WO2000063452A1 - Alliages de magnesium a haute ductilite, leur procede de production et leur utilisation - Google Patents

Alliages de magnesium a haute ductilite, leur procede de production et leur utilisation Download PDF

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WO2000063452A1
WO2000063452A1 PCT/EP2000/002524 EP0002524W WO0063452A1 WO 2000063452 A1 WO2000063452 A1 WO 2000063452A1 EP 0002524 W EP0002524 W EP 0002524W WO 0063452 A1 WO0063452 A1 WO 0063452A1
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weight
mpa
elongation
magnesium alloy
break
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PCT/EP2000/002524
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German (de)
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WO2000063452A8 (fr
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Wolfgang Sebastian
Karl Ulrich Kainer
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Volkswagen Aktiengesellschaft
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Priority to AT00920534T priority Critical patent/ATE268391T1/de
Priority to DE50006687T priority patent/DE50006687D1/de
Priority to EP00920534A priority patent/EP1171643B1/fr
Publication of WO2000063452A1 publication Critical patent/WO2000063452A1/fr
Publication of WO2000063452A8 publication Critical patent/WO2000063452A8/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
    • C22C23/06—Alloys based on magnesium with a rare earth metal as the next major constituent
    • 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
    • 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 magnesium alloys of high ductility, processes for their production and their use, in particular magnesium alloys containing calcium, strontium, zirconium and / or rare earth elements.
  • magnesium alloys in the range of 1.2 to 1.9 g / cm 3, are of great interest as metallic construction materials, above all for vehicle and aircraft construction. In the future, they will be used more and more for the lightweight construction of motor vehicles and airplanes in order to be able to compensate for the weight of additional elements due to increasing comfort and safety standards, particularly in new low-emission automobiles. They are also of interest for transportable devices or systems that are particularly light-weight for other reasons.
  • the lightweight construction enables the construction of energy-saving vehicles and planes, such as the 3-liter motor vehicle, to a particular extent.
  • the cold formability of the commercially available magnesium alloys is limited due to the hexagonal crystal structure and the associated low ductility. Polycrystalline magnesium and most magnesium alloys behave brittle at room temperature. In addition to good mechanical properties such as high tensile strength, ductile behavior is necessary for numerous applications or for certain manufacturing processes for semi-finished products made of magnesium alloys. An improved forming, energy absorption and deformation behavior requires a higher one Ductility and possibly higher strength and toughness. For this purpose, magnesium alloys with these properties have to be developed or their manufacturing processes have to be further developed, because many material variants have material properties that vary greatly with the manufacturing state.
  • Ductility is the ability of a material to undergo a permanent change in shape, which in the uniaxial state is ideally without any elastic component according to the stress-strain diagram. This property is limited by the occurrence of the break. In general, the permanent elongation achieved in the tensile test up to fracture is considered ductility. As a measure of the ductility, the constriction of the fracture, impact work and notch impact work can also be viewed, each with a slightly different statement. These properties can be determined in accordance with EN 10 002, Part 1, or in accordance with DIN 50115 and 50116.
  • a highly plastic material is called ductile.
  • the elongation at break can often have higher values if only medium-high values of the tensile strength are achieved and that conversely only medium-high values of the elongation at break are achieved with high values of the tensile strength. Very high tensile strength values can only be achieved with comparatively low elongation at break values.
  • the elasticity denotes the elastic part of the stress-strain diagram according to Hook's law, where under ideal linear-elastic conditions there is no permanent change in shape.
  • the ratio of the elastic to the plastic part of the stretch gives the best approximation to reality.
  • the impact work is above all a measure of the energy consumption of a semi-finished product and of plastic behavior, i.e. of the deformability and rate of deformation.
  • a high impact work is therefore essential for the use of deformation elements such as crash elements, impact dampers, impact shields and impact carriers.
  • the impact work - measured on notched specimens - is more meaningful than the notched impact work due to higher absolute values for magnesium alloys and affects a largely uniaxial load.
  • the impact energy which is always determined on notched specimens, also characterizes the susceptibility of a material to failure under three-axis loading. Their significance is particularly low if the execution of the notch significantly influences the values of the impact energy.
  • the impact work and the notch impact work are measured under dynamic load and can give an indication of the energy absorption and deformability. In comparison, tensile and compression tests are carried out under quasi-static loads. A conclusion from uniaxial to multiaxial properties or relationships is only partially possible.
  • the values listed below measured on samples in a certain manufacturing condition therefore reflect the current material properties. They provide an indication of the forming behavior that previously occurred during the forming process. In this state, it is possible to draw a conclusion about the properties and behavior of a semi-finished product or even a component with this semi-finished product, which may be further refined, in later use. Furthermore, a conclusion can be drawn about the material properties of formed alloys, e.g. by bending, pressing, pressure rolling, stretch drawing, deep drawing, hydroforming or roll profiling to be processed into semi-finished products. Since the change in the material properties from the cast to the extruded state is similar to the change in the material properties from the cast to the forged, rolled or a similar formed state, it is therefore also possible to draw a conclusion about another formed state.
  • the elastic properties are usually emphasized, as long as the deformation properties and thus the energy absorption of the element and the plastic behavior are not important, as in an accident.
  • the plastic and, in particular, the plastic and / or elastic properties play a role with regard to the multiple reshaping.
  • These properties are typically for use on the the respective ambient temperature, in extreme cases in the range from -40 ° C to +90 ° C, but at individual points in the vehicle or plane to the locally lower or higher temperatures.
