WO2005111251A1 - Alliage de magnesium coule de haute durete et de haute resistance et procede - Google Patents

Alliage de magnesium coule de haute durete et de haute resistance et procede Download PDF

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Publication number
WO2005111251A1
WO2005111251A1 PCT/CN2005/000479 CN2005000479W WO2005111251A1 WO 2005111251 A1 WO2005111251 A1 WO 2005111251A1 CN 2005000479 W CN2005000479 W CN 2005000479W WO 2005111251 A1 WO2005111251 A1 WO 2005111251A1
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Prior art keywords
alloy
casting
strength
crucible
magnesium
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PCT/CN2005/000479
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Chinese (zh)
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WO2005111251A8 (fr
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Yuequn Ma
Rongshi Chen
Enhou Han
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Institute Of Metal Research Chinese Academy Of Sciences
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Priority to CNB2005800098757A priority Critical patent/CN100408709C/zh
Priority to US10/582,541 priority patent/US20090068053A1/en
Publication of WO2005111251A1 publication Critical patent/WO2005111251A1/fr
Publication of WO2005111251A8 publication Critical patent/WO2005111251A8/fr

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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
    • C22C23/02—Alloys based on magnesium with aluminium as the next major constituent
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D21/00—Casting non-ferrous metals or metallic compounds so far as their metallurgical properties are of importance for the casting procedure; Selection of compositions therefor
    • B22D21/002—Castings of light metals
    • B22D21/007—Castings of light metals with low melting point, e.g. Al 659 degrees C, Mg 650 degrees C
    • 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
    • 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
    • C22F1/06—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

