CN100366775C - High strength creep-resisting magnetium base alloy - Google Patents
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Abstract
The present invention relates to magnesium base alloy which comprises at least 85.4 wt% of magnesium (Mg), 4.7 to 7.3 wt% of aluminium (Al), 0.17 to 0.60 wt% of manganese (Mn), 0.0 to 0.8 wt% of zinc (Zn), 1.8 to 3.2 wt% of calcium (Ca), 0.3 to 2.2 wt% of stannum (Sn)and 0.0 to 0.5 wt% of strontium (Sr). The alloy also contains at most 0.004 wt% of ferrum (Fe), at most0.001 wt% of nickel (Ni), at most 0.003 wt% of copper (Cu) or at most 0.03 wt% of silicon (Si). In addition, the alloy contains at most 0.001 wt% of beryllium (Be).
Description
Technical Field
The present invention relates to a high strength magnesium based alloy with good creep resistance, which is suitable for use at high temperatures, even at 175-200 ℃.
Background
Magnesium alloys, which are 1/3 lighter than an equal volume of aluminum, are the lightest structural materials in the automotive industry. Vehicle weight and fuel economy are increasingly important in the automotive industry. By 2010, automobile manufacturers in Europe and North magnesium will reduce fuel consumption by 25%, and in turn will achieve a 30% reduction in CO 2 And (5) discharging. Therefore, the alloy will become more attractive.
Most transmission components are produced by high pressure die casting. This technique presumably has the largest production volume in processes using magnesium alloys, and seems to remain so even in the future. However, other techniques are also used, including sand and metal mold casting, pressure casting, semi-solid casting, thixocasting (thixocasting), and thixomolding (thixomolding).
Alloy cost is an important proportion of the total component cost and is an important factor in developing new alloys. In addition to being cost effective, an ideal magnesium alloy for use in the manufacture of automotive parts should meet certain conditions relating to its properties during casting and when used under continuous stress. Good casting properties include good fluidity of the molten alloy to enter the thin mold sections, low adhesion of the molten alloy to the mold, and oxidation resistance during casting. A good alloy should not crack during the cooling and solidification stages of casting. The alloy cast part should have high tensile and compressive yield strengths and should exhibit low continuous strain (creep resistance) in service under high temperature stress conditions. Good mechanical properties should be maintained if the component is used as a component of a gearbox or crankcase, even at temperatures above 120 ℃. However, some transmission components, such as the engine block, oil pan, intake manifold, lower crankcase, oil pump housing, and others, should withstand even higher temperatures. Improving creep resistance and stress relaxation properties is a key issue for the alloys used to make these components. The alloy should also have corrosion resistance. The physical and chemical properties of the alloy are essentially determined by the presence of other metallic elements which form various intermetallic compounds. These intermetallic compounds inhibit grain sliding under high temperature stress conditions.
One procedure known in the art to improve the stability of metal mixtures is heat treatment, known as aging, which affects the microstructure of the metal. However, the existing commercial die cast magnesium alloys do not respond significantly to aging.
All of the normal-scale cast magnesium alloys are based on the Mg-Al system. Alloys of the Mg-Al-Zn system (e.g. the commercially available alloy AZ 91D) or alloys of the Mg-Al-Mn system with a combination of good castability, corrosion resistance, environmental strength and ductility, but they show poor creep resistance and poor high temperature strength. On the other hand, mg-Al-Si alloys and Mg-Al-RE alloys have better creep resistance, but show insufficient corrosion resistance (AS 41 and AS21 alloys) and poor casting properties (AS 21 and AE42 alloys). Both types of alloys still further exhibit relatively low tensile yield strength at ambient temperature. In addition, high amounts of rare earth elements, such as 2.4% in AE42, increase costs.
