CN101982553A - Heat resistant magnesium alloy without Al and preparation method thereof - Google Patents
Heat resistant magnesium alloy without Al and preparation method thereof Download PDFInfo
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Abstract
The invention discloses a heat resistant magnesium alloy without Al and a preparation method thereof. The heat resistant magnesium alloy comprises the following components: 3-8% of Sn, 1-3% of Si, 1-3% of Ca and the balance Mg. During smelting, pure Sn, Si and Mg-20% Ca intermediate alloys are added to the magnesium melt and the smelting temperature ranges from 750 DEG C to 800 DEG C. In the invention, Sn and Si are used as the alloying elements so as to generate the heat resistant strengthening phases Mg2Sn and Mg2Si with high stability and Ca is added to control the morphology of Mg2Si so as to achieve the aim of refining, and meanwhile, the CaMgSi alloy phase can be generated after Ca compounding. The heat resistant magnesium alloy does not contain Al, has simple preparation method, low cost and easily controlled addition and shows excellent high temperature creep resistance.
Description
Technical field
The present invention relates to a kind of heat resistance magnesium alloy that does not contain Al and preparation method thereof, being specifically related to a kind of Mg-Sn-Si-Ca is heat resistance magnesium alloy and preparation method thereof.
Background technology
Magnesium alloy has other structural metallic materials incomparable advantage with its unique lightweight characteristic in automobile " loss of weight, energy-conservation and reduction of discharging ".But, relatively poor heat-resisting (heat resistance energy and the high temperature and creep resistance) of magnesium alloy makes its application at automotive field be subjected to certain restriction, how to improve the strong and high-temperature creep resistance of heat of magnesium alloy, the heat resistance magnesium alloy of development of new is the major issue that numerous investigators pay special attention to always.Wherein main heat resistance magnesium alloy system has Mg-Al system and Mg-RE (rare earth element) to be.
Mg-Al be most widely used in the alloy be Mg-Al-Zn system (AZ) alloy, but the creep property of such alloy is relatively poor, use temperature can not be above 120 ℃.For further improving its resistance toheat, the investigator has developed further that Mg-Al-Si (AS) is, Mg-Al-Ca (AC) is, Mg-Al-Sr (AJ) is, Mg-Al-RE (AE) is etc., as publication number is that 1119679,1341767,1431328,1431329,101067178 Chinese patent all relates to one or more in enterprising step compound RE, Ca, Sr, Si, the elements such as Sb, Bi in Mg-Al alloy basis, thus develop have high creep resistance more can heat resistance magnesium alloy.With AZ be the alloy phase ratio, the creep property of AS, AC, AJ and AE system improves, but increase rate is limited.Its reason is that mainly Mg-Al is the Mg-Al eutectic reaction temperature low (437 ℃) of alloy, and contains hot mastication phase Mg
17Al
12Although elements such as composite S i, Ca, Sr and RE can generate high-temperature stable mutually in the Mg-Al alloy, because of Mg
17Al
12Existence its High-Temperature Strengthening effect is weakened.Based on this, no Al changes into the main direction into the exploitation of high-temperature heat-resistance magnesium alloy.