  • the load state is usually multi-axis. The conclusion from uniaxial to multiaxial load states is all the more possible the more isotropic the structure.
  • the production by die casting or extrusion, forging and / or rolling is particularly suitable.
  • the production by die casting or extrusion, forging and / or rolling is particularly suitable.
  • Prerequisite for the use of semi-finished products made of magnesium alloys or of components or parts made from them in automobiles may be the fulfillment of certain property profiles depending on the application, e.g. in the case of deformation elements, seat and door frames, a tensile strength of the light material of at least 100 MPa, preferably of at least 130 MPa, together with an elongation at break measured at room temperature of at least 10%, preferably of at least 15%.
  • higher strength values and a higher ductility are also a relief and in some cases also a prerequisite for the shaping of cast blanks or for the further shaping of already shaped blanks or semi-finished products.
  • the higher these properties are in the cast or powder-compacted state, the higher these are usually also in the formed state.
  • a higher ductility can facilitate the forming or the re-forming, in particular the extrusion. Therefore, an elongation at break of at least 10% is also helpful for the subsequent manufacturing steps for elements made of magnesium alloys.
  • a tensile strength of at least 150 MPa measured at room temperature, preferably of at least 180 MPa, or an elongation at break of at least 18%, preferably of at least 20%, particularly preferably of at least 25%, is therefore recommended for several reasons.
  • the elongation at break in commercially available magnesium alloys, measured at room temperature is usually less than 12%.
  • alloys based on Mg-Al-Zn such as AZ31, AZ61 and AZ80, based on Mg-Zn-Zr such as ZK40 and ZK60 or based on Mg-Mn such as M1.
  • Neite describes in Materials Science and Technology, Vol. 8, ED .: K. H. Matucha, 199 ?, in Chapter 4.3.2 Manufacturing processes and mechanical properties of typical magnesium alloys.
  • tensile strengths of 204 to 340 MPa and elongations at break of 9 to 17% are specified - especially with increasing aluminum content - which could be increased to tensile strength of 380 MPa by artificial aging, but the elongation at break decreased to 6 to 8%.
  • Alloy M1 typically had a tensile strength of 225 MPa and an elongation at break of 12% in the extruded state.
  • For the ZE10 alloy in the rolled and annealed, dynamically recrystallized state 215 to 230 MPa tensile strength and 18 to 23% elongation at break are specified.
  • GB 2,296,256 A gives values of the elongation at break of 17.2 and 18% for alloys MgAI0.5-1.1Mn0.10-0.12, which, however, had a rather low flexural strength.
  • magnesium alloys of increased ductility and, if possible, also increased energy absorption, compressive strength and toughness by selecting the parameters which are most likely to work for these purposes, which have the lowest possible density and, moreover, can also be produced as simply and inexpensively as possible.
  • the object is achieved with a magnesium alloy, the additions or traces of Cd less than 1.8% by weight and the traces of up to 0.1% by weight of Cu, up to 0.05% by weight of Fe and bis can contain up to 0.005% by weight of Ni and is characterized in that its content of Ca, Sr, Zr or / and at least one rare earth element SE including Y and La together is 0.1 to 12% by weight and that its compressive strength is at least 350 MPa, their impact energy measured on unskilled specimens is at least 50 J and their elongation at break measured on tensile specimens is at least 13%.
  • the object is also achieved with a corresponding magnesium alloy, which is an alloy based on AM, AS, AZ31, EM, EZ, MA, ME, MN, MZ, SA, ZE or ZM, the content of which is Ca, Sr, Zr or / and at least one rare earth element including Y and La together 0.1 to 12 wt .-%, the compressive strength is at least 350 MPa, the impact energy is at least 50 J and the elongation at break is at least 13%.
  • a corresponding magnesium alloy which is an alloy based on AM, AS, AZ31, EM, EZ, MA, ME, MN, MZ, SA, ZE or ZM, the content of which is Ca, Sr, Zr or / and at least one rare earth element including Y and La together 0.1 to 12 wt .-%, the compressive strength is at least 350 MPa, the impact energy is at least 50 J and the elongation at break is at least 13%.
  • All of these magnesium alloys preferably have a Ca, Sr, Zr or / and at least one rare earth element content of at least 0.15 to 8% by weight, particularly preferably from 0.2 to 5% by weight, very particularly preferably from 0.25 to 3% by weight.
  • Their compressive strength can preferably be at least 375 MPa, particularly preferably at least 400 MPa;
  • their impact energy can preferably be at least 60 J, particularly preferably at least 70 J and their elongation at break can preferably be at least 16%, particularly preferably at least 18%, very particularly preferably at least 20%.
  • the object is also achieved with a corresponding magnesium alloy, which is an alloy based on AM or MA, which either has no addition of Ca, Sr, Zr or / and at least one rare earth element including Y and La, or the content of Ca, Sr, Zr or / and at least one rare earth element including Y and La together 0.1 to 12 wt .-%, the compressive strength is at least 300 MPa, the impact energy is at least 40 J and the elongation at break is at least 16%.
  • the compressive strength is preferably at least 325 MPa, particularly preferably at least 350 MPa, the impact energy is at least 50 J, particularly preferably at least 60 J and the elongation at break is at least 18%, particularly preferably at least 20%.
  • a corresponding magnesium alloy which is an alloy based on AS or SA, which either has no addition of Ca, Sr, Zr or / and at least one rare earth element including Y and La, or the content of Ca, Sr, Zr or / and at least one rare earth element including Y and La together 0.1 to 12 wt .-% and their compressive strength is at least 320 MPa and their elongation at break is at least 12%.
  • Their compressive strength is preferably at least 340 MPa, particularly preferably at least 360 MPa, very particularly preferably at least 380 MPa, and their elongation at break is at least 14%.
  • the object is also achieved with a corresponding magnesium alloy, which is an alloy based on AZ or ZA, the content of Ca, Sr, Zr or / and at least one rare earth element including Y and La together is 0.1 to 12% by weight and whose compressive strength is at least 340 MPa and whose elongation at break is at least 16%.
  • Their compressive strength is preferably at least 360 MPa, particularly preferably at least 380 MPa, and their elongation at break is at least 18%, particularly preferably at least 20%.