The introduction of other alloying elements in the alloy overcomes some of the disadvantages mentioned. German patent specification NO847992 describes magnesium based alloys containing up to 3% by weight calcium, exhibiting a creep strain of less than 0.2% at 200 c and under stress applied at 30MPa for 50 hours. GB2296256 discloses magnesium based alloys containing up to 2 wt% RE and up to 5.5 wt% calcium, claiming a creep rate of 0.01% per 50 hours. WO9625529 discloses magnesium based alloys containing up to 0.8 wt% calcium with creep strain of less than 0.5% at 150 ℃ for 200 hours under applied 35MPa stress. EP799901 describes a semi-solid cast magnesium based alloy containing up to 4 wt% calcium and up to 0.15 wt% strontium, where the ratio Ca/Al should be less than 0.8.EP791662 discloses magnesium based alloys containing up to 3 wt% Ca and up to 3 wt% RE elements, wherein the alloy is die castable only when the elements reach a certain ratio, claiming increased strength at higher temperatures. EP1048743 teaches a method of making cast magnesium alloys comprising up to 3.3% Ca and up to 0.2% Sr, purportedly having improved creep resistance at 150-175 ℃. WO0144529 claims a diecasting alloy which contains up to 7% strontium and which has a creep deformation of 0.06% at 150 ℃. U.S. patent No.6139651 discloses a magnesium based alloy containing up to 1.2 wt% Ca, up to 0.2 wt% Sr, up to 1 wt% RE, up to 0.0015 wt% beryllium, but with Zn in the range of 0.01-1 wt% or 5-10 wt%. The alloy exhibits excellent castability, corrosion resistance and mechanical properties and is indicated to be operable at temperatures up to 150 ℃. However, in order to expand the use of magnesium for crankcase and engine blocks that can operate at temperatures above 150 ℃, there is still a need for higher resistance alloys. It is therefore an object of the present invention to provide a magnesium alloy capable of operating at high temperatures of 175-200 ℃. It is an object of the present invention to provide an alloy with improved strength at ambient and elevated temperatures and improved creep resistance at elevated temperatures up to a temperature range of 175-200 ℃.
It is another object of the present invention to provide an alloy which is particularly suitable for high pressure die casting processes, which shows low sensitivity to die sticking, oxidation and heat cracking, and which has good flowability.
It is yet another object of the present invention to provide a magnesium-based alloy suitable for use at high temperatures that has good corrosion resistance.
It is a further object of the present invention to provide alloys that can also be used in other applications, such as sand casting, metal casting, pressure casting, semi-solid casting, thixocasting, and thixomolding.
It is still a further object of the present invention to provide an alloy that can be successfully cast despite being beryllium-free. It is a further object of the present invention to provide an alloy which exhibits improved strength during aging. It is a further object of the present invention to provide an alloy which exhibits the said characteristics and properties and which has a relatively low cost.
Other objects and advantages of the present invention will become apparent from the following description.
Disclosure of Invention
The present invention relates to a high strength magnesium based alloy with good creep resistance, which is suitable for use at high temperatures, even at 175-200 ℃. The alloy according to the invention has good castability and shows good corrosion resistance. The alloys include aluminum, manganese, zinc, calcium, tin, strontium, and beryllium. The alloy of the present invention contains at least 85.4 wt.% Mg,4.5-7.5 wt.% aluminum, 0.17-0.6 wt.% manganese, 0.0-0.8 wt.% zinc, 1.8-3.2 wt.% calcium, 0.3-2.2 wt.% tin, 0.0-0.5 wt.% strontium, and 0.000-0.001 wt.% beryllium. The contents of iron, nickel, copper and silicon in the alloy do not exceed 0.004 wt%, 0.001 wt%, 0.003 wt% and 0.03 wt%, respectively.
The microstructure of the alloy according to the invention contains a solid solution of Mg-Al or a solid solution of Mg-Al-Sn as a matrix and an intermetallic phase precipitated at the grain boundaries of the Mg-Al or Mg-Al-Sn matrix. The intermetallic compound present in the alloy of the invention is Al 2 Ca，Al 2 (Ca，Sr)，Al 2 (Ca，Sn)， Al 2 (Ca，Sn，Sr)，Al x Mn y Wherein the ratio of "x" to "y" is determined by the aluminum content of the alloy.
The alloys of the present invention are particularly suitable for high pressure die casting due to reduced susceptibility to hot cracking and die sticking. The present invention also relates to alloys that may be used in other processes including sand casting, metal die casting, squeeze casting, semi-solid casting, thixocasting (thixocasting), and thixomolding (thixomolding).
