EP3763845B1 - Magnesiumlegierung und verfahren zur herstellung derselben - Google Patents

Magnesiumlegierung und verfahren zur herstellung derselben Download PDF

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Publication number
EP3763845B1
EP3763845B1 EP19184999.1A EP19184999A EP3763845B1 EP 3763845 B1 EP3763845 B1 EP 3763845B1 EP 19184999 A EP19184999 A EP 19184999A EP 3763845 B1 EP3763845 B1 EP 3763845B1
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EP
European Patent Office
Prior art keywords
magnesium alloy
magnesium
weight
heat treatment
strength
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EP19184999.1A
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German (de)
English (en)
French (fr)
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EP3763845A1 (de
Inventor
Stefan Gneiger
Clemens Simson
Simon Frank
Alexander GROßALBER
Andreas Betz
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LKR Leichtmetallkompetenzzentrum Ranshofen GmbH
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LKR Leichtmetallkompetenzzentrum Ranshofen GmbH
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Priority to EP19184999.1A priority Critical patent/EP3763845B1/de
Priority to CN202080046287.5A priority patent/CN114026260B/zh
Priority to CA3137604A priority patent/CA3137604A1/en
Priority to PCT/EP2020/058280 priority patent/WO2021004662A1/de
Priority to JP2021567860A priority patent/JP2022540542A/ja
Priority to KR1020227000723A priority patent/KR20220030244A/ko
Priority to US17/625,359 priority patent/US20220259705A1/en
Priority to EP20735621.3A priority patent/EP3997251A1/de
Priority to PCT/EP2020/069131 priority patent/WO2021005062A1/de
Priority to CA3138658A priority patent/CA3138658A1/en
Priority to JP2021568980A priority patent/JP2022540544A/ja
Priority to CN202080049996.9A priority patent/CN114096690A/zh
Priority to KR1020227000718A priority patent/KR20220030243A/ko
Priority to US17/625,360 priority patent/US20220267881A1/en
Publication of EP3763845A1 publication Critical patent/EP3763845A1/de
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C23/00—Alloys based on magnesium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C14/00—Alloys based on titanium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/02—Alloys based on aluminium with silicon as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
    • C22C21/08—Alloys based on aluminium with magnesium as the next major constituent with silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/10—Alloys based on aluminium with zinc as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/12—Alloys based on aluminium with copper as the next major constituent
    • C22C21/16—Alloys based on aluminium with copper as the next major constituent with magnesium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C23/00—Alloys based on magnesium
    • C22C23/02—Alloys based on magnesium with aluminium as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C24/00—Alloys based on an alkali or an alkaline earth metal
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C9/00—Alloys based on copper
    • C22C9/04—Alloys based on copper with zinc 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
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • 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
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/043—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with silicon 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
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/047—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with magnesium 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
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/05—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys of the Al-Si-Mg type, i.e. containing silicon and magnesium in approximately equal proportions
    • 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
    • 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
    • C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
    • 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
    • C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
    • C22F1/18—High-melting or refractory metals or alloys based thereon
    • C22F1/183—High-melting or refractory metals or alloys based thereon of titanium or alloys based thereon

Definitions

  • the invention relates to a magnesium alloy.
  • the invention also relates to a method for producing a magnesium alloy.
  • magnesium alloys Due to their low density and good mechanical properties, magnesium alloys are frequently used construction alloys or
  • the object of the invention is to specify a magnesium alloy which has high strength, in particular high compressive strength, and good formability.
  • Another aim of the invention is to provide a method for producing such a magnesium alloy.
  • a magnesium alloy having, in particular consisting of, (in atomic%) 40.0% to 70.0% lithium, more than 0.0% aluminum, optionally also more than 0.0 to 3, 0% by weight calcium, optionally also more than 0.0 to 3.0% by weight rare earth metals, in particular yttrium, optionally also 3.0% by weight to 10.0% by weight zinc, optionally also 2.0% by weight to 10.0% by weight silicon,
  • Remainder magnesium and production-related impurities wherein a ratio of aluminum to magnesium (in at .-%) is 1: 6 to 4: 6.
