN114934217A (en) * | 2022-05-25 | 2022-08-23 | 鹤壁海镁科技有限公司 | Microalloy Mg-Sn-Bi-Gd-Zr high-plasticity magnesium alloy and preparation method thereof |
| CN114934217B (en) * | 2022-05-25 | 2023-09-26 | 鹤壁海镁科技有限公司 | Micro-alloy Mg-Sn-Bi-Gd-Zr high-plasticity magnesium alloy and preparation method thereof |
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