The present invention still further relates to articles produced by casting a magnesium-based alloy having the composition as described above, which alloy exhibits high strength, good creep resistance and castability, is suitable for use at high temperatures, and has good corrosion resistance.
Drawings
The above and other features and advantages of the present invention will be more readily apparent from the following examples and by reference to the accompanying drawings in which:
FIG. 1 is Table 1 showing the chemical composition of the alloy;
FIG. 2 is Table 2 showing the castability of the new alloys;
FIG. 3 is Table 3 showing intermetallic phases in the new alloy;
FIG. 4 is Table 4 showing the mechanical properties and creep characteristics of the alloys;
FIG. 5 is Table 5 showing the effect of aging on the mechanical properties of the alloy;
FIGS. 6,A and B, respectively, show the microstructures of die cast alloys according to examples 1 and 3;
FIGS. 7,A and B, showing the microstructure of die cast alloys according to examples 5 and 7, respectively;
FIGS. 8,A and B, showing the microstructure of die cast alloys according to examples 10 and 12, respectively; and
FIGS. 9,A and B, respectively, show the microstructures of die cast alloys AZ91D (comparative example 1) and AE42 (comparative example 2);
detailed description of the preferred embodiments
It has now been found that certain combinations of elements in magnesium-based alloys, including aluminum, manganese, zinc, calcium, strontium and tin, result in superior performance to that of prior art alloys. These properties include excellent high tensile yield and compressive yield strength at ambient and elevated temperatures, even at 175-200 ℃, excellent creep resistance in the temperature range of 150-200 ℃, good castability and corrosion resistance, a significant response to low temperature aging, and molten metal characteristics. The new alloys show a significant response to aging at 250 ℃, with increased tensile yield strength, compressive yield strength, and creep resistance.
The magnesium-based alloy of the present invention includes 4.7-7.3 wt.% aluminum. If the aluminum concentration is less than 4.7 wt%, the alloy cannot exhibit good fluidity and castability. On the other hand, concentrations of aluminium higher than 7.3% by weight lead to embrittlement and to a deterioration in creep resistance. The alloy of the present invention contains 1.8 to 3.2 weight percent calcium. The presence of calcium in this concentration range leads to a significant improvement in creep resistance and can be carried out with a lower consumption of protective gas, in particular SF 6 Under the conditions of (a), preparing and die casting the alloy, even preparing the alloy without beryllium. Calcium at concentrations below 1.8 wt.% does not ensure sufficient creep resistance. On the other hand, the concentration of calcium should not exceed 3.2 wt.% to avoid embrittlement. An essential feature of the alloy according to the invention is the presence of tin which improves the castability. It was found that tin was present in a concentration of at least 0.3 wt.% to significantly improve castability and wearAnd removing the sticking die. Addition of more than 2.2% tin results in a reduction in the strength of the alloy. The alloy of the present invention contains manganese to reduce the iron content and improve corrosion resistance. The manganese content is dependent on the aluminum content and may vary between 0.17 and 0.6 wt.%. The alloy of the invention may contain up to 0.5 wt% strontium to improve the intermetallic phase and further improve creep resistance. Increasing the strontium concentration, above 0.5% did not significantly improve creep resistance,and also unnecessarily increases costs. The alloy of the invention may contain up to 0.8% zinc to improve castability and strength at ambient temperatures. More than 0.8 wt% of zinc may cause heat cracking.
The alloys of the present invention may contain small amounts of beryllium up to 0.001 weight percent. However, an important feature of the alloy of the present invention is that it can be successfully prepared and cast without beryllium. It is an advantage because beryllium is a toxic metal.
Silicon is a typical impurity present in magnesium used in the preparation of magnesium alloys. Therefore, the magnesium alloy may contain silicon, but the content of silicon should not exceed 0.03 wt%. Iron, nickel and copper are known to significantly reduce the corrosion resistance of magnesium alloys. Thus, the alloy of the present invention contains no more than 0.004 wt.% iron, no more than 0.001 wt.% nickel, and no more than 0.003 wt.% copper.
In a preferred embodiment of the invention, the magnesium based alloy contains 5.9-7.2 wt.% aluminum, 0.9-2.1 wt.% tin, 2.1-3.1 wt.% calcium and 0.2-0.3 wt.% manganese.