  • the invention is based on the knowledge that with an aforementioned alloy composition of a magnesium alloy with a corresponding proportion of lithium (Li) and a mandatory proportion of aluminum (Al) in a certain, aforementioned ratio range of aluminum to magnesium, a microscale microstructure or fine, in particular fine lamellar, microstructure forms in the magnesium alloy.
  • a microscale microstructure or fine, in particular fine lamellar, microstructure forms in the magnesium alloy.
  • a eutectic transformation of the magnesium alloy which occurs with the aforementioned ratio of aluminum to magnesium, is regarded as the theoretical foundation for this behavior.
  • the fine-scale microstructure is associated with high strength, in particular high compressive strength, with good formability of the magnesium alloy at the same time given the corresponding aforementioned proportions of lithium in the magnesium alloy.
  • Orientation composition or orientation line in the phase diagram is in particular a ratio of aluminum to magnesium (in atomic percent, abbreviated as atomic%) of approx Find morphology.
  • atomic% in atomic percent, abbreviated as atomic%
  • the fine, in particular fine lamellar, microstructure or morphology continues to be found with varying degrees which is usually associated with different characteristics of a level of strength, in particular a level of compressive strength, as well as deformability or ductility of the magnesium alloy. Due to this special morphological behavior in the specified composition range, a magnesium alloy can thus be formed which has both high strength, in particular compressive strength, and good formability.
  • the magnesium alloy (in at.%) Has 30.0% to 60.0%, in particular 40% to 50%, lithium.
  • pronounced strength and particularly pronounced formability can be achieved. This is likely to result in particular from a combination of finely structured morphology and a conversion to a body-centered cubic crystal system in the stated lithium range. Both high strength and a high level of formability is evident when the magnesium alloy (in atomic%) has 45% to 50%, in particular 45% to 48%, lithium.
  • magnesium-based alloy denotes a magnesium alloy which, based on its alloy proportions in percent by weight (% by weight), contains magnesium as the main element or as the largest alloy proportion.
  • a practicable construction alloy with very high strength properties and pronounced formability can be achieved, especially in combination with the proportions for lithium listed above.
  • the magnesium alloy (in at.%) Is 40.0% to 60.0% lithium and a ratio of aluminum to magnesium (in at.%) Of 2.5: 6 to 3.5 : 6, in particular about 3: 6.
  • the magnesium alloy contains more than 0.0 to 3.0% by weight, in particular more than 0.0 to 2.0% by weight, preferably more than 0.0 to 1.5% by weight.
  • % Calcium (Ca).
  • the corrosion resistance is improved Magnesium alloy achievable.
  • a reduced tendency of the magnesium alloy to oxidize can thus be implemented, usually advantageously in that a stable oxidation layer is formed on a surface of the magnesium alloy.
  • a grain refining effect in the magnesium alloy can be used or achieved through an aforementioned proportion of calcium, so that a high level of stability of the fine-scale structure can be achieved and the strength of the magnesium alloy can be further increased.
  • the magnesium alloy has 0.5% by weight to 1.0% by weight calcium.
  • the above-mentioned effects in the presence of calcium in the magnesium alloy are based in particular on the formation of CaO. Accordingly, it can be specifically provided that calcium, at least partially, in particular predominantly, preferably completely, in the form of CaO, is added to the magnesium alloy as an alloy component or is contained in the magnesium alloy. This can promote a homogeneous distribution of calcium or CaO in the magnesium alloy. It is therefore particularly advantageous if the magnesium alloy contains CaO in the proportions specified above for calcium.
  • the magnesium alloy contains more than 0.0 to 3.0% by weight, preferably 1.0% by weight to 2.0% by weight, of rare earth metals, in particular yttrium (Y) , having.
