US20130143070A1

US20130143070A1 - Aluminium Material Which Can Be Exposed To High Temperatures, Is Alloyed With Scandium And Has Improved Extrudability

Info

Publication number: US20130143070A1
Application number: US13/752,834
Authority: US
Inventors: Frank Palm
Original assignee: Airbus Operations GmbH
Current assignee: Airbus Operations GmbH
Priority date: 2010-07-29
Filing date: 2013-01-29
Publication date: 2013-06-06
Also published as: EP2598664A1; EP2598664B1; DE102010032768A1; WO2012013185A1

Abstract

The present invention relates to the use of a process for producing an aluminium material which can be exposed to high temperatures and is alloyed with scandium. In this process, a precursor material made of an alloy comprising the metals aluminium and scandium is introduced into a vacuum chamber, the precursor material is subjected to vacuum degassing and the precursor material is treated with nitrogen gas. This is followed by final vacuum degassing of the precursor material.

Description

CROSS-REFERENCE TO RELATED APPLICATIONS

This application is a continuation of International Application No. PCT/DE2011/001504, filed on Jul. 25, 2011, which claims the benefit of the filing date of German Patent Application No. 10 2010 032 768.9 filed Jul. 29, 2010, the disclosures of which applications are hereby incorporated herein by reference.

BACKGROUND OF THE INVENTION

A high temperature-loadable aluminium material alloyed with scandium with improved extrudability.
The invention relates to a high temperature-loadable aluminium material alloyed with scandium, a method for its manufacture as well as the use of a method for its manufacture.
In both aviation and automotive engineering, special alloys are needed to fabricate semi-finished products and components with a high strength and ductility. The weight and corrosion resistance also play an important role.
The manufacture of high-strength aluminium materials alloyed with scandium has been frequently described over the last four decades in various forms of semi-finished products, e.g., sheets, profiles, forgings or castings. These materials exhibit a high strength, a high metallurgical stability and a very good corrosion resistance. The improved strength of these materials is rooted in the precipitation of coherent Al₃Sc phases, which can be specifically generated through defined heat treatment.
For example, aluminium-magnesium materials alloyed with scandium are known from U.S. Pat. No. 3,619,181, U.S. Pat. No. 6,258,318 B1 or EP 0918095 A1. DE 102 48 594 describes a method for manufacturing aluminium sheet materials alloyed with scandium or zirconium that exhibit an elevated fracture toughness. Known from U.S. Pat. No. 4,104,061 is a method for removing contaminants from a metal alloy, in which an alloy is subjected to several cycles of vacuum degassing and gassing with a purging gas.
However, aluminium materials alloyed with scandium often do not exhibit a sufficiently high, durable strength at elevated temperatures. For example, it is known that AlMgSc alloys must be extruded at relative low temperatures of between 300 and 350° C., since the high temperature of the billets would otherwise lead to an undesired loss of cohesion by the AlMgSc material due to the ageing of the Al₃Sc precipitates. However, the molding resistance of this alloy is tangibly elevated at these temperatures, so that operations can only proceed at a diminished extrusion rate. This problem is further aggravated by the heating of the extruded AlMgSc material during the molding process inside the extrusion matrix. Known as adiabatic heating, this process inevitably runs its course during the extrusion of aluminium materials, and leads to an additional heating of the AlMgSc material, so that despite the defined heating of the billet to 350° C., the formability makes it possible to reach 400° C. for a short time in the alloy, or even 450° C. at a high extrusion rate. In terms of materials engineering, the result of an additional heat supply must be equated with a distinct excessive ageing, and a concurrent loss of cohesion by the alloy. For example, such a softened material exhibits a tangibly diminished tensile strength.
Therefore, there is a demand for an aluminium material that does not exhibit these shortcomings.