It was found that the addition of calcium, tin and strontium in the percentages by weight mentioned herein leads to the precipitation of several intermetallic compounds. In the strontium-free alloy of the present invention, the intermetallic compound Al can be detected at the grain boundary of the Mg-Al solid solution 2 Ca，Al 2 (Ca, sn) and Al x Mn y . In the strontium containing alloy of the present invention, the microstructure includes a Mg-Al solid solution having precipitates at grain boundaries, including the intermetallic compound Al 2 Ca，Al 2 (Ca，Sn)，Al 2 (Ca，Sr)，Al 2 (Ca, sr, sn) and Al x Mn y . The ratio of x to y depends on the aluminum concentration in the alloy.
The magnesium alloys of the present invention have been tested and compared to control samples, including the large range of uses, commercially available, magnesium alloys AZ91D and AE42. Metallographic examination by scanning electron microscopy and X-ray diffraction analysis of the precipitates showed that there was a clear difference between the control sample and the alloy according to the invention, for example the formation of new intermetallic precipitates. The microstructure of the new alloy, for example, consists of fine-grained Mg — Al solid solution and eutectic phases located at grain boundaries.
These phases containing Al, ca, sr and Sn have high melting points under high temperature load conditions and prevent grain sliding.
During casting, the alloy is characterized by a combination of three parameters that impart alloy properties: fluidity, mold sticking property and oxidation resistance, and casting properties can be evaluated. In all of the control samples, only the AZ91D alloy had similar castability to the alloy of the present invention, which was significantly better than the AE42 alloy.
Tensile and compression tests at ambient temperature show that the alloys of the invention have a low elongation and a significantly higher Tensile Yield Strength (TYS) and Compressive Yield Strength (CYS) at ambient temperature and at 175 c, even at 200 c.
The corrosion resistance of the new alloys, determined by immersion in NaCl solution and then by stripping in chromic acid, is within the range set according to the resistance of the alloys AZ91D and AE42.
The creep characteristics were measured at 200 hours under a stress of 100MPa and 55MPa respectively and at a temperature of 150 ℃ and 200 ℃. The conditions are selected based on the requirements of the power transmission components, such as the crankcase, oil pan, intake manifold, etc. Creep resistance is characterized by a minimum creep rate value, which is considered to be the most important design parameter for the powertrain components. The creep resistance of the alloy of the invention is far better than that of the alloy AZ91D and the alloy AE42, and the ratio of the resistance coefficients reaches 3 orders of magnitude.
The alloy of the present invention was aged at 250 ℃ for 1 hour. It was found that by this treatment the alloy was subjected to significant precipitation hardening, resulting in an improvement of all mechanical parameters without affecting the corrosion rate. This potentially provides a significant technical advantage to the alloys of the present invention, since the existing commercial die cast magnesium alloys do not show a significant response to aging. For example, low temperature aging can be combined with other technical processes, such as the use of various coating systems and the like.
In a preferred embodiment, the article made of the alloy according to the invention is high pressure die cast.
In other embodiments of the present invention, articles made from the alloys according to the present invention are cast by selecting a process comprising sand casting, metal die casting, squeeze casting, semi-solid casting, thixocasting, and thixomolding.
Based on the above findings, the present invention also includes articles made from the magnesium alloy composition having improved strength, creep resistance, and good corrosion resistance at ambient and elevated temperatures, wherein the articles are used as components of automotive or aerospace construction systems.
In particular, the invention relates to: an article exhibiting a tensile yield strength at ambient temperature higher than 170MPa and a tensile yield strength at 175 ℃ higher than 150 MPa; exhibits less than 1.7X 10 at 150 ℃ and 100MPa stress -9 (ii) a Minimum Creep Rate (MCR) per second; exhibits less than 4.9X 10 at 200 ℃ and 55MPa stress -9 (ii) a minimum creep rate of/s; the product was aged at 250 ℃ for 1 hour.
The invention is further described and explained in the following examples.
Examples
General procedure
The alloy of the invention is prepared in a bath of 100 litres of low carbon steel. CO 2 2 +0.5％5F 6 The mixture of (a) is used as a protective atmosphere. The raw materials used were as follows:
magnesium alloyPure magnesium, grade 9980A, containing at least 99.8% magnesium.
