EP2598664B1 - High temperature scandium-containing aluminium alloy with improved extrudability - Google Patents
High temperature scandium-containing aluminium alloy with improved extrudability Download PDFInfo
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- EP2598664B1 EP2598664B1 EP11761484.2A EP11761484A EP2598664B1 EP 2598664 B1 EP2598664 B1 EP 2598664B1 EP 11761484 A EP11761484 A EP 11761484A EP 2598664 B1 EP2598664 B1 EP 2598664B1
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- Prior art keywords
- weight
- scandium
- primary material
- alloy
- vacuum
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- 229910052706 scandium Inorganic materials 0.000 title claims description 53
- SIXSYDAISGFNSX-UHFFFAOYSA-N scandium atom Chemical compound [Sc] SIXSYDAISGFNSX-UHFFFAOYSA-N 0.000 title claims description 52
- 229910000838 Al alloy Inorganic materials 0.000 title description 3
- 239000000463 material Substances 0.000 claims description 112
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 65
- 238000000034 method Methods 0.000 claims description 65
- 239000000956 alloy Substances 0.000 claims description 64
- 229910045601 alloy Inorganic materials 0.000 claims description 63
- 229910052782 aluminium Inorganic materials 0.000 claims description 54
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 53
- 229910052757 nitrogen Inorganic materials 0.000 claims description 32
- 238000009849 vacuum degassing Methods 0.000 claims description 26
- 238000001125 extrusion Methods 0.000 claims description 19
- 238000004519 manufacturing process Methods 0.000 claims description 17
- 229910052749 magnesium Inorganic materials 0.000 claims description 15
- 239000011777 magnesium Substances 0.000 claims description 15
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 claims description 14
- 239000004411 aluminium Substances 0.000 claims description 14
- 238000002074 melt spinning Methods 0.000 claims description 13
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 13
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 claims description 10
- 239000008187 granular material Substances 0.000 claims description 6
- 239000000356 contaminant Substances 0.000 claims description 5
- 229910052845 zircon Inorganic materials 0.000 claims description 4
- GFQYVLUOOAAOGM-UHFFFAOYSA-N zirconium(iv) silicate Chemical compound [Zr+4].[O-][Si]([O-])([O-])[O-] GFQYVLUOOAAOGM-UHFFFAOYSA-N 0.000 claims description 4
- 239000007858 starting material Substances 0.000 description 65
- 239000007789 gas Substances 0.000 description 15
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 description 14
- 229910052751 metal Inorganic materials 0.000 description 14
- 239000002184 metal Substances 0.000 description 14
- 229910052726 zirconium Inorganic materials 0.000 description 14
- 239000012535 impurity Substances 0.000 description 11
- 150000002739 metals Chemical class 0.000 description 10
- 238000001816 cooling Methods 0.000 description 9
- 238000010438 heat treatment Methods 0.000 description 7
- 239000002243 precursor Substances 0.000 description 7
- 238000003825 pressing Methods 0.000 description 7
- 238000007906 compression Methods 0.000 description 5
- 238000007872 degassing Methods 0.000 description 5
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 4
- 230000006835 compression Effects 0.000 description 4
- 239000011265 semifinished product Substances 0.000 description 4
- 238000005260 corrosion Methods 0.000 description 3
- 230000007797 corrosion Effects 0.000 description 3
- 229910052742 iron Inorganic materials 0.000 description 3
- 229910052748 manganese Inorganic materials 0.000 description 3
- 239000011572 manganese Substances 0.000 description 3
- 229910052710 silicon Inorganic materials 0.000 description 3
- MCMNRKCIXSYSNV-UHFFFAOYSA-N Zirconium dioxide Chemical compound O=[Zr]=O MCMNRKCIXSYSNV-UHFFFAOYSA-N 0.000 description 2
- 230000032683 aging Effects 0.000 description 2
- 238000005275 alloying Methods 0.000 description 2
- 238000000889 atomisation Methods 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 238000005242 forging Methods 0.000 description 2
- 238000002309 gasification Methods 0.000 description 2
- 239000011236 particulate material Substances 0.000 description 2