  • Y yttrium
  • the formation of Y 2 O 3 in the magnesium alloy is particularly relevant here. Accordingly, it can specifically be provided that yttrium, at least partially, in particular predominantly, preferably entirely, in the form of Y 2 O 3, is added to the magnesium alloy as an alloy component or is contained in the magnesium alloy. It is therefore advantageous if the magnesium alloy contains Y 2 O 3 with the aforementioned proportions for yttrium.
  • the magnesium alloy contains both calcium, in particular in the form of CaO, and rare earth metals, in particular yttrium, preferably in the form of Y 2 O 3 , in each case according to the aforementioned content ranges, with calcium in particular more than 0.0 to 1.5 wt .-% and yttrium with 1.0 wt .-% to 2.0 wt .-% has proven.
  • the magnesium alloy contains calcium and rare earth metals, in particular yttrium, with a total proportion of calcium and rare earth metals, in particular yttrium, being more than 0.0 to 3.0% by weight, preferably 1.0% by weight. -% to 2.5% by weight.
  • the compressive strength of the magnesium alloy is at least 300 MPa, in particular at least 350 MPa, preferably at least 380 MPa, particularly preferably at least 400 MPa.
  • This can be achieved with an alloy composition provided according to the invention for the magnesium alloy due to its finely structured microstructure, in particular after the magnesium alloy has been produced by casting.
  • the aforementioned values preferably apply for a maximum compressive strength, in particular for a compression limit or crush limit, of the magnesium alloy.
  • the compressive strength or maximum compressive strength or compression limit or crush limit of the magnesium alloy can advantageously be at least 410 MPa, in particular at least 430 MPa. This can usually be achieved practically with a heat treatment, as is set out in particular below.
  • the magnesium alloy has a good aging capacity, wherein a strength, in particular compressive strength, and / or deformability of the magnesium alloy can be further optimized or preferably increased by heat treatment of the magnesium alloy. It is therefore advantageously provided that a specific compressive strength, in particular a maximum specific compressive strength, of the magnesium alloy, in particular at room temperature, in an exposed state is at least 300 Nm / g, in particular at least 330 Nm / g, preferably at least 350 Nm / g.
  • the outsourced state denotes a state of the magnesium alloy after a heat treatment of the magnesium alloy has been carried out. Boundary conditions of the heat treatment that are favorable for this purpose are further explained in particular below in the context of a method for producing a magnesium alloy and can be used accordingly.
  • the specified material parameters for the magnesium alloy primarily values for compressive strength or specific compressive strength, relate in particular to a room temperature, which is usually between 20 ° C and 25 ° C, usually around 20 ° C.
  • the mechanical properties of the magnesium alloy can be optimized for a specific application by adding further alloy elements.
  • a strength, in particular the compressive strength, of the magnesium alloy it is favorable if the magnesium alloy is 3.0% by weight to 10.0 Has wt .-% zinc.
  • An optimization of the compressive strength, in particular without particularly restricting formability, can be achieved if the magnesium alloy has 7.0% by weight to 10.0% by weight zinc.
  • zinc it is favorable for this if the magnesium alloy contains 2.0% by weight to 10.0% by weight, preferably 3.0% by weight to 7.0% by weight, of silicon.
  • a method for producing a magnesium alloy according to the invention is generally based on the fact that starting materials of the magnesium alloy are mixed and cooled starting from a liquid or partially liquid phase.
  • the magnesium alloy according to the invention or a pre-material, semi-finished product or component with or from the magnesium alloy can be produced in a simple manner by means of conventional casting processes, for example with die casting processes, die casting processes, continuous casting processes or permanent mold casting processes. It has proven to be particularly advantageous if the production of the magnesium alloy according to the invention includes a heat treatment in order to optimize a microstructure or morphology of the magnesium alloy with regard to strength, in particular compressive strength, or formability.
  • the further object of the invention is achieved by a method for producing a magnesium alloy according to the invention, wherein a heat treatment of the magnesium alloy is carried out in order to optimize or increase a strength, in particular compressive strength, and / or formability of the magnesium alloy. It has been shown that a heat treatment of the magnesium alloy can further optimize or increase a strength, in particular compressive strength, or deformability of the magnesium alloy, so that it can be set in a targeted manner, preferably tailored to an intended use of the magnesium alloy.