Manganese oxide-at a melting temperature of 700 ℃ -720 ℃Al-60% Mn master alloy is added to the molten magnesium at DEG C, depending mainly on the magnesium concentration. The special preparation of the loading sheet and the intensive stirring of the melt for 15-30 minutes serve to promote the dissolution of manganese in the molten magnesium.
AluminiumCommercially pure Al (less than 0.2% impurities).
Tin (Sn)Commercially pure tin (less than 0.25% impurities).
Calcium carbonate-master alloy Al-75% ca.
Strontium salt-master alloy Al-90% sr.
ZincCommercial pure Zn (less than 0.1% impurities).
Typical temperatures for adding Al, ca, sr, sn and Zn are 690 deg.C-710 deg.C. The mixture was stirred vigorously for 2-15 minutes to dissolve these elements in the molten magnesium sufficiently.
Beryllium (beryllium)-adding 5-10ppm beryllium in some new alloys in the form of the master alloy Al-1% be after tempering the melt at a temperature of 660-690 ℃ before casting. However, be is not included in the preparation and casting of most new alloys.
After preparation of the desired composition, the alloy was cast into 8kg ingots. In the casting mold, casting is performed without any protection of the molten metal at the solidification stage. No burning or oxidation was observed on the surface of all the test ingots. Chemical analysis was performed using a spark emission spectrometer. The die casting test was conducted using an IDRA OL-320 cold chamber die casting machine with a mold closing force of 345 tons. The metal mold used to produce the test specimens was a six-cavity mold, producing:
two circular samples for the tensile test according to ASTM standard B557M-94,
-one sample suitable for creep testing,
-one sample suitable for fatigue testing,
an astm e23 standard impact test specimen,
a circular sample with a diameter of 10mm, which is used for the immersion corrosion test according to the ASTM G31 standard.
The die castability was evaluated in the die casting test by observing the fluidity (F), the Oxidation Resistance (OR) and the die-sticking property (D). For the three properties, each alloy was rated for an increase in mass from 1 to 10. The combined "casting performance factor" (CF) was calculated by weighing three parameters, where the weighing factor for the die-bond was 4, the flowability and the oxidation, each with a weighing factor of 1:
where T is the actual casting temperature and 670 is the casting temperature of the AZ91D alloy [. Degree.C. ].
Metallographic examination was performed using an optical microscope and a Scanning Electron Microscope (SEM) equipped with an Energy Dispersive Spectrometer (EDS). X-ray diffraction analysis combined with EDS analysis was used to determine the phase composition.
Tensile and compressive tests were performed at ambient and elevated temperature using an Instron4483 machine equipped with a high temperature chamber. Tensile Yield Strength (TYS), ultimate Tensile Strength (UTS) and elongation (% E), and Compressive Yield Strength (CYS) were measured.
SATEC type M-3 machine was used for creep testing. Creep tests were carried out under a stress of 100MPa and 55MPa respectively and at a temperature of 150 ℃ and 200 ℃ for 200 hours. The conditions are selected based on the desired creep characteristics of the power transmission components, such as the crankcase, oil pan, intake manifold, etc. Creep resistance is characterized by a minimum creep rate value (MCR), which is considered to be the most important design parameter for a power transmission component.
The corrosion properties were evaluated using the immersion corrosion test according to ASTM Standard G31-87. Test samples, cylindrical rods 100mm long and 10mm in diameter, were freed from oil stains in acetone and then immersed in 5% NaCl solution at ambient temperature 23. + -.1 ℃ for 72 hours. The test was repeated 5 times for each alloy. Then, at 80 ℃ in a chromic acid solution (1 per liter of solution) over about 3 minutes80gCrO 3 ) In (3), the sample is stripped of corrosion products. Weight loss was determined for calculation in mg/cm 2 Average corrosion rate calculated per day.
Examples of alloys
Tables 1-5 show the chemical composition and properties of the alloys according to the invention and the alloys of the comparative examples. Table 1 shows the chemical composition of 14 new alloys and 5 control examples. Comparative examples 1 and 2 are commercially available magnesium alloys AZ91D and AE42, respectively.