BRIEF SUMMARY OF THE INVENTION

The object of the present invention is to provide a method for manufacturing an aluminium material alloyed with scandium, as well as the use of such a method, which improves the high temperature-loadability of this material. It is further desirable to provide a method for manufacturing an aluminium material alloyed with scandium, as well as the use of such a method, which makes it possible to reduce the employed quantity of scandium.
Another object of the present invention is to provide an aluminium material alloyed with scandium as well as a method for its manufacture, wherein the aluminium material alloyed with scandium exhibits an improved strength and improved thermal stability. In addition, it is desirable to provide an aluminium material alloyed with scandium that can be molded at high temperatures without the alloy losing cohesion. Furthermore, it is desirable for the aluminium material alloyed with scandium to exhibit an improved extrudability and that it be possible to process it at a high extrusion rate.
A solution according to the invention is described in the independent claims. Preferred embodiments are obtained via combination with the features in the subclaims.
One aspect of the invention indicates the use of a method encompassing the following steps: (a) Introducing a primary material comprising an alloy encompassing the metals aluminium and scandium into a vacuum chamber, (b) vacuum degassing the primary material, (c) gassing the primary material with nitrogen, and (d) subjecting the primary material to final vacuum degassing, in order to manufacture a high temperature-loadable aluminium material alloyed with scandium.
Another aspect of the invention indicates a method for manufacturing a high temperature-loadable aluminium material alloyed with scandium encompassing the following steps: (a) Introducing a primary material comprising an alloy encompassing the metals aluminium and scandium into a vacuum chamber, (b) vacuum degassing the primary material, (c) gassing the primary material with nitrogen, and (d) subjecting the primary material to final vacuum degassing.
Another aspect of the invention indicates a method for manufacturing a high temperature-loadable aluminium material alloyed with scandium encompassing the following steps: (a) Introducing a primary material comprising an alloy encompassing the metals aluminium and scandium into a vacuum chamber, wherein the primary material was fabricated according to the melt spinning process, (b) vacuum degassing the primary material, (c) gassing the primary material with nitrogen, and (d) subjecting the primary material to final vacuum degassing.
Another aspect of the present invention involves providing a high temperature-loadable aluminium material alloyed with scandium, which can be obtained in a method encompassing the following steps: (a) Introducing a primary material comprising an alloy encompassing the metals aluminium and scandium into a vacuum chamber, (b) vacuum degassing the primary material, (c) gassing the primary material with nitrogen, and (d) subjecting the primary material to final vacuum degassing.
Another aspect of the present invention involves providing a high temperature-loadable aluminium material alloyed with scandium, which can be obtained in a method encompassing the following steps: (a) Introducing a primary material comprising an alloy encompassing the metals aluminium and scandium into a vacuum chamber, wherein the primary material was fabricated according to the melt spinning process, (b) vacuum degassing the primary material, (c) gassing the primary material with nitrogen, and (d) subjecting the primary material to final vacuum degassing.
Preferred embodiments are disclosed in the corresponding, dependent claims.