  • the heat treatment is carried out at a temperature greater than 200 ° C., in particular between 200 ° C. and 450 ° C., for more than 20 minutes, in particular more than 1 hour.
  • a heat treatment at a temperature between 250.degree. C. and 400.degree. C., preferably between 270.degree. C. and 350.degree. C. has proven to be particularly suitable for a pronounced increase in strength, in particular compressive strength.
  • the heat treatment is carried out for more than 1 hour (hour), preferably between 1 hour and 10 hours, particularly preferably between 1 hour and 6 hours, in order to adjust the strength efficiently.
  • a heat treatment between 300 ° C.
  • a starting material, semi-finished product or component is advantageously implemented with, in particular made of, a magnesium alloy according to the invention or obtainable by a method according to the invention for producing a magnesium alloy according to the invention.
  • a starting material, semi-finished product or component formed with a magnesium alloy also has an advantageously high strength, in particular compressive strength, and good formability.
  • Fig. 1 shows a schematic phase diagram representation (in at .-%) for magnesium-lithium-aluminum (Mg-Li-Al) according to a conventional ternary phase diagram configuration, with composition ranges or content ranges of alloy proportions of a magnesium alloy according to the invention being indicated.
  • the dash-dotted line A shows an orientation composition of a Mg-Li-Al alloy with a ratio of aluminum to magnesium (in at.%) Of approx in a content range of 40.0 at.% to 70.0 at.% lithium at this ratio of aluminum to magnesium, a particularly homogeneous, fine-scale, in particular fine lamellar, microstructure or morphology is found.
  • a pronounced strength and particularly pronounced formability can be found in particular in a composition range (in at .-%) of 30.0% to 60.0% lithium and one Ratio of aluminum to magnesium (in at .-%) from 1: 6 to 4: 6.
  • This composition range is in Fig. 1 with a square shown with a dashed line, marked with reference numeral 2.
  • test series were carried out with different alloy compositions of magnesium alloys. In the following, characteristic data of Mg-20% Li-15% Al-1% Ca-0.5% Y (in% by weight) and Mg-20% Li-24% Al-1% are representative of the aforementioned composition ranges. Ca-0.5% Y (in% by weight) manufactured magnesium alloy samples are shown.
  • the magnesium alloy samples were produced by permanent mold casting, in particular magnesium alloy samples having a cylindrical shape, a diameter of 5 mm and a length of 10 mm were produced.
  • the magnesium alloy samples were subjected to compression tests at room temperature, approximately 20 ° C., and flow curves were determined as the result, which represent a yield stress, in MPa, as a function of a degree of deformation, in%.
  • Fig. 2 shows a flow stress diagram with flow curves as the result of compression tests with magnesium alloy samples made from Mg-20% Li-15% Al-1% Ca-0.5% Y (in% by weight) at room temperature. Shown are flow curves of magnesium alloy samples immediately after production of the magnesium alloy samples (as-cast), in Fig. 2 shown as solid lines, identified by reference numeral 3. In addition, flow curves of magnesium alloy samples after a heat treatment (aging) carried out of the magnesium alloy samples are shown, in Fig. 2 shown as dashed lines, identified by reference number 4. For this purpose, magnesium alloy samples were subjected to a heat treatment at 330 ° C. for 3 hours and then flow curves were determined by means of pressure tests. A clear influence of the heat treatment on the compressive strength and formability of the magnesium alloy samples can be seen, which gives the potential to optimize compressive strength and formability, especially for a later application, by means of heat treatment.
  • FIGS. 3 and 4 show scanning electron microscope images of the magnesium alloy samples made from Mg-20% Li-15% Al-1% Ca-0.5% Y (in% by weight) with different magnifications.
  • light grain boundary phases in whitish-gray
  • fine crystal structures or morphologies in an area enclosed by the grain boundary phases, in particular in a central section of this area, or in the interior of the mixed crystal, can be seen can be seen in particular in Fig. 4 .