The heat resistance magnesium alloy of no Al mainly contains Mg-Zn system and Mg-RE is a heat resistance magnesium alloy.With Mg-Al base alloy phase ratio, also there is eutectic reaction temperature low (437 ℃) in the Mg-Zn base alloy, problem such as MgZn phase high temperature is easily softening down, so the increase rate of its resistance toheat is still limited.Comparatively speaking, Mg-RE is that alloy is more extensive with the concern that its excellent heat resisting is subjected to.Because of the precipitated phase that contains RE has high thermostability usually, RE element rate of diffusion in magnesium matrix is slower simultaneously, make the Mg-RE alloy have higher high temperature strength and good creep-resistant property, with Mg-Al system and Mg-Zn be the alloy phase ratio, Mg-RE is the component that are used in 200～300 ℃ of following long term operations.Recent years, the domestic patent that discloses serial relevant Heat Resistant Rare Earth-magnesium Alloy is as Mg-Gd-Y system (publication number 1804083), Mg-Y-Sm-Zr (publication number 1814837), Mg-Gd-Mn-Sc (publication number 101058861), Mg-Y-Gd-Zn-Mn (publication number 101148724), Mg-Gd-Y-Sm-Zr (publication number 101532106 and 101532107).Disclosed heat resistance magnesium alloy is main alloy element with rare earth all in the above-mentioned patent, and wherein the content of rare earth element is all more than 10%.Because of rare earth costs an arm and a leg, Mg-RE is that the production and the manufacturing cost of heat resistance magnesium alloy is very high, is mainly used in fields such as aerospace at present, is difficult to promote the use of at civil area.In the heat resistance magnesium alloy of no Al, publication number is that 101397623 and 101392345 Chinese patent discloses Mg-Cu-Y system respectively and Mg-Ni-Y is a heat resistance magnesium alloy.
From Mg-Si and Mg-Sn binary phase diagram as can be known, Si and Sn can react respectively with Mg and generate dystectic Mg
2Si (fusing point is 1083 ℃) and Mg
2Sn (fusing point is 771 ℃) phase, and Mg-Mg
2Si, Mg-Mg
2Sn eutectic reaction temperature is respectively 638 ℃ and 561 ℃.As seen, no matter Mg-Si and Mg-Sn alloy are that the thermostability or the eutectic reaction temperature of the compound that generates all is significantly higher than Mg-Al and Mg-Zn alloy.Therefore, composite S i or Sn all should significantly improve its high-temperature creep resistance in the Mg alloy.And compare with rare earth element, Sn and Si have significant advantage in price.It is main alloy element that the present invention selects Sn and Si, and the Mg-Sn-Si that intends disclose a kind of Al of nothing is a heat resistance magnesium alloy, and compound a spot of Ca element to be controlling and to improve the tissue of this alloy system, thereby improves its performance.Recently, publication number is that 101161840 Chinese patent discloses a kind of Mg-Sn-Si alloy, and utilizing high temperature (490～550 ℃), long-time (way of 1～4h) insulation can effectively change eutectic Mg
2The form of Si phase, but this method treatment temp height, the time is long, and energy consumption is big, and creep-resistant property is general.
Summary of the invention
The objective of the invention is to overcome the defective of prior art, a kind of heat resistance magnesium alloy that does not contain Al and preparation method thereof is provided.The present invention utilizes Si and Sn to react the intermetallic compound Mg that generates high thermal stability respectively with Mg
2Si and Mg
2The Sn phase, and utilize the Ca Mg that can effectively go bad
2This characteristic of Si phase morphology, thus a kind of low cost of Al, heat resistance magnesium alloy of high creep resistance energy of not containing obtained.
Purpose of the present invention realizes by following technical solution.
A kind of heat resistance magnesium alloy that does not contain Al contains following composition: Mg, Sn, Si and Ca; The weight percent of each composition is: Sn 3～8%, Si1～3%, Ca 1～3%, surplus is Mg.
The weight percent of each composition is preferably: Sn 4～8%, Si1～3%, Ca 1～3%, surplus is Mg.
The described method that does not contain the heat resistance magnesium alloy of A1 specifically may further comprise the steps:
(1) melts pure Mg down at 750～800 ℃, keep 750～800 ℃, in the magnesium melt, add pure Sn, pure Si and Mg-20%Ca master alloy by prescription;
(2) stir, be incubated 10 minutes again, obtain the Mg-Sn-Si-Ca melt;
(3) the Mg-Sn-Si-Ca melt is carried out refining after, melt is molded into metal die through 300 ℃ of preheatings, promptly get the heat resistance magnesium alloy that does not contain Al.