  • the object is also achieved with a corresponding magnesium alloy, which is an alloy based on EM or ME, which either has no addition of Ca, Sr, Zr or / and at least one rare earth element including Y and La, or the content of Ca, Sr, Zr or / and at least one rare earth element including Y and La together 0.1 to 12 wt .-%, the compressive strength is at least 360 MPa and the elongation at break is at least 12%. Their compressive strength is preferably at least 380 MPa and their elongation at break is at least 14%.
  • the object is also achieved with a corresponding magnesium alloy, which is an alloy based on MN, the content of Ca, Sr, Zr or / and at least one rare earth element including Y and La together is 0.1 to 12% by weight and the compressive strength at least 300 MPa and their elongation at break is at least 12%.
  • Their compressive strength is preferably at least 320 MPa, particularly preferably at least 340 MPa, and their elongation at break is at least 14%.
  • the Mn content is in particular at least 1.1% by weight, preferably at least 1.3% by weight.
  • the object is also achieved with a corresponding magnesium alloy, which is an alloy based on EZ or ZE, the content of Ca, Sr, Zr or / and at least one rare earth element including Y and La together being 0.1 to 12% by weight and whose compressive strength is at least 320 MPa and whose elongation at break is at least 18%.
  • Their compressive strength is preferably at least 340 MPa, particularly preferably at least 360 MPa, very particularly preferably at least 380 MPa and their elongation at break is at least 20%.
  • the object is also achieved with a corresponding magnesium alloy, which is an alloy based on MZ or ZM, the content of Ca, Sr, Zr or / and at least one rare earth element including Y and La together is 0.1 to 12% by weight and whose compressive strength is at least 300 MPa and whose elongation at break is at least 12%.
  • Their compressive strength is preferably at least 325 MPa and their elongation at break is at least 16%.
  • the content of Ca, Sr, Zr and / or at least one rare earth element can be from 0.15 to 8% by weight, preferably from 0.2 to 5% by weight, particularly preferably from 0.25 to 3 % By weight.
  • Their compressive strength can preferably be at least 375 MPa, particularly preferably at least 400 MPa and also up to 460 MPa.
  • Your impact work can preferably be at least 40 J, particularly preferably at least 60 J, very particularly preferably at least 80 J and also up to 120 J.
  • Their elongation at break can preferably be at least 16%, particularly preferably at least 19%, very particularly preferably at least 22%, even more preferably at least 25% and up to 30% when measuring tensile samples. All mechanical measurements are related to room temperature.
  • the magnesium alloy can contain 0.5 to 10% by weight of Al, 0.1 to 4% by weight of Mn and possibly 0.1 to 6% by weight of Ca or / and Sr, respectively.
  • Their compressive strength is at least 320 MPa, their elongation at break is at least 16% and their impact energy measured on non-notched samples is at least 25 J.
  • Mg can also contain 0.5 to 10% by weight of AI, 0.1 to 4% by weight of Si and, if appropriate, 0.1 to 6% by weight of Ca or / and Sr, with their compressive strength being at least 350 MPa and their elongation at break at least 13% and their hitting work is at least 50 J.
  • Mg can also contain 0.1 to 4% by weight of Mn and 0.1 to 6% by weight of at least one rare earth element and / or Y, its compressive strength being at least 360 MPa, its elongation at break being at least 13% and its impact energy being at least 40 J. .
  • Mg In addition to Mg, it can also contain 0.2 to 4% by weight of Mn and 0.2 to 6% by weight of Ca or / and 0.1 to 6% by weight of Sr, its compressive strength at least 300 MPa, its elongation at break at least 15% and its impact energy is at least 20 J.
  • Mg can also contain 0.1 to 5% by weight of Zn and 0.1 to 6% by weight of at least one rare earth element including Y and La and optionally 0.1 to 3% by weight of Zr, their compressive strength being at least 320 MPa Elongation at break is at least 20% and its impact energy measured on unskilled specimens is at least 50 J.
  • Mg can also contain 0.1 to 5% by weight of Zn, 0.1 to 4% by weight of Mn and optionally 0.1 to 6% by weight of Ca or / and Sr, with their compressive strength being at least 300 MPa and their elongation at break at least 13% and their hitting work is at least 40 years.
  • These magnesium alloys preferably have a plastic portion of the stress determined in the tensile test according to the stress-strain diagram from the difference of Tensile stress and yield stress of at least 40 MPa, particularly preferably at least 60 MPa, very particularly preferably from 80 to 120 MPa.
  • All of these magnesium alloys can include have been produced by extrusion. However, other forming processes instead of or together with extrusion are advantageous, especially forging. They are preferably formed, in particular extruded or / and forged, and have a fine-grained, dynamically recrystallized structure, in particular with an average grain size of not more than 20 ⁇ m, and a content of precipitation phases of not more than 5% by volume, preferably of not more than 2% by volume. They can preferably have a structure with an average grain size of at most 50 ⁇ m, preferably of at most 25 ⁇ m, particularly preferably of at most 15 ⁇ m, very particularly preferably of at most 8 ⁇ m. The average grain size is determined on bevels using conventional stereometric methods.
  • the remaining contents of the chemical composition mentioned consist predominantly or essentially of magnesium. Contents of cadmium interfere with processing only because of their toxicity, but are otherwise of particular advantage in terms of formability. Trace levels of copper, iron and nickel should be as low as possible, since they have a negative effect on processing and / or material properties.
  • the chemical composition of the magnesium alloys varied only slightly or almost not at all from the composition of the melt to the composition before or after extrusion to the composition of the semi-finished product made from it.
  • the semi-finished product or component according to the invention preferably consists essentially of a magnesium alloy which is selected from the group of alloys based on EM, EZ, ME, MN, MZ, ZE and ZM with a content of at least one rare earth element AM, AS, AZ, MA , MN, MZ, SA, ZA or ZM with calcium or / and strontium addition or EZ, MN or ZE with zirconium addition.
  • the invention further relates to a method for producing such a magnesium alloy, in which an original or compacted shaped body is produced and dynamically recrystallized by shaping and / or shaping.
  • the molded body can therefore have been produced via the melt or / and via powder.
  • a degree of shaping in particular during the extrusion, a degree of shaping of at least 1.5, preferably at least 2 or even at least 3, is selected in order to achieve a dynamic recrystallization and a fine-grained structure.
  • the degree of forming characterizes the degree of cross-sectional reduction during forming and is given as the natural logarithm of the ratio of the starting cross-section to the cross-section after the forming.
  • the formed or / and deformed shaped body can then be processed or processed into a semi-finished product and / or a component made from or with this semi-finished product.