Definitions

  • the invention relates to a casting gold and a preparation technology thereof.
  • the purpose of the present invention is to prepare a low-cost, high-strength, high-toughness cast magnesium alloy by means of alloying and heat treatment.
  • the invention is not only suitable for permanent mold casting of metal molds, but also suitable for sand casting, pressure casting, squeeze casting and other processes. Background technique
  • magnesium alloys As a light metal material, magnesium alloys have many advantages, such as high specific strength, excellent machining and casting properties, good damping characteristics, dimensional stability, and electromagnetic shielding capabilities. Due to the above characteristics, magnesium alloy components have been widely used in many industrial sectors, including automotive systems, 3C products (computers, communications, consumer electronics) manufacturing, and military industries. In recent years, due to the increasingly urgent demand for automobile weight reduction, the low density of magnesium alloys has once again made it extremely attractive in the transportation field. The demand for mirror alloys has experienced a period of rapid growth.
  • Table 1 shows the tensile mechanical properties of some typical commercial cast magnesium alloys. Tensile mechanical properties of a typical cast magnesium alloy
  • the currently used pressure cast AZ91 alloy has the highest strength, but the low plasticity of the phase X inch limits its application.
  • the AM60 alloys have high plasticity, their low strength also limits their large number of applications.
  • a small amount of magnesium-rare earth alloys have both high strength and high toughness, such as ZE63, the high cost and complicated heat treatment process make these alloys difficult to apply in large areas. As a result of raising The strength and plasticity of the alloy is the key to further expanding the scope of application of magnesium alloys. Therefore, it is an urgent task to develop a low-cost, high-strength and high-toughness magnesium alloy.
  • European patent 0879898A1 discloses a magnesium alloy with excellent high temperature properties and pressure casting properties, but the alloy disclosed by the invention has lower room temperature strength (tensile strength ⁇ 230 MPa) and plasticity (elongation ⁇ 5%).
  • U.S. Patent 20030084968A1 discloses a stubborn creep resistant magnesium alloy, but the alloy disclosed in the invention also has low room temperature plasticity (elongation ⁇ 5%).
  • 6,139,651 discloses a continuous alloy for high temperature applications, but the alloy disclosed in this invention is not ideal in terms of room temperature strength and ductility.
  • a few patents have obtained some promising high-strength and high-toughness magnesium alloys, such as US patent 20010055539A1, the development of more ideal room-temperature high-strength and high-toughness magnesium alloys needs further development.
  • 1241276 discloses a creep-resistant alloy which contains 1.5-4.0 wt% aluminum, 0.5-1.8 wt% silicon, 0.05-0.6 wt% rare earth, 0.005-1.5 wty. The balance of strontium or antimony, magnesium.
  • Chinese patent CN1341767 discloses a multi-component automotive heat-resistant magnesium alloy and its casting process. The alloy contains 5-7 wt% aluminum, 0.5-1.0 wt% zinc, 0.6-1.5 wt% silicon, and 0.4- 0.7 wt% antimony, 0.1-0.3 wt% rare earth, 0.002 wt% beryllium, and magnesium as the balance balance.
  • the main object of the present invention is to provide a cast magnesium alloy having both high strength and high toughness by rationally selecting alloying elements and adopting appropriate heat treatment means.
  • the second object of the present invention is that the rhenium prepared by this method is not only suitable for permanent mold casting, but also suitable for sand casting, pressure casting, squeeze casting and other processes.
  • the third object of the present invention is that the magnesium alloy prepared by this method has not only excellent room temperature mechanical properties, but also some alloys also have excellent high temperature mechanical properties.
  • a fourth object of the present invention is that, in addition to the above characteristics, the magnesium alloy prepared by this method has a relatively low production cost.
  • the medium aluminum content and the medium zinc content constitute a high-strength and high-toughness magnesium alloy base system; the addition of trace elements and a suitable heat treatment process further achieve the alloy's best mechanical properties.
  • the aluminum content in the alloy of the present invention is 3-9 wt%; the zinc content is 3.5-9 wt% ; the manganese content is 0.15-1.0 wt% ; the antimony content is 0.01-2 wt% ; and the magnesium content is balanced.
  • the balance; the alloy may further contain 0 ⁇ 2 wt% of one of the three elements of cerium-rich mixed rare earth, calcium, and silicon.
  • the strengthening and toughening mechanism of the present invention is as follows: 1), the solid solution strengthening mechanism of the element. 2) Strengthening mechanism of secondary break-out phase: As the zinc content increases, the Mg 17 Al 12 phase gradually decreases, and at the same time, the Mg-Al-Z ⁇ phase and the magnesium-zinc binary phase gradually increase; in addition, Mn, Sb, etc. After trace elements, new particle-enhancing phases or particles such as Al-Mn, M ⁇ Sba, etc. will be generated. 3) The addition of certain elements (such as antimony) will also refine the grains and the continuous brittle secondary precipitation phase distributed on the grain boundaries, thereby improving the strength, plasticity and casting properties of the alloy. 4), the heat treatment process will further improve the mechanical properties of the alloy by adjusting the number and shape of the secondary precipitation phases.
  • the aluminum element is not only very effective for improving the room temperature strength and hardness of gold, but also makes it easier to cast gold by widening the solidification interval of the alloy.