  • a very different fine structure can also be seen, especially in the vicinity of the grain boundary phases.
  • Fig. 5 shows a flow stress diagram with flow curves as the result of compression tests with magnesium alloy samples made from Mg-20% Li-15% Al-1% Ca-0.5% Y (in% by weight) at room temperature, with magnesium alloy samples after heat treatments have been carried out at different heat treatment temperatures were examined. Shown are flow curves of magnesium alloy samples which were subjected to a heat treatment at 270 ° C. for 4 hours, in Fig. 5 shown as dashed lines, denoted by reference numeral 5, and flow curves of magnesium alloy samples, which were subjected to a heat treatment at 330 ° C for 4 hours, in Fig. 5 Shown as solid lines, marked with reference number 6.
  • Fig. 6 shows a yield stress diagram with flow curves as the result of compression tests with magnesium alloy samples made from Mg-20% Li-24% Al-1% Ca-0.5% Y (in% by weight) at room temperature, with magnesium alloy samples after heat treatments have been carried out at different heat treatment temperatures were examined. Shown are flow curves of magnesium alloy samples which were subjected to a heat treatment at 270 ° C. for 4 hours, in Fig. 6 shown as dashed lines, denoted by reference numeral 7, and flow curves of magnesium alloy samples comprising a Were subjected to heat treatment at 330 ° C for 4 hours, in Fig. 6 shown as solid lines, identified by reference numeral 8.
  • FIG. 6 shows a yield stress diagram with flow curves as the result of compression tests with magnesium alloy samples made from Mg-20% Li-24% Al-1% Ca-0.5% Y (in% by weight) at room temperature, with magnesium alloy samples after heat treatments have been carried out at different heat treatment temperatures were examined. Shown are flow curves of magnesium alloy samples which were subjecte
  • Fig. 7 shows a hardness diagram as the result of hardness tests according to Vickers with magnesium alloy samples made from Mg-20% Li-15% Al-1% Ca-0.5% Y (in% by weight) at room temperature, about 20 ° C., with magnesium alloy samples after performed heat treatments with different heat treatment times were investigated.
  • the heat treatment temperature used was 330 ° C.
  • the hardness diagram shows mean values of hardnesses according to Vickers (HV 0.1) from several measurements depending on different heat treatment times t, from 0 minutes (min) to 300 minutes, of the magnesium alloy samples.
  • HV 0.1 hardness diagram
  • a successive increase in hardness with a heat treatment time can be seen, with a high degree of hardness being achievable in particular with a heat treatment time of more than 60 minutes.
  • This behavior can possibly be explained by a diffusion of calcium into the inner area of the mixed crystal.
  • a magnesium alloy according to the invention thus advantageously has both high strength and good formability, which can be optimized or preferably increased in particular by means of heat treatment. In particular, it is also possible to optimize or set a hardness of the magnesium alloy in a defined manner.