The results of metallographic examination of the new alloy and comparative examples 1 and 2 are shown in figures 6 to 9. The micrographs show very fine grains of Mg-Al solid solution or Mg-Al-Sn solid solution surrounded by precipitates of grain boundary eutectic. These phases were identified using X-ray diffraction analysis and EDS analysis. The results obtained are shown in table 3 together with the data for the control alloy. The table shows that alloying with aluminum, calcium, tin, strontium, manganese and zinc in the weight percentages described herein results in the formation of new intermetallic phases that are different from the intermetallic compounds present in the AZ91D and AE42 alloys.
The die casting properties of the new alloys are shown in table 2. It is clear that the new alloy of the present invention shows significantly better die castability than the AE42 alloy (comparative example 2). Comparative examples 3-5 show that the addition of tin significantly reduces the die-sticking tendency of the Mg-Al-Ca alloy.
The tensile, compressive and creep properties and corrosion resistance of the new alloys are shown in table 4. The results show that at ambient temperature, and in particular at elevated temperatures of 175 ℃ and 200 ℃, the novel alloys of the present invention exhibit Tensile Yield Strength (TYS) and Compressive Yield Strength (CYS) that are significantly higher than those of the common alloys AZ91D and AE42.
As can be seen from the creep characteristics of table 4, the alloys of the present invention exhibit higher Tensile Yield Strength (TYS) and higher Compressive Yield Strength (CYS) at ambient temperature, at 175 ℃ and 200 ℃ when compared to AZ91D alloy, and significantly higher Tensile Yield Strength (TYS) and Compressive Yield Strength (CYS) when compared to AE42 alloy.
As can be seen from Table 4, the greatest advantage of the alloy of the present invention is its creep resistance. The minimum creep rate values (MCR) of the new alloys were reduced by 2 or 3 orders of magnitude when compared to the commercial alloys AZ91D and AE42 at 150 ℃ and 200 ℃. For example, a value of 1429X 10 at 150 ℃ compared with that of alloy AZ91D -9 In contrast, the MCR value of the alloy according to the invention in example 5 is 0.80X 10 -9 /sec。
Table 5 shows the effect of aging at 250 ℃ for 1 hour on the properties of the new alloys. TYS, UTS, E and CYS values were determined at 20 ℃. The table shows values before and after treatment. As can be seen from the table, the aging treatment improved the parameters of most of the studies.
While the invention has been described with respect to certain specific embodiments, many modifications and variations are possible. It is, therefore, to be understood that within the scope of the appended claims, the invention may be practiced otherwise than as specifically described.
Claims (13)
1. A magnesium-based alloy, said alloy comprising:
i) At least 85.4% by weight of magnesium,
ii) 4.7 to 7.3% by weight of aluminium,
iii) 0.17-0.60% by weight of manganese,
iv) up to 0.8% by weight of zinc,
v) 1.8 to 3.2% by weight of calcium,
vi) 0.3 to 2.2% by weight of tin,
vii) up to 0.5% by weight strontium, and
viii) up to 0.004 wt.% iron, up to 0.001 wt.% nickel, up to 0.003 wt.% copper, up to 0.03 wt.% silicon and up to 0.001 wt.% beryllium, and
ix) incidental impurities.
2. The alloy according to claim 1, which contains 5.9-7.2 wt.% of aluminium, 0.9-2.1 wt.% of tin, 2.1-3.1 wt.% of calcium and 0.2-0.35 wt.% of manganese.
3. The alloy according to claim 1, comprising in its structure a Mg-Al solid solution or a Mg-Al-Sn solid solution as matrix, and being selected from Al 9 Ca，Al 2 (Ca，Sr)，Al x Mn y ，Al 9 (Ca, sn) and Al 2 An intermetallic compound of (Ca, sn, sr), wherein the intermetallic compound is located at a grain boundary of a matrix of the Mg-Al solid solution or Mg-Al-Sn solid solution.
4. The alloy according to claim 1, which is beryllium-free.
5. The alloy according to claim 1, which exhibits a tensile yield strength at ambient temperature higher than 170MPa and a tensile yield strength at 175 ℃ higher than 150 MPa.