Described prescription is the weight percent of each composition in the finished product: Sn 3～8%, Si1～3%, Ca 1～3%, and surplus is Mg.
Described prescription is the weight percent of each composition in the finished product, and preferred: Sn 4～8%, Si1～3%, Ca 1～3%, surplus is Mg.
The present invention is an alloy element with Sn and Si, has the heat-resisting strengthening phase Mg of high stability with generation
2Sn and Mg
2Si, and the purpose of adding Ca is to control Mg
2The form of Si reaches the purpose of refinement, and Ca also can generate the CaMgSi alloy phase after compound simultaneously.The present invention compares with prior art, has following advantage and beneficial effect:
(1) do not contain Al in the heat resistance magnesium alloy disclosed in this invention, can overcome the Mg that is generated in the heat resistance magnesium alloy that contains Al
17Al
12Instable problem under the phase high temperature.
(2) alloying element in the disclosed heat resistance magnesium alloy system is common element among the present invention, and is with low cost, compares with magnesium-rare earth, has significant cost advantage.
(3) utilize common castmethod can prepare this heat resistance magnesium alloy, manufacture method is simple, and is with low cost.
(4) the heat resistance magnesium alloy Good Heat-resistance of being developed, under 250 ℃ and 60MPa stress condition, with AZ91 alloy phase ratio, its creep-resistant property improves 10～30 times, compares with Mg-3Sn-1Si, the highlyest improves 74 times.
Description of drawings
Fig. 1 is the SEM photo of Mg-5Sn-2Si alloy;
Fig. 2 is the XRD figure spectrum of Mg-5Sn-2Si alloy;
Fig. 3 is the SEM photo of Mg-5Sn-2Si-2Ca alloy;
Fig. 4 is the XRD figure spectrum of Mg-5Sn-2Si-2Ca alloy;
The creep strain curve that Fig. 5 is AZ91, Mg-5Sn, Mg-5Sn-2Si and four kinds of alloy materials of Mg-5Sn-2Si-2Ca under 250 ℃ and the effect of 60MPa tensile stress;
The creep strain curve that Fig. 6 is AZ91, Mg-3Sn-1Si and three kinds of alloy materials of Mg-3Sn-1Si-1Ca under 250 ℃ and the effect of 60MPa tensile stress;
The creep strain curve that Fig. 7 is AZ91, Mg-8Sn-3Si and three kinds of alloy materials of Mg-8Sn-3Si-3Ca under 250 ℃ and the effect of 60MPa tensile stress.
Embodiment
In order to understand technical characterstic of the present invention better, the present invention is further illustrated below in conjunction with embodiment, need to prove, embodiment is not a limiting the scope of the invention.
The preparation of embodiment 1Mg-5Sn-2Si-2Ca alloy
The used starting material of present embodiment comprise pure Mg, pure Sn, pure Si and Mg-20%Ca master alloy.The preparation method is: melt the pure Mg of 332g down at 770 ℃, (component is 45wt%MgCl to utilize insulating covering agent in the melting process
2, 35wt%KCl, 10wt%CaF
2, 10wt%NaCl) 2g covers to prevent the magnesium scaling loss.Treat that (Sn 5% according to prescription in pure Mg fusing back, Si 2%, and Ca 2%, and all the other are Mg) add the pure Sn of 20g, the pure Si of 8g and 40g Mg-20%Ca master alloy successively, continue insulation 10 minutes at 770 ℃, stir 1 minute melt then to guarantee that alloying element is uniformly dispersed in melt.Continue insulation again after 10 minutes, utilize C
2Cl
6Melt is carried out refining.Then the magnesium melt is molded in the metal die of 300 ℃ of preheatings, thereby to the Mg-5Sn-2Si-2Ca alloy.For contrast, Mg-5Sn and Mg-5Sn-2Si alloy have also been prepared in the present embodiment.In addition, also prepared AZ91 (Mg-9Al-1Zn) alloy sample that is most widely used in the industrial production.