  • the magnesium alloy according to the invention or a component with or made from the magnesium alloy according to the invention thus offers the potential to implement robust and resistant components, in particular structural components, in particular in the automotive industry, aircraft industry and / or space industry, preferably adapted to the purpose.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Powder Metallurgy (AREA)
  • Continuous Casting (AREA)
  • Forging (AREA)
EP19184999.1A 2019-07-08 2019-07-08 Magnesiumlegierung und verfahren zur herstellung derselben Active EP3763845B1 (de)

Priority Applications (14)

Application Number Priority Date Filing Date Title
EP19184999.1A EP3763845B1 (de) 2019-07-08 2019-07-08 Magnesiumlegierung und verfahren zur herstellung derselben
CA3137604A CA3137604A1 (en) 2019-07-08 2020-03-25 Magnesium alloy and method for producing same
PCT/EP2020/058280 WO2021004662A1 (de) 2019-07-08 2020-03-25 Magnesiumlegierung und verfahren zur herstellung derselben
JP2021567860A JP2022540542A (ja) 2019-07-08 2020-03-25 マグネシウム合金およびその製造方法
KR1020227000723A KR20220030244A (ko) 2019-07-08 2020-03-25 마그네슘 합금 및 이의 제조 방법
US17/625,359 US20220259705A1 (en) 2019-07-08 2020-03-25 Magnesium alloy and method for producing same
CN202080046287.5A CN114026260B (zh) 2019-07-08 2020-03-25 镁合金及用于生产其的方法
PCT/EP2020/069131 WO2021005062A1 (de) 2019-07-08 2020-07-07 Legierung mit feinskaligem eutektischen, insbesondere nanoeutektischem, gefüge und herstellung derselben
EP20735621.3A EP3997251A1 (de) 2019-07-08 2020-07-07 Legierung mit feinskaligem eutektischen, insbesondere nanoeutektischem, gefüge und herstellung derselben
CA3138658A CA3138658A1 (en) 2019-07-08 2020-07-07 Alloy having fine-scale eutectic, in particular nanoeutectic, structure and production of such an alloy
JP2021568980A JP2022540544A (ja) 2019-07-08 2020-07-07 微細スケールの共晶組織、具体的にはナノ共晶組織を有する合金、およびそのような合金の製造
CN202080049996.9A CN114096690A (zh) 2019-07-08 2020-07-07 具有精细尺度共晶结构，特别是纳米共晶结构的合金以及这种合金的生产
KR1020227000718A KR20220030243A (ko) 2019-07-08 2020-07-07 미세-규모 공정, 특히, 나노공정, 조직을 갖는 합금 및 이러한 합금의 제조
US17/625,360 US20220267881A1 (en) 2019-07-08 2020-07-07 Alloy having fine-scale eutectic, in particular nanoeutectic, structure and production of such an alloy

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EP20735621.3A Pending EP3997251A1 (de) 2019-07-08 2020-07-07 Legierung mit feinskaligem eutektischen, insbesondere nanoeutektischem, gefüge und herstellung derselben

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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB683813A (en) * 1949-09-29 1952-12-03 Magnesium Elektron Ltd Improvements in or relating to magnesium base alloys
DE1255928B (de) * 1966-01-13 1967-12-07 Metallgesellschaft Ag Verfahren zur Erzielung eines langanhaltenden Veredelungseffektes in Aluminium-Silicium-Legierungen
CN104060137A (zh) * 2014-06-29 2014-09-24 应丽红 一种耐磨硅铝合金
EP3252181A4 (en) * 2015-01-27 2018-06-20 Santoku Corporation Magnesium-lithium alloy, rolled material and shaped article
CN107406926B (zh) * 2015-03-25 2020-11-13 株式会社斯巴鲁 镁锂合金、由镁锂合金构成的轧制材料及含有镁锂合金作为原材料的被加工品
KR20180061348A (ko) * 2015-11-10 2018-06-07 닛산 지도우샤 가부시키가이샤 전기 디바이스용 부극 활물질, 및 이것을 사용한 전기 디바이스
WO2018021360A1 (ja) * 2016-07-26 2018-02-01 株式会社三徳 マグネシウム－リチウム合金及びマグネシウム空気電池
CN106148786B (zh) * 2016-08-22 2018-12-18 上海交通大学 高强度铸造镁锂合金及其制备方法

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EP3763845A1 (de) 2021-01-13
WO2021004662A1 (de) 2021-01-14
KR20220030243A (ko) 2022-03-10
US20220259705A1 (en) 2022-08-18
US20220267881A1 (en) 2022-08-25
CA3137604A1 (en) 2021-01-14
KR20220030244A (ko) 2022-03-10
CN114026260B (zh) 2023-06-20
WO2021005062A1 (de) 2021-01-14
EP3997251A1 (de) 2022-05-18
JP2022540542A (ja) 2022-09-16
JP2022540544A (ja) 2022-09-16
CN114096690A (zh) 2022-02-25
CA3138658A1 (en) 2021-01-14

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