  • the aluminum content in the alloy should be at least 3wt% ; however, too high aluminum content will adversely affect the plasticity of the alloy. Therefore, the upper limit of the aluminum content of the alloy in the present invention is 9 t%.
  • magnesium alloys zinc is another important alloying element besides aluminum.
  • zinc and aluminum are used together to improve the room temperature strength and casting properties of the alloy.
  • it is well known that in the magnesium-aluminum-zinc alloy system if the matching of zinc and aluminum is not suitable, it will increase the tendency of the alloy to crack hot and deteriorate the casting moldability.
  • the present invention according to the relationship between the die-casting performance of the magnesium-aluminum-zinc ternary alloy system and the aluminum-zinc content (see FIG.
  • the zinc content in the alloy of the present invention should be at least 3.5 wt%.
  • the highest zinc content should not exceed 9 wt%.
  • the manganese element in the alloy of the present invention is added in the form of an aluminum-manganese intermediate alloy. Although the role of manganese in improving the tensile strength of the alloy is not obvious, it can also play a role in improving the yield strength by the aluminum-manganese particle phase present in the primary crystal grains.
  • the main role of manganese in the present invention is to improve the corrosion resistance of the alloy.
  • Manganese can form compounds with impurity elements (such as iron, nickel, etc.) in the alloy during the smelting process of the manganese, which is precipitated on the bottom of the crucible to remove impurities and eliminate the harmful effects of these elements on the corrosion resistance of the alloy.
  • the amount of manganese added is limited by its low solid solubility, and the amount of manganese added in the present invention is 0.15-1 wt%.
  • the antimony element in the present invention is either added in a powder form wrapped in aluminum foil paper, or is added in a block form.
  • a small amount of antimony will refine the primary crystal grains and the secondary precipitated phase, thereby improving the mechanical properties of the alloy and reducing the tendency of hot cracking.
  • the antimony content exceeds 3 ⁇ 4 2 wt%, the coarsened Mg3Sb 2 particles will instead reduce the mechanical properties. Therefore, the content of antimony in the present invention should be controlled between 0.01% and 2% by weight.
  • the alloy in the present invention may further contain 0 to 2% by weight of a certain element of one of cerium-rich mixed rare earth, calcium, and silicon.
  • the cerium-rich mixed rare earth in the present invention is a commercially available product, and its manufacturer is Baotou Huamei Rare Earth High-tech Co., Ltd. About 50% of the cerium-rich rare earths are cerium, and the other main components are lanthanum and neodymium.
  • the addition of a small amount of rare earth can improve the hardness and high temperature mechanical properties of magnesium alloys, but excessive rare earths will increase the cost on the one hand, and on the other hand will cause coarse particles to precipitate out and cause the decline in mechanical properties and casting properties.
  • the content of rare earth should be controlled between 0 and 2 wt%, and more ideally, it should be limited between 0 and 1 wt%.
  • the addition of calcium will not only play a role in flame retardance, but also improve the high temperature mechanical properties and creep resistance of the alloy. However, the addition of calcium will reduce the casting properties and exacerbate the hot cracking tendency of the alloy.
  • silicon element will also improve the high temperature mechanical properties and creep resistance of the alloy, but too much silicon element will produce coarse Ms particles and cause the decrease of mechanical properties.
  • the smelting and casting process of the alloy in the present invention can be divided into the following steps:
  • the heat treatment of the present invention greatly affects the mechanical properties of the alloy.
  • the alloy heat treatment methods of the present invention can be divided into three types: T4 (solution treatment), T5 (aging treatment), and T6 (addition treatment after solution treatment). ,.
  • T4 solution treatment is best carried out in a protective atmosphere (such as argon, 99 ⁇ 99.5% air (or C0 2 ) + 0.5-1% SF 6 mixed gas, etc.), and its temperature range is 3400 0 (TC and zinc content Closely related.
  • a protective atmosphere such as argon, 99 ⁇ 99.5% air (or C0 2 ) + 0.5-1% SF 6 mixed gas, etc.
  • the solid solution temperature of magnesium alloy should be 10 ⁇ 20 ° C lower than the solidus temperature of the alloy.
  • the solidus temperature of magnesium-aluminum-zinc ternary alloy system can refer to Figure 2.
  • the addition of certain elements (such as antimony) will have a slight impact on the solidus temperature, so a more accurate solidus temperature can be determined by the differential thermal analysis data of the alloy.
  • the T4 solution treatment time it can be taken from 8 to 24 hour.
  • T5 aging treatment The temperature of T5 aging treatment is 70 ⁇ 200 ° C, and the aging treatment time is 8 ⁇ 24 hours.
  • T6 heat treatment it can be understood as a combination of T4 and T5 heat treatment. Specifically, T4 heat treatment is performed first, and then T5 heat treatment is performed.
  • the heat treatment changes the distribution and quantity of particle-reinforced phases, it significantly affects the mechanical properties.
  • the T4 solution-treated sample will improve the plasticity and impact resistance because the mesophase is re-dissolved into the matrix, but the yield strength will be reduced.
  • T5 aging treatment can eliminate residual stress and improve mechanical properties to a certain extent.
  • the T6 treatment can redistribute the number and shape of the secondary precipitation phases, so it can significantly increase the strength and hardness of the alloy, but the plasticity of the alloy will decrease.