  • the semi-finished product or the component produced from or with the semi-finished product can be directed, e.g. further deformed by bending, pressing, pressure rolling, stretch drawing, deep drawing, hydroforming or roll profiling, e.g. processed, joined and / or e.g. by cutting, drilling, milling, grinding, lapping, polishing can be surface-treated by etching, pickling, painting or other coating.
  • the semi-finished product or the component made therefrom or with it can be produced using at least one low-heat joining process such as gluing, riveting, plugging, pressing, pressing, clinching, folding, shrinking or screwing and / or at least one heat-generating joining process such as composite casting, composite forging, composite extrusion , Composite rolling, soldering or welding, in particular beam welding or fusion welding, with a similar or different type Semi-finished product or component can be connected.
  • the different semi-finished product or component can also consist essentially of a magnesium alloy or of another alloy or also of a non-metallic material. It can have the same or a different geometry as the semi-finished product or component according to the invention.
  • the joining process can be used in particular to produce a housing, an apparatus, a system, a profile construction and / or a cladding from several elements.
  • semi-finished products are to be understood as shaped bodies which have not yet been completed and are ready for use in their respective application.
  • components are the shaped articles suitable for the intended purpose.
  • both terms flow smoothly into one another, since the same molded body can be a semifinished product for one purpose, but can already be a component for the other.
  • the text does not make a strict distinction between semifinished product and component, or both are mentioned at the same time or only spoken of magnesium alloy, although both may be meant.
  • the semi-finished products made of magnesium alloys according to the invention or the components produced therefrom or with them can be used as rims, gearbox housings, steering wheel skeletons, wishbones, frame elements, elements of vehicle cells or vehicle outer skins, vehicle cells, vehicle outer skin, cockpit supports, cockpit skin, housings, floor elements, floors, lids, covers, tank elements , Tank flaps, brackets, supports, brackets, angles, hollow profiles, pipes, deformation elements, crash elements, crash absorbers, impact absorbers, impact shields, impact beams, small parts such as Gears, as impellers and other types of wheels, as welded profile constructions, for the vehicle body, for seat, window or / and door frames, as semi-finished products, components or assemblies on or in the automobile or aircraft.
  • a bolt with a very large diameter can be cast, which can then be pressed with a high-performance extrusion press into round bolts with a diameter that corresponds to the recipient diameter.
  • the segregation is reduced by the thermomechanical treatment.
  • the cast bolts can first be subjected to heat treatment depending on the alloy composition in e.g. 350 ° C are homogenized in the range from 6 h to 12 h in order to eliminate segregations in the structure, which in some cases to improve heterogeneous structure and to increase the pressability. Then the homogenized bolts can be machined to the required dimensions.
  • the extrusion of the magnesium alloys can be carried out in the same extrusion plants that are used for the extrusion of aluminum alloys, both via direct and indirect extrusion.
  • the deformation behavior must only be specifically taken into account when designing the tool (die).
  • Sharp-edged inlets, such as those used with aluminum alloys, should be avoided with magnesium alloys, otherwise there is a risk of surface cracks. In many cases e.g. an inlet angle of approx. 50 ° is used for matrices of round profiles for magnesium alloys.
  • the most important parameter besides the extrusion temperature is the extrusion speed, because it significantly influences the properties and the surface quality of the extrusion profiles.
  • a high pressure also requires a high extrusion speed, which is sought for economic reasons.
  • a high extrusion speed is usually associated with an even better surface quality.
  • the pressability of the magnesium alloys is comparable to that of hard-pressed aluminum alloys.
  • a high extrusion speed is desirable from an economic point of view, but is not always feasible with magnesium alloys.
  • the parameters for the extrusion usually have to be worked out in detail, since there is a great potential for optimization.
  • the extrusion is advantageously followed by a heat treatment.
  • This heat treatment is usually not of great interest since the alloys according to the invention are usually not greatly improved by this heat treatment.
  • the semi-finished products can be straightened, further shaped, processed, joined and / or surface treated.
  • solid and extruded profiles in simple or complicated cross sections can be extruded without problems.
  • semi-finished products can be improved or components can be produced from them or, if necessary, from them.
  • a AI, E denotes at least one rare earth element SE, with La and Y also being counted among the rare earth elements, M or MN Mn, S Si and Z Zn - usually with contents in% by weight, unless stated otherwise .
  • alloy information such as AZ31 are indicated by the numbers, as usual for the respective alloy, only in the order of magnitude, which can vary to a relatively wide extent, as is customary in the industry.
  • a low manganese content may be present in the starting alloy used in the examples and the modified AZ-based alloys produced therewith. All examples showed traces of less than 0.1 wt% Cd, less than 0.05 wt% Cu, less than 0.04 wt% Fe and less than 0.003 wt% Ni .
  • the alloys were made as high-purity commercially available alloys or usually from high-purity starting alloys such as AM, AS or AZ alloys or by adding high-purity magnesium HP-Mg, a rare earth element-containing master alloy with a ratio of Nd to other rare earths including yttrium of 0.92, a zirconium-containing master alloy, alloyed with calcium or strontium.
  • the standard alloys contained an Mn content of up to about 0.2% by weight.
  • the alloys were melted in a steel crucible under the protective gas atmosphere of an Ar-SF 6 mixture. The melt was kept and cast at a temperature in the range from 780 to 820 ° C., once also at 750 ° C.
  • the blanks required for the subsequent extrusion were cast in a cylindrical steel mold with machining allowance.
  • the mold had a diameter of 90 or 110 mm and a mold temperature in the range from 80 to 320 ° C.
  • the element contents achieved were checked spectroscopically. With all alloys, care was taken to ensure that the structure of the cast body is as homogeneous as possible and free of impurities, since this can have a sensitive effect on ductility. All alloys could be melted, poured off and processed into bolts without any problems.