DETAILED DESCRIPTION

The method according to the invention and/or its use allows the manufacture of AlSc materials that exhibit a greater processing window for fabricating semi-finished products. For example, the materials manufactured based on the method according to the invention and/or its use can be processed at higher temperatures, faster extrusion rates and higher press molding conditions. For example, this is advantageous for the fabrication of semi-finished products via the extrusion method.
In addition, the method enables the manufacture of lightweight and corrosion-proof AlSc materials with a very high thermal stability. These materials manufactured according to the invention exhibit a high toughness and tolerance to damage, and enable cost-effective processing. The advantage to the method according to the invention and its use is that strengthening takes place “in situ”, and, for example, there is no need for the use of nanoscale reinforcing phase powders, which are difficult to process and explosive.
Within the framework of the present invention, “aluminium material” is understood as a metallic material that essentially consists of aluminium, and can be alloyed with other metals.
Within the framework of the present invention, a “high temperature-loadable AlSc-material” is an aluminium material alloyed with scandium and possibly even other metals, whose structure or microstructure remains largely stable at a temperature load in excess of 350° C., i.e., the grain size and quantity of precipitants remains largely constant, along with their size and distribution, so that the material possesses strength characteristics at room temperature similar to those before temperature exposure. Within the framework of the present invention, a “high temperature-loadable AlSc material” preferably exhibits a drop in tensile strength R_mof less than 5% after exposed to a temperature of 350° C. by comparison to the initial material at room temperature, or a drop in tensile strength R_mof less than 10% after exposed to a temperature of 375° C. by comparison to the initial material at room temperature.
A use described herein of a method for manufacturing a high temperature-loadable aluminium material alloyed with scandium encompasses the following procedural steps: (a) Introducing a primary material comprising an alloy encompassing the metals Al and Sc into a vacuum chamber, (b) vacuum degassing the primary material, (c) gassing the primary material with nitrogen, and (d) subjecting the primary material to final vacuum degassing.
The primary material used in the method comprises an alloy encompassing the metals aluminium and scandium. The quantity of scandium in the alloy can lie between 0.1 and 10.0% w/w relative to the overall weight of the alloy, for example between 0.2 and 2.0% w/w or 0.5 and 1.5% w/w. The alloy preferably contains scandium in a quantity of 0.6 to 1.0% w/w relative to the overall weight of the alloy.
In an embodiment, the alloy additionally encompasses at least one other, optional metal, which in the aluminium materials exhibits similar properties to scandium, for example Zr, Ti, Y, Hf, Ta, La, Ce, Tb, Nd, Eu, Gd, Dy, Ho and Er. The quantity of one or more of these elements in the alloy can respectively measure up to 5% w/w, and overall up to 10% w/w relative to the overall weight of the alloy. These elements can act in an additive manner with the scandium, i.e., they can be “forcibly dissolved” with the scandium in the aluminium material, and thereby enable an increase in strength via precipitation hardening. The Al₃Sc phase is here modified by replacing part of the scandium with one of the aforementioned elements.
In an embodiment of the present invention, the alloy used as the primary material encompasses zirconium in addition to aluminium and scandium The quantity of zirconium in the alloy can lie between 0.05 and 5.0% w/w relative to the overall weight of the alloy, for example between 0.1 and 1.0% w/w or 0.2 and 0.7% w/w. The alloy preferably contains zirconium in a quantity of 0.3 to 0.5% w/w.
It is assumed that adding zirconium to an AlSc alloy modifies the precipitated A₃Sc phase to Al₃Sc_1-xZr_x, without it losing any of its strength-increasing effect. For example, adding zirconium makes it possible to reduce the minimal cooling rate that must be observed to generate a mixed crystal oversaturated with scandium and zirconium. This slows the excessive ageing, and hence the loss in strengthening capability. As a result, the AlScZr alloy can withstand a specific temperature for a longer period of time before starting to excessively age. At the same time, using zirconium enables a certain reduction in the quantity of scandium in the alloy, which is a relatively expensive alloy element in light of its rarity.
In another embodiment of the present invention, the alloy contains at least one other, optional element additionally or alternatively to the aforementioned alloy elements from the group encompassing Mg, Zn, Mn, Ag, Li, Cu, Si, Cr or Ca. The quantity of these elements in the alloy can measure up to 10% w/w for Mg, and up to 5% w/w for the respective other elements, and up to 25% w/w overall relative to the respective overall weight of the alloy. Adding these elements makes it possible to specifically influence the properties of the material fabricated out of the primary material. For example, adding lithium or calcium reduces the overall density of the generated material, and thereby enables the manufacture of especially lightweight materials. Adding magnesium and/or manganese elevates the strength of the aluminium material, and thereby enables the manufacture of especially hard materials.