  • the room temperature mechanical properties can reach: tensile strength cj b 270MPa, yield strength. ⁇ ⁇ . ⁇ , extension 5 6%, Brinell hardness 70, impact energy ot k 12J.
  • the magnesium alloy prepared by the present invention has both high strength and high toughness characteristics, and is particularly suitable for light, sturdy, and high toughness materials, such as automobile wheels.
  • the magnesium alloy prepared by the present invention has not only excellent room temperature mechanical properties, but also some alloys have good high temperature mechanical properties. 3)
  • the invention is cost-effective. The raw materials used are readily available, low cost, and suitable for large-scale production.
  • the smelting and casting process of the invention is simple and stable.
  • the alloying element used in the present invention does not cause significant side reactions with the iron crucible wall or the covering agent, and the process is stable.
  • the invention has a wide range of applicable processes.
  • the invention is not only applicable to metal mold casting, but is also applicable to processes such as sand casting, pressure casting, squeeze casting and the like.
  • Fig. 12 Schematic diagram of the pressure casting performance of Vlg-Al-Zn ⁇ element alloy and the location of the alloy in the embodiment
  • Fig. 2 is a phase diagram (solid phase surface) of the Mg-Al-ZnH element alloy and a schematic diagram of the location of the alloy of the example.
  • Fig. 3 is a DTA curve of the alloy of Example 1 of the present invention.
  • Fig. 4 shows the as-cast structure of the alloy of Example 1 of the present invention.
  • FIG. 5 is a schematic diagram of the distribution of Mg3Sb 2 in the alloy of Example 1 after T4 heat treatment.
  • the arrow marks in the figure indicate the distribution of Mg3Sb 2 particles in the alloy of Example 1.
  • Fig. 6 is the structure of the alloy of Example 1 after T4 heat treatment.
  • Fig. 7 shows the structure of the alloy of Example 1 after T6 heat treatment.
  • Fig. 8 is a comparison of room temperature mechanical properties of three alloys (AM60, AZ9 Example 1) in the as-cast state.
  • Fig. 9 is a comparison of room temperature mechanical properties of three alloys (AM60, AZ91, Example 1) T6 in a heat-treated state.
  • Fig. 10 is a comparison of room temperature mechanical properties of the four alloys (Example 1, Example 2, Example 3, AZ91) T6 in the heat-treated state.
  • FIG. 11 is a comparison of the high-temperature mechanical properties of the four alloys (Example 1, Example 2, Example 3, AZ91) T6 in the heat-treated state at 150 ° C.
  • Fig. 12 is a comparison of the high temperature mechanical properties of three alloys (Example 4, Example 5, AZ91) T6 at 150 ° C in the heat-treated state. detailed description
  • alloy composition The three magnesium alloys are made from commercial high-purity raw materials in a low-carbon steel crucible. Of the three alloys, commercial grades
  • AZ91 and AM60 are both comparative examples.
  • the chemical composition of the three magnesium alloys was analyzed by inductively coupled plasma-atomic emission spectroscopy (ICP-AES). See 3 ⁇ 42 for the chemical composition of the three ⁇ gold.
  • the smelting of the alloy was performed in a 15 kg crucible and resistance furnace.
  • the crucible and casting mold are made of mild steel.
  • the following uses Example 1 as an example to elaborate the smelting and casting process of the alloy.
  • the smelting and casting process of AZ91 and AM60 alloys is similar to that of AZY641, except that the amount of various alloying elements is different.
  • T4 heat treatment temperature can be deduced from the differential thermal analysis (DTA) data of the alloy.
  • DTA differential thermal analysis
  • the T4 heat treatment of the alloy of Example 1 cannot exceed il370 ° C.
  • the T4 heat treatment temperature of the alloy of Example 1 was 370 ° C, and the time was 12 hours.
  • the T4 heat treatment temperature of AZ91 and AM60 alloys is 410 ° C, and the heat treatment time is controlled between 16 and 24 hours. T4 heat treated samples were air-cooled to room temperature.
  • T5 heat treatment three alloys can be treated with the same T5 heat treatment.
  • the temperature of the T5 heat treatment is controlled at 180 ° C, and the temperature of the T5 heat treatment is 16 hours. All the heat-treated samples are air-cooled to room temperature.
  • T6 heat treatment can be regarded as a combination of T4 and T5 heat treatment. Each alloy can be heat-treated with the appropriate T4 and T5, respectively, as described.
  • the sample for tissue observation is prepared as follows: The surface is smoothed with 1000-size silicon carbide water-abrasive paper; then the oil-based diamond abrasive paste machine is used to leak light; the polished sample surface is etched with a 2% strength nitric acid alcohol solution. Facial tissue observation was performed on an electronic scanning microscope Philips XL30 ESEM-FEG / EDAX equipped with an energy spectroscopy device.
  • the as-cast microstructure of the alloy of Example 1 has a certain degree of refinement of the primary crystal grains and the secondary precipitation phase (refer to FIG. 4).
  • the mechanism of this process can be understood as follows: a small amount of antimony will form MS particles with a melting point of 1228 ° C with magnesium; these ⁇ 813 ⁇ 4 particles will be preferentially formed during the melt cooling process, and some of these particles will become the primary phase
  • the heterogeneous nucleation center plays a role in refining the primary phase; other Mg3Sb 2 particles will appear at the growing liquid front and interact with the precipitation of the secondary phase, resulting in a more dispersed secondary precipitation phase distribution.
  • Mg3Sb 2 particles appeared not only inside the primary crystal grains, but also on the grain boundaries (refer to Figure 5).