  • the castings were then homogenized at 350 ° C. over 12 h.
  • bolts of 70 mm in diameter and 120 mm in length were produced; for 6 samples of the alloy AZ31CaO, 3, however, a diameter of 74 mm was chosen.
  • the homogenized and turned bolts were then well prepared for extrusion.
  • the bolts were then heated to the respective extrusion temperature in the range from 200 to 450 ° C., warmed through for 60 to 150 minutes and extruded in a 400 t horizontal press.
  • the temperature of the pin is therefore the temperature that the pin has when it enters the extrusion press.
  • Preliminary tests were carried out with the AZ31 alloy in a 400 t extrusion press with direct extrusion (Tables 1 and 2). With a recipient diameter of 74 mm, a wide range of parameters could be successfully examined.
  • the preliminary tests allowed the test parameters to be defined.
  • the appropriate extrusion parameters were selected in systematic preliminary tests on the AZ31 reference alloy; The mechanical properties and the average grain sizes were determined on the extruded samples (Tables 1 and 2).
  • the results of the preliminary tests essentially determined the test parameters of the subsequent tests.
  • the extrusion pressures that occurred varied in a wide range depending on the alloy used and the parameters set.
  • the final pressures reached were for alloys without Ca, SE or Zr addition in the range of 10 ⁇ 2 MPa at extrusion temperatures above 300 ° C and for Ca, SE or Zr-containing alloys up to 4 MPa higher.
  • the reason for the higher extrusion pressures and thus for the increased deformation resistance of magnesium alloys with Ca, SE or Zr addition is a higher proportion of stable precipitates than with magnesium alloys without this addition. For lower temperatures, somewhat higher extrusion pressures were generally determined.
  • All alloys both the starting alloys and the alloys modified by additives, could easily be formed in a wide range of temperatures, extrusion speeds and extrusion ratios.
  • the extrusion pressures that occurred varied depending on the alloy used and the extrusion parameters set.
  • the bolts showed good compressibility with a large scope in terms of pressing force and pressing speed.
  • the lower extrusion temperature is due to the insufficient plastic deformability below a temperature in the range of about 200 to 220 ° C, the upper extrusion temperature is limited by the proximity to the eutectic temperature and possibly by the first formation of parts of a melt-liquid phase.
  • the measurement results of the Brinell hardness determinations made no special statements possible.
  • the Brinell hardness of the extruded samples was found to be 7 to 22% greater than that of the cast samples.
  • the hardness increased with the aluminum content.
  • the tensile strength was up to 287 MPa
  • the compressive strength up to 365 MPa
  • the elongation at break up to 21.6%
  • the impact energy of notched specimens up to 85 J ( Tables 3a / c). All of these material properties were therefore significantly higher than those determined on samples in the cast state.
  • the average grain sizes trended with the extrusion temperature e.g. in the range of 6 to 12 ⁇ m or 3.5 to 10 ⁇ m.
  • the average grain size was in the range from 4.5 to 9 ⁇ m and thus smaller due to the addition of Ca, the average grain sizes also increasing somewhat in proportion to the extrusion temperature.
  • the extruded alloy MN150Ca0.2 showed a very strong increase in most mechanical properties compared to the extruded alloy MN150.
  • the addition of Zr0.7 to the extruded starting alloy MN150 had little effect.
  • Lower mechanical properties were determined for the extruded ZE10 alloy, but these varied greatly with the temperature, so that even better mechanical properties can be achieved with an even higher temperature:
  • the properties of the ZE10 alloy are significantly influenced by the rare earths and can the variation of the rare earth elements including lanthanum and yttrium and their contents can be further optimized.
  • the impact work on unskilled specimens had decreased slightly in comparison to the specimens of the ZE10 alloy.
  • the zirconium additive stabilized the structure of the extruded ZE10ZrO.7 alloy.
  • microstructures with average grain sizes in the range of 2.2 to 4.5 ⁇ m were created. These small grain sizes were created over a wide range of extrusion parameters. The slight variation in grain size depending on the extrusion parameters was striking with this alloy.
  • magnesium alloys in particular were found to be suitable, in which each 1% by weight of AI had a Ca content in the range from about 0.05 to 0.2 % By weight of Ca was added in order to enable the Al 2 Ca phase to be eliminated.
  • the phase AI 2 Ca proved to be more temperature stable than the phase Mg 17 AI 12 and was therefore able to hinder the grain growth during extrusion better than the phase Mg 17 AI 12 .
  • the Mg 2 Si precipitation phase also prevented grain growth during extrusion better than the Mg 17 AI 12 phase.
  • the addition of Ca to Al-free alloys led to the formation of Mg 2 Ca or Ca 5 Zn 2 precipitates.
  • phase Mg 17 Al 12 which normally appears with magnesium alloys containing Al, does cause a somewhat increased strength, but is also responsible for a lower elongation at break. Since this phase is even more brittle than the pure hexagonal Mg phase, larger contents of Mg ⁇ 7 AI 12 should be avoided.
  • magnesium alloys according to the invention are inexpensive for extrusion, but in principle, in addition or as an alternative to extrusion, they are also suitable for other types of shaping and further shaping on account of their material properties.
  • Table 1 Results of the preliminary tests to determine the extrusion parameters with the AZ31 alloy at an extrusion temperature of 400 ° C, a die diameter of 16 mm, a recipient diameter of 74 mm and a compression ratio of 1:21
  • Table 2 Influence of the compression ratio on the average grain sizes and the mechanical properties from the tensile test at an extrusion temperature of 400 ° C. in the preliminary tests to determine the extrusion parameters
  • Table 3a Average values of the measurement results of the mechanical tests on various samples of the CA. Magnesium alloys containing Sr, SE and Zr and their starting alloys:
  • Table 3b Average values of the values that can be determined from the stress-strain diagram of the tensile tests for modified magnesium alloys and their starting alloys.
  • Table 3c Highest mean values of the measurement results of the mechanical properties selected from various individual samples of the modified magnesium alloys:
  • Table 3d Mainly occurring grain sizes in the as-cast state after homogenization at 350 ° C for 4 h or after extrusion with the modified magnesium alloys and their starting alloys
  • Table 3e Process parameters for various samples of the modified magnesium alloys and their starting alloys.
  • Table 3f Manufacturing parameters and material properties of individually selected extruded samples of the modified alloys and their starting alloys: length of bolt 120 mm, diameter of bolt 70 mm, mold diameter mostly 90 mm