In an exemplary embodiment, the primary material comprises an alloy encompassing the metals aluminium, magnesium and scandium. In another exemplary embodiment, the primary material comprises an alloy encompassing the metals aluminium, magnesium, manganese, scandium and zirconium.
As a rule, commercially available aluminium alloys always contain undesirable, but mostly tolerable contaminants. Examples of such contaminants include elements such as alkali metals, Fe, Si, Be or In. These contaminants can each be present in a quantity of up to about 0.5% w/w, and overall in a quantity of up to 2% w/w relative to the respective overall weight of the alloy. However, such contaminants do not detract from either the method according to the invention or its application, or from the AlSc material according to the invention.
Used as the primary material in an exemplary embodiment is an AlMgMnScZr alloy that consists mainly of aluminium along with added alloys of 4.3% w/w magnesium, 0.7% w/w scandium, 0.3% w/w zirconium and 0.5% w/w manganese, each relative to the overall weight of the alloy, wherein the percentage of contaminants like Fe, Si, Zn, etc. relative to the overall weight of the alloy lies under 0.5% w/w.
In an embodiment, the primary material is used as a particulate material, e.g., in the form of a powder, granules or in the form of flakes. In an embodiment, the primary material is introduced into the vacuum chamber as loose bulk. For example, the bulk density can lie between 5 and 40%, 10 and 30% or 15 and 20%. However, it is also possible to pre-compact the primary material to a density of up to 50%.
Used as the primary material in an embodiment is a rapidly solidified material, which was obtained via powder metallurgical rapid solidification processing (English: “rapid solidification processing”). The accelerated cooling makes it possible to dissolve considerably more scandium in the oversaturated mixed crystal than would be possible in a state of equilibrium. For example, the primary material can be cooled at cooling rates of 100 to 10⁹K/s, e.g., at cooling rates of 1000 to 10⁸K/s, of 10⁴to 10⁷K/s or 10⁵to 10⁶K/s. Suitable methods for manufacturing a rapidly solidified primary material include vaporization or atomization, the centrifuge molding method, splat cooling or the melt spinning process.
In a preferred embodiment, the primary material is fabricated via the melt spinning method. In this method, the melted alloy is cast onto a rapidly rotating, water-cooled metal cylinder through a ceramic nozzle. The intimate contact between the forming metal film and cylinder as well as the high thermal conductivity of the latter produce an extremely fast cooling rate. The metal film is lifted off before the metal cylinder has completed one full revolution, so that a continuous, thin strip forms. The cooling rate is correlated with the strip thickness, which in turn can be controlled by the rolling rate. For example, the strip thickness can lie between 0.01 and 1.00 mm. The strip thickness preferably measures less than 0.1 mm. The strip obtained in this way can be comminuted to manufacture a particulate material. For example, the primary material fabricated according to the melt spinning method can be further processed in the form of granules. The advantage to such granules fabricated according to the melt spinning method by comparison to a preliminary material in powder form, which poses a high explosive risk due to its large surface, is that it is significantly easier to handle without any special safety precautions. As a consequence, using a primary material fabricated according to the melt spinning method enables simplified and more efficient processing.
The primary material introduced into the vacuum chamber is degassed under a vacuum in step (b) of the method according to the invention and/or use according to the invention. During the degassing process, the primary material, whose surface can be contaminated with hydrogen, oxides as well as hydroxides and moisture, is treated in a vacuum, so as to remove these potentially present, undesired contaminants. Vacuum degassing is performed in a suitable, gastight container, also referred to as vacuum chamber or recipient, wherein the latter exhibits a gas outlet connected with a vacuum system by way of a valve.
In an embodiment of the present invention, vacuum degassing is performed under a vacuum of 0.1 to 10⁻⁸mbar. For example, the vacuum chamber can be controlled in such a way that the vacuum ranges from 8·10⁻²to 10⁻⁷mbar, 5·10⁻²to 10⁻⁶mbar, 2.5·10⁻²to 10⁻⁵mbar or 10⁻²to 10⁻⁴mbar.
In order to increase efficiency, the degassing process can be performed at an elevated temperature. In an exemplary embodiment, vacuum degassing can be performed at a temperature of 100 to 400° C., preferably at a temperature of 250 to 380° C. or 275 to 350° C., especially preferred at 290° C. However, it is also possible to perform vacuum degassing at other temperatures, for example at room temperature, i.e., at about 20° C.
For example, vacuum degassing can be performed over a period of 1 to 3000 min, 5 to 500 min or 10 to 100 min. In an exemplary embodiment, vacuum degassing in procedural step (b) and/or (d) is performed over a period of 15 min to 30 min.
In an exemplary embodiment of the present invention, vacuum degassing in procedural step (b) and/or (d) is performed under a vacuum of 0.05 mbar and at a temperature of 290° C. over a period of 15 to 30 min.