  • FIGs 6 and 7 show the microstructure evolution of the alloy of Example 1 caused by different heat treatment methods. It can be seen from Figure 6 that T4 heat treatment caused most of the secondary precipitated phases to be re-dissolved into the primary phase, and the remaining particles in the figure are all particles with high melting points (such as MfeSbz and Al-Mn ⁇ particles). The T6 heat treatment caused the solute elements to be re-precipitated from the primary grains and distributed in a more diffuse form at the grain boundaries and inside the grains (see Figure 7).
  • Samples of room temperature mechanical tensile properties of alloys are prepared with reference to Chinese national standard GB 6397-86.
  • the parallel distance of the sample is 30 X 6 X 3 (mm).
  • the surface of the sample was polished with 1000 grit silicon carbide sandpaper.
  • the strain rate for the tensile test is 1.11 X 1 ⁇ .
  • the high-temperature (150 ° C) mechanical tensile properties of the alloy have a parallel distance of 27X 5 X3 (mm).
  • the surface of the sample was polished with 1000-size silicon carbide sandpaper.
  • the strain rate of the tensile test was 5.55 ⁇ 10 4 S 4 .
  • For the preparation and experimental method of the Brinell hardness sample of the alloy refer to GB231-84.
  • the parallel distance of the sample is 10x10x55
  • the sample is an unnotched sample.
  • Figure 8 shows the comparison of room temperature mechanical properties of as-cast alloys (AZ91-F, AM60-F, Example 1-F).
  • Figure 9 shows the comparison of room temperature mechanical properties of T6 heat treated alloys (AZ91-T6, AM60-T6. Example 1-T6).
  • Example 1 Mechanical properties of alloy at room temperature Yield strength Tensile strength Elongation Impact energy Heat treated state Brinell hardness
  • Example 1 for smelting and casting.
  • the differences are: The zinc content of the two is different.
  • heat treatment of alloy Refer to Example 1 for heat treatment. The differences are: According to the DTA data of the alloy of Example 2, the temperature of the solution heat treatment is 360 ° C, and the time is 12 hours; the temperature of the aging treatment is 180 ° C, and the time is 16 hours.
  • Reference Example 1 is a mechanical property test. Table 5. Mechanical properties of the alloy of Example 2 at room temperature Yield strength Tensile strength Elongation Impact energy Heat treated state Brinell hardness
  • T6 heat treatment 145 250 6 .74 12 The comparison of high temperature mechanical properties between Example 2 and AZ91 alloy is shown in Figure 11. It can be seen that in Example 2, not only the comprehensive mechanical properties at room temperature are better than AZ91, but also the mechanical properties at high temperature are also better than AZ91.
  • Example 3 The chemical composition of the alloy of Example 3 is shown in Table 6. Table 6. Chemical composition of alloy in Example 3 (wt% wt.%) Alloy Aluminum Zinc Manganese Magnesium Example 3 5.89 6.74 0.35 0.53 Equilibrium balance
  • Example 1 for smelting and casting.
  • the differences are: The zinc content of the two is different.
  • Example 1 for heat treatment.
  • the temperature of the solution heat treatment is 350 ° C, and the time is 12 hours; the temperature of the aging treatment is 180 ° C, and the time is 16 hours.
  • T6 heat treatment 153 260 5 77 9 The comparison of high temperature mechanical properties between Example 3 and AZ91 alloy is shown in Figure 11. It can be seen that not only the comprehensive mechanical properties at room temperature are higher than AZ91, but also the strength properties of high temperature mechanical properties are better than AZ91.
  • Example 1 for smelting and casting.
  • the differences are as follows: The alloy of Example 4 is added with a small amount of cerium-rich mixed rare earth on the basis of the alloy of Example 1.
  • the melting point of mixed rare earth is high, it is necessary to add cerium-rich mixed rare earth when adding ingredients, and it is best to add mixed rare earth when the melt temperature in the crucible is 750 ⁇ 800 ° C.
  • Example 1 for heat treatment.
  • the differences are as follows: According to the DTA data of the alloy of Example 4, the heat treatment solution temperature of the alloy is 370 ° C and the time is 12 hours; the temperature of the aging treatment is 180 ° C and the time is 16 hours.
  • Example 4 Mechanical properties of alloy at room temperature Yield strength Tensile strength Elongation Impact energy Heat treated state Brinell hardness
  • T6 heat treatment 146 272 8.7 77 13 The comparison of the high temperature mechanical properties of Example 4 and AZ91 alloy is shown in FIG. 12. It can be seen that although the comprehensive mechanical properties at room temperature of Example 1 are better than AZ91, the high-temperature mechanical properties are slightly better than AZ91.
  • Example 1 for smelting and casting.
  • the differences are as follows: Reference to the smelting and casting of Example 1. The difference is that in addition to the differences in aluminum and zinc content, a small amount of cerium-rich mixed rare earth was added to the alloy of Example 5.
  • the melting point of mixed rare earth is high, it is necessary to add cerium-rich mixed rare earth when adding ingredients, and it is best to add mixed rare earth when the melt temperature in the crucible is 750 ⁇ 800 ° C.
  • Example 1 for heat treatment.
  • the heat treatment solution temperature of the alloy is 350 ° C and the time is 12 hours;
  • the temperature of the aging treatment is 180 ° C and the time is 16 hours.
  • Reference Example 1 is a mechanical property test. Table 11 Mechanical properties at room temperature of the alloy of Example 5 Yield strength Tensile strength Elongation Impact energy Heat treated state Brinell hardness
  • T6 heat treatment 156 282 7.0 79 12 The comparison of high temperature mechanical properties between Example 5 and AZ91 alloy is shown in Figure 12. It can be seen that in Example 5, not only the comprehensive mechanical properties of room temperature are better than AZ91, but also the strength properties of high temperature mechanical properties are better than AZ91.