- 239000000843 powder Substances 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 238000002360 preparation method Methods 0.000 description 2
- 238000007712 rapid solidification Methods 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 229910052725 zinc Inorganic materials 0.000 description 2
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- -1 Zirconium Chemical compound 0.000 description 1
- 230000004913 activation Effects 0.000 description 1
- 239000000654 additive Substances 0.000 description 1
- 230000000996 additive effect Effects 0.000 description 1
- 238000005273 aeration Methods 0.000 description 1
- 229910052783 alkali metal Inorganic materials 0.000 description 1
- 150000001340 alkali metals Chemical class 0.000 description 1
- SNAAJJQQZSMGQD-UHFFFAOYSA-N aluminum magnesium Chemical compound [Mg].[Al] SNAAJJQQZSMGQD-UHFFFAOYSA-N 0.000 description 1
- CUOITRGULIVMPC-UHFFFAOYSA-N azanylidynescandium Chemical compound [Sc]#N CUOITRGULIVMPC-UHFFFAOYSA-N 0.000 description 1
- 229910052790 beryllium Inorganic materials 0.000 description 1
- 239000000919 ceramic Substances 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 230000001427 coherent effect Effects 0.000 description 1
- 238000005056 compaction Methods 0.000 description 1
- 238000011109 contamination Methods 0.000 description 1
- 210000001787 dendrite Anatomy 0.000 description 1
- 230000001419 dependent effect Effects 0.000 description 1
- 229910001873 dinitrogen Inorganic materials 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 230000029142 excretion Effects 0.000 description 1
- 238000004880 explosion Methods 0.000 description 1
- 239000002360 explosive Substances 0.000 description 1
- 238000001513 hot isostatic pressing Methods 0.000 description 1
- 239000001257 hydrogen Substances 0.000 description 1
- 229910052739 hydrogen Inorganic materials 0.000 description 1
- 150000004679 hydroxides Chemical class 0.000 description 1
- 238000011065 in-situ storage Methods 0.000 description 1
- 229910052738 indium Inorganic materials 0.000 description 1
- 238000002347 injection Methods 0.000 description 1
- 239000007924 injection Substances 0.000 description 1
- 238000010409 ironing Methods 0.000 description 1
- 238000000462 isostatic pressing Methods 0.000 description 1
- 229910001092 metal group alloy Inorganic materials 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 238000005088 metallography Methods 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- QJGQUHMNIGDVPM-UHFFFAOYSA-N nitrogen group Chemical group [N] QJGQUHMNIGDVPM-UHFFFAOYSA-N 0.000 description 1
- 238000004663 powder metallurgy Methods 0.000 description 1
- 238000004881 precipitation hardening Methods 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 230000002787 reinforcement Effects 0.000 description 1
- 230000003014 reinforcing effect Effects 0.000 description 1
- 230000000717 retained effect Effects 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 238000001179 sorption measurement Methods 0.000 description 1
- 238000007782 splat cooling Methods 0.000 description 1
- 230000001502 supplementing effect Effects 0.000 description 1
- ZVWKZXLXHLZXLS-UHFFFAOYSA-N zirconium nitride Chemical compound [Zr]#N ZVWKZXLXHLZXLS-UHFFFAOYSA-N 0.000 description 1
Classifications
-
- 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
- C22C1/00—Making non-ferrous alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/04—Making non-ferrous alloys by powder metallurgy
- C22C1/0408—Light metal alloys
- C22C1/0416—Aluminium-based alloys
-
- 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
- C22F1/02—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working in inert or controlled atmosphere or vacuum
-
- 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
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2201/00—Treatment under specific atmosphere
- B22F2201/20—Use of vacuum
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/12—Both compacting and sintering
- B22F3/14—Both compacting and sintering simultaneously
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/12—All metal or with adjacent metals
- Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
- Y10T428/12736—Al-base component
Definitions
- the invention relates to a high-temperature scandium alloyed aluminum material, a process for its preparation and the use of a process for its preparation.