In the method according to the invention or its use, the vacuum degassing step (b) is interrupted by a step (c), in which the primary material is gassed with nitrogen. In an embodiment, the nitrogen is introduced into the vacuum chamber via the gas outlet to which the vacuum system is connected, wherein the gas outlet is provided with a valve suitable for this purpose, e.g., with a 3/2 way valve. However, the nitrogen can also be introduced into the vacuum chamber via a separate gas inlet. For example, depending on the vacuum chamber configuration, the nitrogen gas can be blown onto the surface of the primary material, or also be blown through the primary material from below.
In an embodiment, dry nitrogen is used to gas the primary material. This makes it possible to prevent the primary material from again becoming contaminated with hydrogen and water. For example, nitrogen containing less than 1000 ppm water is suitable, e.g., less than 500 ppm, less than 250 ppm, less than 100 ppm, less than 50 ppm or less than 5 ppm water.
For example, the primary material can be gassed with nitrogen over a period of 1 to 30 min, 2 to 20 min or 5 to 15 min. In an exemplary embodiment, the primary material is gassed with nitrogen over a period of 10 min. In another exemplary embodiment, the primary material is gassed with nitrogen for at least as long as it takes for atmospheric pressure to prevail in the vacuum chamber.
Steps (b) and (c) can be performed once or several times in succession. In an embodiment of the present invention, steps (b) and (c) are performed several times in succession, for example 1 to 10 times, 2 to 9 times, 3 to 8 times, 4 to 7 times, or 5 to 6 times. Steps (b) and (c) are preferably performed 5 times in succession.
Without being bound to a specific theory, it is assumed that the surface of the primary material is activated during vacuum degassing, which then enables the adsorption along with a chemical reaction between the nitrogen and AlSc alloy. As a result, scandium nitride phases that are thermally very stable seem to form. In the presence of elements that can enhance or replace the scandium, e.g., zirconium, it is also possible to form corresponding nitride phases with the latter, e.g., zirconium nitride phases in the presence of zirconium in the alloy.
In the method according to the invention, steps (b) and (c) are followed by a final vacuum degassing of the primary material as procedural step (d). Vacuum degassing is performed as described under step (b).
In an exemplary embodiment, the overall duration of procedural steps (b), (c) and (d) does not exceed 3000 min, 500 min, 300 min, 150 min or 100 min.
After final vacuum degassing, the primary material can be compacted. Compaction can take place mechanically or with a gas pressure. Examples of suitable mechanical compaction methods are cold pressing, isostatic pressing or vacuum pressing. One example of a suitable compaction method involving gas pressure is hot-isostatic pressing (HIP). Compaction can take place at atmospheric pressure or under a vacuum.
In an embodiment, the primary material is compacted in the vacuum chamber after the final degassing step (d). In an exemplary embodiment, the primary material is compacted via mechanical vacuum pressing in the vacuum chamber after the final degassing step (d).
For example, the compacted AlSc material can exhibit a density of greater than 80%, greater than 90%, greater than 95%, greater than 98% or greater than 99%. In a preferred embodiment, the density of the compacted AlSc material is greater than 95%.
After compaction, the obtained AlSc material can be formed to fabricate a semi-finished product and molded articles. Examples of suitable forming methods are extrusion or extrusion molding, rolling, forging, stretch forming, stamping, impact extrusion or deep drawing.
The AlSc material manufactured based on the method according to the invention or its application exhibits an improved extrusion moldability or extrudability. Due to its high temperature-loadability, the AlSc material according to the invention can be extrusion molded at higher temperatures, so that the flow resistance or forming resistance of the material diminishes, making the latter more readily deformable. Within the framework of the present invention, an “AlSc material with improved extrusion moldability” can preferably be further processed at a temperature greater than 320° C. via extrusion molding, without the tensile strength R_mof the material dropping significantly by comparison to the initial material at room temperature, i.e., at 20° C. For example, the AlSc material according to the invention exhibits a drop in tensile strength R_mof less than 5% relative to the initial material at room temperature after extrusion molded at about 350° C., and/or of less than 10% relative to the initial material at room temperature after extrusion molded at about 375° C.
In an exemplary embodiment, the compacted AlSc material is processed further via extrusion molding at 320 to 400° C., preferably at 340 to 375° C., or at about 350° C.
For example, the materials manufactured based on the method according to the invention or its application can be used to fabricate a welded, rolled, forged or extrusion molded or extruded component for an aircraft, ship or motor vehicle. In a preferred embodiment, the materials manufactured based on the method according to the invention or its application are used to fabricate an extrusion molded or extruded component for an aircraft, ship or motor vehicle.