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Abstract

La présente invention concerne un alliage de magnésium coulé de haute dureté et de haute résistance et un procédé de coulé de cet alliage, dans lequel cet alliage est constitué sensiblement de 3 à 9 % en masse d'aluminium, de 3,5 à 9 % en masse de zinc, de 0,15 à 1 % en masse de manganèse, de 0,0 1 à 2 % en masse d'antimoine et du solde en magnésium. Cet alliage peut aussi comprendre un élément sélectionné dans le groupe constitué des métaux mixtes enrichis au cérium, du calcium ou du silicium pour o à 2 % en masse. Dans cette invention après le traitement thermique T6 (solution plus vieillissement), les propriétés mécaniques de l'alliage typique de cette invention peuvent atteindre les propriétés suivantes: résistance en tension Σb > ou égale à 270Mpa, résistance de rendement Σ0,2 supérieure ou égale à 140 Mpa, élongation Δ5 supérieure ou égale à 6 %, dureté de Brinel supérieure ou égale à 70, travail balistique Ak supérieur ou égal à 12J. Certains alliages de l'invention non seulement possèdent d'excellentes propriétés mécaniques à température ambiante mais possèdent également de bonnes propriétés mécaniques à température élevée. Les coûts de production de cette invention sont relativement faibles et une production à grande échelle est souhaitable. L'alliage de cette invention peut être appliqué dans un processus de coulée, tels qu'une coulée en moule permanent, coulée en moule de sable, coulée sous presse, coulée en extrusion et dans d'autres processus similaires.
PCT/CN2005/000479 2004-05-19 2005-04-11 Alliage de magnesium coule de haute durete et de haute resistance et procede WO2005111251A1 (fr)

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US10/582,541 US20090068053A1 (en) 2004-05-19 2005-04-11 High strength and high ductility magnesium alloy and its preparation method

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CNB2004100205671A CN100338250C (zh) 2004-05-19 2004-05-19 一种高强度高韧性铸造镁合金的制备方法

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AT503854B1 (de) * 2006-05-19 2008-01-15 Arc Leichtmetallkompetenzzentrum Ranshofen Gmbh Magnesium-basislegierung
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CN102632822A (zh) * 2012-03-31 2012-08-15 北京华盛荣镁业科技有限公司 客车座椅框架及其制造方法与客车座椅
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DE102015109775B3 (de) 2015-06-18 2016-09-22 RobArt GmbH Optischer Triangulationssensor zur Entfernungsmessung
CN105039816B (zh) * 2015-07-20 2017-05-31 河南科技大学 一种低成本高强耐热镁合金及其制备方法
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CN114540681B (zh) * 2021-12-29 2022-10-25 北京理工大学 一种高强高模耐腐蚀的双相镁锂合金结构件及制备方法
CN114836663B (zh) * 2022-05-31 2023-04-11 重庆大学 一种高强度铸造镁合金及其制备方法