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  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
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  • Crystallography & Structural Chemistry (AREA)
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Abstract

L'invention concerne un alliage de magnésium qui peut contenir des additifs ou des traces de Cd en une quantité inférieure à 1,8 % en poids, lesdites traces ayant une teneur en Cu pouvant aller jusqu'à 0,1 % en poids, une teneur en Fe pouvant aller jusqu'à 0,05 % en poids et une teneur en Ni pouvant aller jusqu'à 0,05 % en poids. Cet alliage se caractérise par le fait qu'il est à base de AM, AS, AZ31, EM, EZ, MA, ME, MN, MZ, SA, ZE ou ZM et présente, éventuellement, une teneur en Ca, Sr, Zr et/ou au moins en un élément des terres rares, y compris en Y et en La, qui est de 0,1 à 12 % en poids. L'invention concerne en outre un procédé permettant de produire un tel alliage de magnésium, selon lequel on produit un corps façonné par formage original ou compactage, lequel est recristallisé de façon dynamique par transformation ou déformation. L'invention concerne aussi un semi-fini constitué de cet alliage de magnésium, ou bien un composant produit à partir de ce semi-fini ou avec ce semi-fini, ou bien encore un composite comportant un tel semi-fini ou un tel composant.
PCT/EP2000/002524 1999-04-03 2000-03-22 Alliages de magnesium a haute ductilite, leur procede de production et leur utilisation WO2000063452A1 (fr)