For above-mentioned alloy organizing and performance thereof are described, present embodiment at first utilizes the metallographic specimen preparation procedure of standard to prepare and organizes observing samples, and utilize electronic scanning Electronic Speculum (SEM) to observe its tissue, utilize X-ray diffraction (XRD) method to determine its phase composite.And prepared the tensile creep sample, measure the high temperature creep property of above-mentioned alloy.
SEM photo and the XRD figure spectrum that is respectively the Mg-5Sn-2Si alloy illustrated in figures 1 and 2.
As can be seen from Figure 1, contain the crystalline phase of thick branch in the Mg-5Sn-2Si alloy structure, the sheet phase of dark white, other parts should be the Mg matrix.From XRD analysis result (shown in Figure 2) as can be seen, the Mg-5Sn-2Si alloy is mainly by Mg, Mg
2Si and Mg
2Sn.Analyze as can be known in conjunction with XRD figure spectrum and scanning electron microscope power spectrum (EDS) thereof, wherein thick branch is crystalline to be Mg mutually
2Si, and the sheet of dark white is Mg mutually
2Sn.
Fig. 3 and SEM photo and the XRD figure spectrum that is respectively the Mg-5Sn-2Si-2Ca alloy shown in Figure 4.
As can be seen from Figure 3, with Mg-5Sn-2Si alloy phase ratio, the obvious refinement of Mg-5Sn-2Si-Ca alloy organizing.From XRD analysis result (shown in Figure 4) as can be seen, the phase composite of Mg-5Sn-2Si-Ca alloy is except Mg, Mg
2Si and Mg
2Outside the Sn, formed a kind of new compound phase CaMgSi in addition.In conjunction with XRD figure spectrum and sem energy spectrum analysis thereof as can be known, the compound that is particle aggregation shape feature in the SEM photo is Mg mutually
2Si, after Ca is compound, Mg
2The dendroid characteristic disappear that Si is mutually thick shows good stigma of degeneracy.And flaky Mg
2Sn still keeps its original form mutually, and Ca is compound to be had no significant effect its form.Analyze through EDS, be radial growth in the tissue or thick flaky compound is the CaMgSi phase.
As seen, behind complex Ca on the basis of Mg-Sn-Si alloy system, one side is the refinement alloy structure effectively, can realize Mg especially
2The morphology Control of Si phase, it is gone bad by thick dendroid is particulate state.Simultaneously, in alloy, can also generate new intermetallic compound CaMgSi.
Figure 5 shows that AZ91, Mg-5Sn, Mg-5Sn-2Si and four kinds of alloy materials of Mg-5Sn-2Si-2Ca at 250 ℃, the creep curve under the constant action of pulling stress of 60MPa.Along with the prolongation of creep time, the deflection of sample increases gradually.Can obtain alloy creep tension set and minimum creep rate based on creep curve, wherein the creep rupture unit elongation is defined as the ratio between deflection and the gauge length (18mm), and minimum creep rate ratio between unit elongation and the deformation time when being defined as state creep stage.
Under 250 ℃ and 60MPa effect, creep rupture took place in the AZ91 alloy in the time of 3.1 hours, and its creep rupture unit elongation is very low, only is 1.4%, and its minimum creep rate is 0.00451/h; And to the Mg-5Sn alloy, its Deformation velocity is very fast, and creep rupture promptly took place at 1.1 hours, and the creep rupture unit elongation is 13.5%, and its minimum creep rate is 0.09151/h; And the Mg-5Sn-2Si alloy that in the Mg-5Sn alloy, obtains behind the compound 2%Si, its rate of deformation has reduction slightly, and creep rupture takes place behind stretching 4.14h, and the creep rupture unit elongation is reduced to 3.9%, and minimum creep rate is 0.009671/h.But for Mg-5Sn-2Si-2Ca, under 250 ℃ and 60MPa envrionment conditions, the creep strain amount of this material increases slow increase in time, and creep time arrives and do not rupture yet more than 50 hours, and its minimum creep rate is 0.00021/h.