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN1210897A (zh) * 1997-05-21 1999-03-17 爱信高冈株式会社 具有优越高温性能和模铸性的镁合金
US6471797B1 (en) * 2001-04-11 2002-10-29 Yonsei University Quasicrystalline phase-reinforced Mg-based metallic alloy with high warm and hot formability and method of making the same
CN1401804A (zh) * 2001-08-22 2003-03-12 东南大学 低成本耐热镁合金
CN1412332A (zh) * 2002-10-17 2003-04-23 山西至诚科技有限公司 一种镁合金的制备方法
JP2004263280A (ja) * 2003-03-04 2004-09-24 Toyota Central Res & Dev Lab Inc 防蝕マグネシウム合金部材、マグネシウム合金部材の防蝕処理方法およびマグネシウム合金部材の防蝕方法

Family Cites Families (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US2314852A (en) * 1940-09-09 1943-03-23 Anglo California Nat Bank Of S Heat treatment of magnesium base alloys
US3119725A (en) * 1961-11-27 1964-01-28 Dow Chemical Co Die-expressed article of magnesium-base alloy and method of making
US4675157A (en) * 1984-06-07 1987-06-23 Allied Corporation High strength rapidly solidified magnesium base metal alloys
CN1127306A (zh) * 1994-07-12 1996-07-24 宇部兴产株式会社 抗蠕变耐腐蚀镁合金
JP3898302B2 (ja) * 1997-10-03 2007-03-28 日本パーカライジング株式会社 金属材料用表面処理剤組成物および処理方法
IL125681A (en) * 1998-08-06 2001-06-14 Dead Sea Magnesium Ltd Magnesium alloy for high temperature applications
JP3603706B2 (ja) * 1999-12-03 2004-12-22 株式会社日立製作所 高強度Ｍｇ基合金とＭｇ基鋳造合金及び物品
CN1168840C (zh) * 2001-08-14 2004-09-29 上海交通大学 汽车用多元耐热镁合金及其熔铸工艺
CN1488773A (zh) * 2003-09-05 2004-04-14 郑州大学 一种含稀土高锌镁合金及其制备方法

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN1210897A (zh) * 1997-05-21 1999-03-17 爱信高冈株式会社 具有优越高温性能和模铸性的镁合金
US6471797B1 (en) * 2001-04-11 2002-10-29 Yonsei University Quasicrystalline phase-reinforced Mg-based metallic alloy with high warm and hot formability and method of making the same
CN1401804A (zh) * 2001-08-22 2003-03-12 东南大学 低成本耐热镁合金
CN1412332A (zh) * 2002-10-17 2003-04-23 山西至诚科技有限公司 一种镁合金的制备方法
JP2004263280A (ja) * 2003-03-04 2004-09-24 Toyota Central Res & Dev Lab Inc 防蝕マグネシウム合金部材、マグネシウム合金部材の防蝕処理方法およびマグネシウム合金部材の防蝕方法

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
LIU Z. ET AL: "Survey of the Mg-Al Based Elevated temperature Magnesium Casting Alloys", MATERIALS FOR MECHANICAL ENGINEERING, vol. 25, no. 11, November 2001 (2001-11-01) *

Cited By (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103305735A (zh) * 2013-06-24 2013-09-18 山东富通电气有限公司 一种增强型镁合金及其制造方法
CN109182857A (zh) * 2018-11-08 2019-01-11 中信戴卡股份有限公司 一种高强韧变形镁合金及制备方法
CN109182857B (zh) * 2018-11-08 2024-01-30 中信戴卡股份有限公司 一种高强韧变形镁合金及制备方法
CN110373559A (zh) * 2019-08-26 2019-10-25 上海交通大学 一种适合镁及镁合金熔炼与铸造的方法
CN115029594A (zh) * 2022-06-20 2022-09-09 重庆大学 一种变形镁合金及其制备方法
CN115976384A (zh) * 2022-12-30 2023-04-18 重庆大学 具有优异高温力学性能的AlN/AE44复合材料及其制备方法
CN115976384B (zh) * 2022-12-30 2024-02-23 重庆大学 具有优异高温力学性能的AlN/AE44复合材料及其制备方法

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