Example

Used as the primary material was an AlMgScZr alloy consisting mainly of aluminium along with alloys of 4.3% w/w magnesium, 0.7% w/w scandium, 0.3% w/w zirconium and 0.5% w/w manganese, each relative to the overall weight of the alloy. The percentage of contaminants like Fe, Si, Zn, etc. relative to the overall weight of the alloy was under 0.5% w/w.
The AlMgScZr alloy was used in the form of granules fabricated according to the melt spinning method. The nominal strip thickness defining the achievable cooling rate in the melt spinning process measured 0.100 mm. Calculated from the latter is a maximum cooling rate (derived from the metallographically determined so-called dendrite arm spacing) of about 2·10⁵K/s.
The AlMgScZr primary material was used to fabricate a material A based on a manufacturing method for AlMgSc materials according to prior art (method A), and a material B based on the method according to the invention (method B). The two materials were processed further into rods via extrusion molding in the same way.

Method A (Comparative Example)

The primary material was placed in a recipient with a diameter of 31 mm as loose bulk with a height of 150 mm. The recipient exhibited a gas outlet that was connected to a vacuum system by way of a valve. Vacuum degassing was performed at 5·10⁻²mbar and a temperature of 290° C. over a period of 120 min.
After degassing, the primary material in the recipient was mechanically compacted into a bolt under a vacuum in a 200 t press at a temperature of 290° C. and pressing force of about 330 N/mm². The obtained bolt exhibited a density of about 99% and a height of 25 mm.

Method B

The primary material was placed in a recipient with a diameter of 31 mm as loose bulk with a height of 150 mm. The recipient exhibited a gas outlet that was connected to a vacuum system and a nitrogen source by way of a 3/2 way valve. Vacuum degassing was performed at 5·10⁻²mbar and a temperature of 290° C. over a period of 15 min. The primary material was then gassed by introducing dry nitrogen with a water content of less than 100 ppm into the recipient until atmospheric pressure prevailed in the vacuum chamber. The vacuum degassing step described above and subsequent nitrogen gassing were performed 5 times in all. This was followed by final vacuum degassing at 5·10⁻²mbar and a temperature of 290° C. The entire process took 300 min.
The primary material in the recipient was then mechanically compacted into a bolt under a vacuum in a 200 t press at a temperature of 290° C. and pressing force of about 330 N/mm². The obtained bolt exhibited a density of about 99% and a height of 25 mm.

Further Processing of Materials A and B

The bolts obtained according to methods A or B and cooled to room temperature were removed from the recipient and overtorqued to a diameter of 30 mm and length of 22 mm. The bolts were subsequently heated to about 320° C. in an extrusion molding device in a furnace, wherein the heating period and retention time came to 120 min in all. Extrusion molding took place with a 200 t press with a continuously rising extrusion rate, wherein the initial speed measured 250 mm/min, and the final speed measured 4000 mm/min. The pressed profile geometry was a rod with a diameter of 6 mm and length of about 500 mm. The press molding ratio measured 25:1.

Strength Test

A respective 3 round tensile specimens according to DIN 50125 were taken from the pressed rods, specifically from the beginning, middle and end regions of the respective rod. The results of the strength test are presented in Table 1.

TABLE 1

	Material A
Parameter	(comparative example)	Material B

Tensile strength R_m	Beginning: 580	Beginning: 578
(N/mm²)	Middle: 514	Middle: 588
	End: 432	End: 542
Yield strength R_p0.2	Beginning: 556	Beginning: 548
(N/mm²)	Middle: 452	Middle: 571
	End: 406	End: 541

As demonstrated by the results of the strength test, the strength of material B is largely constant. As the pressing rate increases accompanied by an added (adiabatic) heat of material deformation, the strength of the material B manufactured in the method according to the invention remains intact for a long time, and only tapers slightly near the end of the extrudate (by about 6%). By contrast, the strength falls off sharply toward the end of the rod in the material A manufactured using the method according to prior art. The loss in strength for material A already exceeds 11% in the middle of the extrudate, and even exceeds 25% at the end of the extrudate.
As a consequence, the method according to the invention and/or its use enables the manufacture of aluminium materials alloyed with scandium, which exhibit a constant, high material strength even at high forming rates (extrusion molding rates). In addition, the AlMgSc material modified according to the invention can be extrusion molded at higher temperatures than in prior art, without suffering the large losses in strength described above in the process.
Additional exemplary embodiments or aspects of the present invention are described in the following:
1. Method for manufacturing a high temperature-loadable aluminium material alloyed with scandium, encompassing the following steps:

a) Introducing a primary material comprising an alloy encompassing the metals aluminium and scandium into a vacuum chamber,
b) Vacuum degassing the primary material,
c) Gassing the primary material with nitrogen, and
d) Subjecting the primary material to final vacuum degassing.