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AT00920534T ATE268391T1 (de) 1999-04-03 2000-03-22 Magnesiumlegierungen hoher duktilität, verfahren zu deren herstellung und deren verwendung
DE50006687T DE50006687D1 (de) 1999-04-03 2000-03-22 Magnesiumlegierungen hoher duktilität, verfahren zu deren herstellung und deren verwendung
EP00920534A EP1171643B1 (fr) 1999-04-03 2000-03-22 Alliages de magnesium a haute ductilite, leur procede de production et leur utilisation

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Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2002099147A1 (fr) * 2001-06-06 2002-12-12 Noranda, Inc. Alliages de moulage a base de magnesium dotes de caracteristiques ameliorees a temperatures elevees

Families Citing this family (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
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DE10221720A1 (de) * 2002-05-16 2003-11-27 Bayerische Motoren Werke Ag Magnesiumlegierung
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GB201700714D0 (en) * 2017-01-16 2017-03-01 Magnesium Elektron Ltd Corrodible downhole article
US11998192B2 (en) 2021-05-10 2024-06-04 Cilag Gmbh International Adaptive control of surgical stapling instrument based on staple cartridge type

Citations (22)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB831638A (en) * 1957-06-05 1960-03-30 Dow Chemical Co Magnesium-base alloy
US3024108A (en) * 1960-02-19 1962-03-06 Dow Chemical Co Magnesium-base alloy
DE1179008B (de) * 1956-07-27 1964-10-01 Fuchs Fa Otto Magnesiumknetlegierungen und deren Verwendung
EP0414620A1 (fr) * 1989-08-24 1991-02-27 PECHINEY RECHERCHE (Groupement d'Intérêt Economique régi par l'Ordonnance du 23 Septembre 1967) Immeuble Balzac Procédé d'obtention d'alliages de magnésium par pulvérisation-dépôt
US4997622A (en) * 1988-02-26 1991-03-05 Pechiney Electrometallurgie High mechanical strength magnesium alloys and process for obtaining these alloys by rapid solidification
US5071474A (en) * 1990-06-15 1991-12-10 Allied-Signal Inc. Method for forging rapidly solidified magnesium base metal alloy billet
US5078962A (en) * 1989-08-24 1992-01-07 Pechiney Electrometallurgie High mechanical strength magnesium alloys and process for obtaining these by rapid solidification
US5143564A (en) * 1991-03-28 1992-09-01 Mcgill University Low porosity, fine grain sized strontium-treated magnesium alloy castings
US5147603A (en) * 1990-06-01 1992-09-15 Pechiney Electrometallurgie Rapidly solidified and worked high strength magnesium alloy containing strontium
DE4208504A1 (de) * 1992-03-17 1993-09-23 Metallgesellschaft Ag Maschinenbauteil
JPH06200348A (ja) * 1992-05-22 1994-07-19 Mitsui Mining & Smelting Co Ltd 高強度マグネシウム合金
JPH07278717A (ja) * 1994-04-12 1995-10-24 Ube Ind Ltd 加圧部での耐へたり性に優れたマグネシウム合金製部材
JPH0841576A (ja) * 1994-07-28 1996-02-13 Honda Motor Co Ltd 高強度マグネシウム合金及びマグネシウム合金鋳物の熱処理方法
WO1996025529A1 (fr) * 1995-02-17 1996-08-22 Institute De La Technologie Du Magnesium, Inc. Alliages de magnesium resistant au fluage, pour la coulee sous pression
US5552110A (en) * 1991-07-26 1996-09-03 Toyota Jidosha Kabushiki Kaisha Heat resistant magnesium alloy
EP0791662A1 (fr) * 1996-02-27 1997-08-27 Honda Giken Kogyo Kabushiki Kaisha Alliage de magnésium résistant à la chaleur
JPH09263871A (ja) * 1996-03-29 1997-10-07 Mitsui Mining & Smelting Co Ltd 高強度マグネシウム合金製の熱間鍛造品及びその製造法
EP0799901A1 (fr) * 1996-04-04 1997-10-08 Mazda Motor Corporation Alliage à base de magnesium résistant à la chaleur
JPH09271919A (ja) * 1996-04-04 1997-10-21 Mitsui Mining & Smelting Co Ltd 耐熱マグネシウム合金部材の製造方法およびそれに用いるマグネシウム合金、並びにマグネシウム合金成形部材
US5681403A (en) * 1993-06-28 1997-10-28 Nissan Motor Co., Ltd. Magnesium alloy
US5693158A (en) * 1993-02-12 1997-12-02 Mazda Motor Corporation Magnesium light alloy product and method of producing the same
JPH09316586A (ja) * 1996-05-29 1997-12-09 Mitsui Mining & Smelting Co Ltd 耐熱・耐摩耗マグネシウム合金

Family Cites Families (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE742684C (de) * 1937-11-23 1943-12-15 Ig Farbenindustrie Ag Verwendung von Magnesiumlegierungen
DE1259578B (de) * 1959-05-01 1968-01-25 Dow Chemical Co Verfahren zur pulvermetallurgischen Herstellung einer dispersionsverfestigten Magnesiumlegierung
GB901324A (en) * 1959-09-09 1962-07-18 Magnesium Elektron Ltd Improvements in or relating to magnesium base alloys
US3094413A (en) * 1960-09-14 1963-06-18 Magnesium Elektron Ltd 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
US3119684A (en) * 1961-11-27 1964-01-28 Dow Chemical Co Article of magnesium-base alloy and method of making
US3419385A (en) * 1964-10-22 1968-12-31 Dow Chemical Co Magnesium-base alloy
GB1061398A (en) * 1964-11-19 1967-03-15 Magnesium Elektron Ltd Nuclear fuel cans
DE9400065U1 (de) * 1994-01-04 1994-02-24 Geck, Hans-Lothar, 58579 Schalksmühle Sargbeschlag aus Metall