6. The alloy according to claim 1, which exhibits less than 1.7 x 10 at 150 ℃ and 100MPa stress -9 Minimum Creep Rate (MCR)/s.
7. The alloy according to claim 1, which shows less than 4.9 x 10 at 200 ℃ and 55MPa stress -9 Minimum creep rate in/s.
8. An article which is a casting of the magnesium alloy of any one of claims 1 to 7.
9. The article according to claim 8, wherein the casting process is selected from the group consisting of high pressure die casting, sand casting, metal die casting, squeeze casting, semi-solid casting, thixocasting (thixocasting), and thixomolding (thixomolding).
10. The article according to claim 8, which exhibits a tensile yield strength at ambient temperature higher than 170MPa and a tensile yield strength at 175 ℃ higher than 150 MPa.
11. The article according to claim 8 which exhibits less than 1.7 x 10 at 150 ℃ and 100MPa stress -9 Minimum Creep Rate (MCR)/s.
12. The article according to claim 8 exhibiting less than 4.9 x 10 at 200 ℃ and 55MPa stress -9 Minimum creep rate in/s.
13. The article according to claim 8, which has been aged at 250 ℃ for 1 hour.
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| CN101448964B (en) * | 2006-05-18 | 2011-12-14 | 通用汽车环球科技运作公司 | High strength/ductility magnesium-based alloys for structural applications |
| CN101985714B (en) * | 2010-12-07 | 2012-09-26 | 吉林大学 | High-plasticity magnesium alloy and preparation method thereof |
| CN102337437A (en) * | 2011-09-13 | 2012-02-01 | 四川大学 | High-plasticity casting Mg-Sn-Zn-Al series magnesium alloy |
| CN103834839A (en) * | 2012-11-23 | 2014-06-04 | 天津德盛镁科技发展有限公司 | Novel calcium strontium heat-resistant magnesium alloy |
| CN104480361B (en) * | 2014-11-26 | 2017-01-11 | 沈阳工业大学 | High-strength/toughness heat-resistant die casting magnesium alloy and preparation method thereof |
| CN107250402A (en) * | 2015-02-26 | 2017-10-13 | 株式会社栗本铁工所 | Heat resistance magnesium alloy |
| CN108950333A (en) * | 2018-07-16 | 2018-12-07 | 江苏理工学院 | A kind of high-performance Mg-Al-Zn-Mn-Ca magnesium alloy and preparation method thereof |
| CN113981286B (en) * | 2021-11-01 | 2022-06-21 | 吉林大学 | Corrosion-resistant high-strength plastic magnesium alloy and preparation method thereof |
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- 2003-01-07 CN CNB031031706A patent/CN100366775C/en not_active Expired - Lifetime
Patent Citations (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB524113A (en) * | 1939-01-23 | 1940-07-30 | Tennyson Fraser Bradbury | Magnesium alloy |
| GB596102A (en) * | 1945-07-19 | 1947-12-29 | Rupert Martin Bradbury | A new magnesium base alloy |
| JPS613863A (en) * | 1984-06-15 | 1986-01-09 | Ube Ind Ltd | Die casting magnesium alloy |
| CN1127306A (en) * | 1994-07-12 | 1996-07-24 | 宇部兴产株式会社 | Creep-resisting, corrosion-resisting magnesium alloy |
| CN1174243A (en) * | 1996-04-04 | 1998-02-25 | 玛志达株式会社 | Heat-resisting magensium alloy forming member, heat-resisting magnesium alloy for forming and forming method thereof |
| CN1210897A (en) * | 1997-05-21 | 1999-03-17 | 爱信高冈株式会社 | Magnesium alloy having superior elevated-temperature properties and die castability |
| EP1048743A1 (en) * | 1999-04-30 | 2000-11-02 | General Motors Corporation | Creep-resistant magnesium alloy die castings |
| EP1108799A2 (en) * | 1999-12-03 | 2001-06-20 | Hitachi, Ltd. | High strength Mg based alloy and its uses |
| CN1382823A (en) * | 2001-03-14 | 2002-12-04 | 利优比株式会社 | Creep resistance Dow metal |
Also Published As
| Publication number | Publication date |
|---|---|
| CN1515696A (en) | 2004-07-28 |
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