2. Method according to aspect 1, wherein the primary material was fabricated according to the melt spinning process.
3. Method according to aspect 1 or 2, wherein the primary material is present as granules.
4. Method according to one of the preceding aspects, wherein the alloy additionally contains magnesium.
5. Method according to one of the preceding aspects, wherein the alloy additionally encompasses at least one other, optional metal selected from the group comprised of Zr, Ti, Y, Hf, Ta, La, Ce, Tb, Nd, Eu, Gd, Dy, Ho and Er and/or additionally encompasses at least one other, optional element selected from the group comprised of Zn, Mn, Ag, Li, Cu, Si or Ca.
6. Method according to one of the preceding aspects, wherein vacuum degassing is performed according to step (b) and/or (d) under a vacuum of 0.1 to 10⁻⁸mbar.
7. Method according to one of the preceding aspects, wherein vacuum degassing is performed according to step (b) and/or (d) at a temperature of 275 to 400° C.
8. Method according to one of the preceding aspects, wherein vacuum degassing is performed according to step (b) and/or (d) over a period of 15 min to 30 min.
9. Method according to one of the preceding aspects, wherein steps (b) and (c) are performed 1 to 10 times in succession.
10. Method according to one of the preceding aspects, wherein the method encompasses another, additional step (e) in which the primary material is compacted in the vacuum chamber immediately after step (d).
11. High temperature-loadable aluminium material alloyed with scandium, which can be obtained in the method encompassing the following steps:

12. Use of a material according to aspect 11 for manufacturing a welded, rolled, extrusion molded or forged component for an aircraft, ship or motor vehicle.
13. Welded, rolled, extrusion welded or forged component for an aircraft, ship or motor vehicle consisting of a material according to aspect 11.

Claims

1. A method for producing a high temperature-loadable alloy comprising the steps of:

a) introducing a primary material comprising an alloy of aluminium and scandium into a vacuum chamber;

b) vacuum degassing the primary material;

c) gassing the primary material with nitrogen; and

d) subjecting the primary material to final vacuum degassing;

for producing a high temperature-loadable aluminium material alloyed with scandium.

2. The method according to claim 1, wherein the resulting high temperature-loadable aluminium material alloyed with scandium exhibits improved extrusion moldability.

3. The method according to claim 1, wherein the primary material was procuded via the melt spinning method.

4. The method according to claim 1, wherein the primary material is present in the form of granules.

5. The method according to claim 1, wherein the alloy additionally contains magnesium.

6. The method according to claim 1, wherein the alloy additionally comprises at least one other element selected from the group consisting of Zr, Ti, Y, Hf, Ta, La, Ce, Tb, Nd, Eu, Gd, Dy, Ho, Zn, Mn, Ag, Li, Cu, Si and Ca and mixtures thereof.

7. The method according to claim 1, wherein vacuum degassing according to step (b) and/or (d) is performed using a vacuum of 0.1 to 10⁻⁸mbar.

8. The method according to claim 1, wherein vacuum degassing according to step (b) and/or (d) is performed at a temperature of 275 to 400° C.

9. The method according to claim 1, wherein vacuum degassing according to step (b) and/or (d) is performed over a period of 15 min to 30 min.

10. The method according to claim 1 wherein steps (b) and (c) are performed a plurality of times in succession.

11. The method according to claim 1, wherein the method encompasses another, additional step (e) in which the primary material is compacted in the vacuum chamber immediately after step (d).

12. Method for producing a high temperature-loadable aluminium material alloyed with scandium comprising the following steps:

a) introducing a primary material comprising an alloy of aluminium and scandium into a vacuum chamber, wherein the primary material was fabricated according to the melt spinning process;

b) vacuum degassing the primary material;

c) gassing the primary material with nitrogen; and

d) subjecting the primary material to a final vacuum degassing.

13. High temperature loadable aluminium material alloyed with scandium, obtained in the method comprising the following steps:

b) vacuum degassing the primary material;

c) gassing the primary material with nitrogen; and

d) subjecting the primary material to final vacuum degassing.

14. The method according to claim 13 comprising using the high temperature loadable aluminium material to produce a welded, rolled, extrusion molded or forged component for an aircraft, ship or motor vehicle.

15. A welded, rolled, extrusion molded or forged component for an aircraft, ship or motor vehicle, comprising a material according to claim 13.