Patent Citations (22)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE1179008B (de) * 1956-07-27 1964-10-01 Fuchs Fa Otto Magnesiumknetlegierungen und deren Verwendung
GB831638A (en) * 1957-06-05 1960-03-30 Dow Chemical Co Magnesium-base alloy
US3024108A (en) * 1960-02-19 1962-03-06 Dow Chemical Co Magnesium-base alloy
US4997622A (en) * 1988-02-26 1991-03-05 Pechiney Electrometallurgie High mechanical strength magnesium alloys and process for obtaining these alloys by rapid solidification
EP0414620A1 (fr) * 1989-08-24 1991-02-27 PECHINEY RECHERCHE (Groupement d'Intérêt Economique régi par l'Ordonnance du 23 Septembre 1967) Immeuble Balzac Procédé d'obtention d'alliages de magnésium par pulvérisation-dépôt
US5078962A (en) * 1989-08-24 1992-01-07 Pechiney Electrometallurgie High mechanical strength magnesium alloys and process for obtaining these by rapid solidification
US5147603A (en) * 1990-06-01 1992-09-15 Pechiney Electrometallurgie Rapidly solidified and worked high strength magnesium alloy containing strontium
US5071474A (en) * 1990-06-15 1991-12-10 Allied-Signal Inc. Method for forging rapidly solidified magnesium base metal alloy billet
US5143564A (en) * 1991-03-28 1992-09-01 Mcgill University Low porosity, fine grain sized strontium-treated magnesium alloy castings
US5552110A (en) * 1991-07-26 1996-09-03 Toyota Jidosha Kabushiki Kaisha Heat resistant magnesium alloy
DE4208504A1 (de) * 1992-03-17 1993-09-23 Metallgesellschaft Ag Maschinenbauteil
JPH06200348A (ja) * 1992-05-22 1994-07-19 Mitsui Mining & Smelting Co Ltd 高強度マグネシウム合金
US5693158A (en) * 1993-02-12 1997-12-02 Mazda Motor Corporation Magnesium light alloy product and method of producing the same
US5681403A (en) * 1993-06-28 1997-10-28 Nissan Motor Co., Ltd. Magnesium alloy
JPH07278717A (ja) * 1994-04-12 1995-10-24 Ube Ind Ltd 加圧部での耐へたり性に優れたマグネシウム合金製部材
JPH0841576A (ja) * 1994-07-28 1996-02-13 Honda Motor Co Ltd 高強度マグネシウム合金及びマグネシウム合金鋳物の熱処理方法
WO1996025529A1 (fr) * 1995-02-17 1996-08-22 Institute De La Technologie Du Magnesium, Inc. Alliages de magnesium resistant au fluage, pour la coulee sous pression
EP0791662A1 (fr) * 1996-02-27 1997-08-27 Honda Giken Kogyo Kabushiki Kaisha Alliage de magnésium résistant à la chaleur
JPH09263871A (ja) * 1996-03-29 1997-10-07 Mitsui Mining & Smelting Co Ltd 高強度マグネシウム合金製の熱間鍛造品及びその製造法
EP0799901A1 (fr) * 1996-04-04 1997-10-08 Mazda Motor Corporation Alliage à base de magnesium résistant à la chaleur
JPH09271919A (ja) * 1996-04-04 1997-10-21 Mitsui Mining & Smelting Co Ltd 耐熱マグネシウム合金部材の製造方法およびそれに用いるマグネシウム合金、並びにマグネシウム合金成形部材
JPH09316586A (ja) * 1996-05-29 1997-12-09 Mitsui Mining & Smelting Co Ltd 耐熱・耐摩耗マグネシウム合金

Non-Patent Citations (14)

* Cited by examiner, † Cited by third party
Title
A RAMAN: "USES OF RARE EARTH METALS AND ALLOYS IN METALLURGY", ZEITSCHRIFT FUR METALLKUNDE,DR.RIEDERER VERLAG GMBH. STUTTGART,DE, vol. 68, no. 3, March 1977 (1977-03-01), pages 163 - 166, XP002142630, ISSN: 0044-3093 *
AMERICAN SOCIETY FOR METALS: "METALS HANDBOOK, BAND 2, SEITEN 480-491, PROPERTIES OF MAGNESIUM ALLOYS", METALS PARK, ASM,US, VOL. VOL. 2, XP002142632 *
B.L. MORDIKE ET AL: "Magnesium alloys and their applications", 1998, WERKSTOFF-INFORMATIONSGESELLSCHAFT MBH, FRANKFURT, DE, XP002151320 *
B.L.MORDIKE ET AL: "Magnesium alloys and their applications", 1998, WERKSTOFF-INFORMATIONSGESELLSCHAFT MBH, FRANKFURT, DE, XP002151319 *
CHEMICAL ABSTRACTS, vol. 128, no. 8, 23 February 1998, Columbus, Ohio, US; abstract no. 91825, HIRATA, KOUSHIROU ET AL: "Effects of aluminum content and heat treatment on tensile properties of semi-solid formed Mg-Al alloys" XP002151321 *
DATABASE WPI Section Ch Week 9433, Derwent World Patents Index; Class M, Page 26, AN 1994-269751[33], XP002151322 *
KEIKINZOKU (1997), 47(12), 672-678 *
M NAKANISHI ET AL: "TENSILE PROPERTIES OF THE ZK60 MAGNESIUM ALLOY PRODUCED BY HOT EXTRUSION OF MACHINED CHIP", JOURNAL OF MATERIALS SCIENCE LETTERS,GB,CHAPMAN AND HALL LTD. LONDON, vol. 17, no. 23, 1 December 1998 (1998-12-01), pages 2003 - 2005, XP002142629, ISSN: 0261-8028 *
MOHRI TAKESHI ET AL: "MICROSTRUCTURE AND MECHANICAL PROPERTIES OF A MG-4Y-3RE ALLOY PROCESSED THERMO-MECHANICAL TREATMENT", STN CHEMICAL ABSTRACTS,XX,XX, vol. 130, no. 8, 20 October 1997 (1997-10-20), XP002142637 *
MUKHINA I Y ET AL: "INVESTIGATION OF THE MICROSTRUCTURE AND PROPERTIES OF CASTABLE NEODYMIUM- AND YTTRIUM-BEARING MAGNESIUM ALLOYS AT ELEVATED TEMPERATURES", METAL SCIENCE AND HEAT TREATMENT,US,CONSULTANTS BUREAU. NEW YORK, vol. 39, no. 5/06, 1 May 1997 (1997-05-01), pages 202 - 206, XP000739773, ISSN: 0026-0673 *
PATENT ABSTRACTS OF JAPAN vol. 1996, no. 02 29 February 1996 (1996-02-29) *
PATENT ABSTRACTS OF JAPAN vol. 1996, no. 06 28 June 1996 (1996-06-28) *
PATENT ABSTRACTS OF JAPAN vol. 1998, no. 02 30 January 1998 (1998-01-30) *
PATENT ABSTRACTS OF JAPAN vol. 1998, no. 04 31 March 1998 (1998-03-31) *

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2002099147A1 (fr) * 2001-06-06 2002-12-12 Noranda, Inc. Alliages de moulage a base de magnesium dotes de caracteristiques ameliorees a temperatures elevees

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DE19915277A1 (de) 2000-10-05
ATE268391T1 (de) 2004-06-15

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