In the practice, generally with the evaluation index of minimum creep rate as the measurement creep-resistant property, for the Mg-5Sn-2Si-2Ca alloy, its minimum creep rate is respectively 1/457,1/48 and 1/22 of Mg-5Sn, Mg-5Sn-2Si and AZ91 alloy.As seen, the Mg-5Sn-2Si-2Ca alloy shows excellent creep-resistant property, and with AZ91 alloy phase ratio, this alloy creep resisting ability has improved about 22 times.
The preparation of embodiment 2Mg-3Sn-1Si-1Ca alloy
The used starting material of present embodiment comprise pure Mg, pure Sn, pure Si and Mg-20%Ca master alloy.The preparation method is: melt the pure Mg of 364g down at 750 ℃, (component is 45wt.%MgCl to utilize insulating covering agent in the melting process
2, 35wt.%KCl, 10wt.%CaF
2, 10wt.%NaCl) 2g covers to prevent the magnesium scaling loss.Treat that pure Mg fusing back adds the pure Sn of 12g, the pure Si of 4g and 20g Mg-20%Ca master alloy successively according to prescription (Sn 3%, Si1%, Ca 1%, all the other are Mg).Continue down insulation 10 minutes at 750 ℃, stir melt 1 minute then, continue insulation again after 10 minutes, utilize C to guarantee that alloying element is uniformly dispersed in melt
2Cl
6Melt is carried out refining.Then the magnesium melt is molded in the metal die of 300 ℃ of preheatings, thereby obtains the Mg-3Sn-1Si-1Ca alloy.For contrast, also prepared AZ91 (Mg-9Al-1Zn) alloy sample that is most widely used in Mg-3Sn-1Si and the industrial production in the present embodiment.
Present embodiment has also carried out tissue observation and creep property test to Mg-3Sn-1Si and Mg-3Sn-1Si-1Ca alloy.Fabric analysis shows, Mg-3Sn-1Si and Mg-3Sn-1Si-1Ca alloy have similar tissue signature to Mg-5Sn-2Si among the embodiment 1 with Mg-5Sn-2Si-2Ca, and difference is that the quantity of alloy phase is less relatively.
Figure 6 shows that three kinds of alloy materials of AZ91, Mg-3Sn-1Si and Mg-3Sn-1Si-1Ca at 250 ℃, the creep curve under the constant action of pulling stress of 60MPa.Along with the prolongation of creep time, the deflection of sample increases gradually.Can obtain alloy creep tension set and minimum creep rate based on creep curve, wherein the definition of creep rupture unit elongation and minimum creep rate is identical with embodiment 1.
Under 250 ℃ and 60MPa effect, creep rupture took place in the AZ91 alloy in the time of 3.1 hours, and its creep rupture unit elongation is very low, only is 1.4%, and its minimum creep rate is 0.00451/h; And very fast relatively to the creep strain speed of Mg-3Sn-1Si alloy, creep rupture promptly took place after 2.3 hours, the creep rupture unit elongation is 5.6%, its minimum creep rate is 0.02441/h; But for Mg-3Sn-1Si-1Ca, under 250 ℃ and 60MPa envrionment conditions, the creep strain amount of this material increases slow increase in time, creep time arrives and does not rupture yet more than 55 hours, its minimum creep rate is 0.000331/h, and this minimum creep rate is respectively 1/74 and 1/13 of Mg-3Sn-1Si and AZ91 alloy.As seen, the Mg-3Sn-1Si-1Ca alloy shows excellent creep-resistant property, and with AZ91 alloy phase ratio, this alloy creep resisting ability has improved about 13 times, and compares with Mg-3Sn-1Si, and this alloy creep resisting ability has improved about 74 times.
The preparation of embodiment 3Mg-8Sn-3Si-3Ca alloy
The used starting material of present embodiment comprise pure Mg, pure Sn, pure Si and Mg-20%Ca master alloy.The preparation method is: melt the pure Mg of 296g down at 800 ℃, (component is 45wt.%MgCl to utilize insulating covering agent in the melting process
2, 35wt.%KCl, 10wt.%CaF
2, 10wt.%NaCl) 2g covers to prevent the magnesium scaling loss; Treat that (Sn 8% according to prescription in pure Mg fusing back, Si 3%, and Ca 3%, and all the other are Mg) add the pure Sn of 32g, the pure Si of 12g and 60g Mg-20%Ca master alloy successively, continue down insulation 10 minutes at 800 ℃, stir melt 1 minute then to guarantee that alloying element is uniformly dispersed in melt.Continue insulation again after 10 minutes, utilize C
2Cl
6Melt is carried out refining.Then the magnesium melt is molded in the metal die of 300 ℃ of preheatings, thereby makes the Mg-8Sn-3Si-3Ca alloy.For contrast, also prepared AZ91 (Mg-9Al-1Zn) alloy sample that is most widely used in Mg-8Sn-3Si and the industrial production in the present embodiment.
Present embodiment has also carried out tissue observation and creep property test to Mg-8Sn-3Si and Mg-8Sn-3Si-3Ca alloy.Fabric analysis shows, Mg-8Sn-3Si and Mg-8Sn-3Si-3Ca alloy have similar tissue signature to Mg-5Sn-2Si among the embodiment 1 with Mg-5Sn-2Si-2Ca, and difference is that the quantity of alloy phase significantly increases.
Figure 7 shows that three kinds of alloy materials of AZ91, Mg-8Sn-3Si and Mg-8Sn-3Si-3Ca at 250 ℃, the creep curve under the constant action of pulling stress of 60MPa.Along with the prolongation of creep time, the deflection of sample increases gradually.Can obtain alloy creep tension set and minimum creep rate based on creep curve, wherein the definition of creep rupture unit elongation and minimum creep rate is identical with embodiment 1.
Under 250 ℃ and 60MPa effect, creep rupture took place in the AZ91 alloy in the time of 3.1 hours, and its creep rupture unit elongation is very low, only is 1.4%, and its minimum creep rate is 0.00451/h; And for Mg-8Sn-3Si and Mg-8Sn-3Si-3Ca alloy, its creep strain speed is all slower.For the Mg-8Sn-3Si alloy, creep rupture promptly took place after 32 hours, the creep rupture unit elongation is 4.5%, its minimum creep rate is 0.001381/h; But for Mg-8Sn-3Si-3Ca, under 250 ℃ and 60MPa envrionment conditions, the creep strain amount of this material increases slow increase in time, and creep time arrives and do not rupture yet more than 60 hours, and its minimum creep rate is 0.000151/h.As seen, Mg-8Sn-3Si alloy ratio AZ91 alloy has lower minimum creep rate, also shows creep-resistant property preferably.And for the Mg-8Sn-3Si-3Ca alloy, its creep speed is lower, is 1/30 of AZ91 alloy, shows excellent creep-resistant property, and with AZ91 alloy phase ratio, this alloy creep resisting ability has improved about 30 times.
Claims (5)
1. a heat resistance magnesium alloy that does not contain Al is characterized in that, contains following composition: Mg, Sn, Si and Ca; The weight percent of each composition is: Sn 3～8%, Si1～3%, Ca 1～3%, surplus is Mg.
2. a kind of heat resistance magnesium alloy that does not contain Al according to claim 1 is characterized in that the weight percent of each composition is: Sn 4～8%, Si1～3%, Ca1～3%, surplus are Mg.
3. preparation claim 1 or the 2 described methods that do not contain the heat resistance magnesium alloy of Al is characterized in that, specifically may further comprise the steps:
(1) melts pure Mg down at 750～800 ℃, keep 750～800 ℃, in the magnesium melt, add pure Sn, pure Si and Mg-20%Ca master alloy, be incubated 10 minutes by prescription;
(2) stir, be incubated 10 minutes again, obtain the Mg-Sn-Si-Ca melt;
(3) the Mg-Sn-Si-Ca melt is carried out refining after, melt is molded into metal die through 300 ℃ of preheatings, promptly get the heat resistance magnesium alloy that does not contain Al.
4. method according to claim 3 is characterized in that, described prescription is the weight percent of each composition in the finished product: Sn 3～8%, Si1～3%, Ca 1～3%, and surplus is Mg.
5. method according to claim 4 is characterized in that, described prescription is the weight percent of each composition in the finished product: Sn 4～8%, Si1～3%, Ca 1～3%, and surplus is Mg.
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Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104278179A (en) * | 2013-12-13 | 2015-01-14 | 济南大学 | Si-intensified Mg-Sn casting magnesium alloy material |
| CN107400813A (en) * | 2017-09-22 | 2017-11-28 | 广州宇智科技有限公司 | Mg Li Si magnesium lithium alloys and its processing technology with anti-flammability |
| CN109881060A (en) * | 2019-03-26 | 2019-06-14 | 华南理工大学 | A kind of corrosion-resistant magnesium alloy and preparation method thereof containing Si |
| CN115679172A (en) * | 2022-11-10 | 2023-02-03 | 南昌大学 | Ultrahigh-conductivity hot-pressed cast magnesium alloy and preparation method thereof |
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| CN101161840A (en) * | 2007-11-29 | 2008-04-16 | 哈尔滨工程大学 | Mg-Si-Sn series magnesium alloy and heat treatment process for deteriorate Chinese character shaped eutectic Mg2Si phase therein |
| CN101440449A (en) * | 2008-12-23 | 2009-05-27 | 重庆大学 | Multicomponent heat resisting magnesium alloy and preparation thereof |
| CN101463441A (en) * | 2009-01-15 | 2009-06-24 | 上海交通大学 | Rare earth-containing high strength heat resisting magnesium alloy and preparation thereof |
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2010
- 2010-09-21 CN CN2010102912526A patent/CN101982553B/en not_active Expired - Fee Related
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101161840A (en) * | 2007-11-29 | 2008-04-16 | 哈尔滨工程大学 | Mg-Si-Sn series magnesium alloy and heat treatment process for deteriorate Chinese character shaped eutectic Mg2Si phase therein |
| CN101440449A (en) * | 2008-12-23 | 2009-05-27 | 重庆大学 | Multicomponent heat resisting magnesium alloy and preparation thereof |
| CN101463441A (en) * | 2009-01-15 | 2009-06-24 | 上海交通大学 | Rare earth-containing high strength heat resisting magnesium alloy and preparation thereof |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104278179A (en) * | 2013-12-13 | 2015-01-14 | 济南大学 | Si-intensified Mg-Sn casting magnesium alloy material |
| CN107400813A (en) * | 2017-09-22 | 2017-11-28 | 广州宇智科技有限公司 | Mg Li Si magnesium lithium alloys and its processing technology with anti-flammability |
| CN109881060A (en) * | 2019-03-26 | 2019-06-14 | 华南理工大学 | A kind of corrosion-resistant magnesium alloy and preparation method thereof containing Si |
| CN109881060B (en) * | 2019-03-26 | 2021-05-14 | 华南理工大学 | Si-containing corrosion-resistant magnesium alloy and preparation method thereof |
| CN115679172A (en) * | 2022-11-10 | 2023-02-03 | 南昌大学 | Ultrahigh-conductivity hot-pressed cast magnesium alloy and preparation method thereof |
| CN115679172B (en) * | 2022-11-10 | 2023-11-28 | 南昌大学 | Ultrahigh-heat-conductivity die-casting magnesium alloy and preparation method thereof |
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