- the object of the present invention is to provide a method for producing a scandium alloyed aluminum material and the use of such a method, whereby the high temperature load capacity of this material is improved. It is further desirable to provide a method for producing a scandium-alloyed aluminum material and the use of such a method that makes it possible to reduce the amount of scandium used.
- Another object of the present invention is to provide a scandium-alloyed aluminum material and a method of making the same, the scandium-alloyed aluminum material having improved strength and thermal stability.
- a use of a method comprising the steps of: (a) introducing a precursor comprising an alloy comprising the metals aluminum and scandium into a vacuum chamber, said precursor being an AlMgMnScZr alloy consisting of 4.3 wt% Magnesium, 0.7% by weight scandium, 0.3% by weight zirconium and 0.5% by weight manganese, in each case based on the total weight of the alloy, the proportion of impurities in the total weight of the alloy being below 0.5% by weight, the rest is aluminum, (b) vacuum gases of the starting material at a vacuum of 0.1 to 10 -8 mbar and a temperature of 275 to 400 ° C over a period of 15 to 30 minutes, (c) gassing the starting material with nitrogen a duration of 1 to 30 minutes, where the nitrogen contains a water content of less than 1000 ppm, and (d) final vacuum degassing of the raw material at a vacuum of 0.1 to 10 -8 mbar and a temperature of
- a method of making a high temperature scandium alloyed aluminum material comprising the steps of: (a) introducing a precursor material comprising an alloy comprising the metals aluminum and scandium into a vacuum chamber, the precursor material comprising an AlMgMnScZr; Alloy consisting of 4.3 wt .-% magnesium, 0.7 wt .-% scandium, 0.3 wt .-% zirconium and 0.5 wt .-% manganese, each based on the total weight of the alloy, wherein the proportion of impurities in the total weight of the Alloy below 0.5 wt .-%, the rest is aluminum, wherein the starting material (b) vacuum gases of the starting material at a vacuum of 0.1 to 10 -8 mbar and a temperature of 275 to 400 ° C over a period of 15 to 30 minutes, (c) gasification of the starting material with nitrogen for a period of 1 to 30 minutes, the nitrogen having a water content
- a high temperature scannable aluminum alloy material obtainable by a process comprising the steps of: (a) incorporating a primary material comprising an alloy comprising the metals aluminum and scandium in a vacuum chamber, wherein the starting material is an AlMgMnScZr alloy consisting of 4.3 wt .-% magnesium, 0.7 wt .-% scandium, 0.3 wt .-% zirconium and 0.5 wt .-% manganese, each based on the total weight of the alloy, wherein the proportion of impurities in the total weight of the alloy is less than 0.5 wt .-%, the balance is aluminum, wherein the starting material was prepared by the melt spinning method, (b) vacuum gases of the starting material at a vacuum of 0.1 to 10 -8 mbar and a temperature of 275 to 400 ° C over a period of 15 to 30 minutes, (c) gassing the starting material with nitrogen over a period of 1 to 30 minutes, the starting material was prepared by the melt spinning method,
- the inventive method and / or its use allows the production of AlSc materials, which have a larger processing window for the production of semi-finished products.
- the materials produced by the process according to the invention and / or its use can be processed at higher temperatures, faster extrusion rates and higher injection ratios. This is for example advantageous for the production of semi-finished products by means of the extrusion process.
- the invention enables the production of lightweight and corrosion-resistant AlSc materials with very high heat resistance. These materials according to the invention have a high toughness and damage tolerance and allow cost-effective process leading.
- the inventive method and its use has the advantage that the reinforcement takes place "in situ" and, for example, no nanoscale reinforcing phase powder must be used, which are difficult to process and explosive.
- an "aluminum material” is understood to mean a metallic material which consists essentially of aluminum and may be alloyed with other metals.
- a "high-temperature-loadable AlSc material” is an aluminum material alloyed with scandium and, if appropriate, even further metals, whose structure or microstructure is at a Temperature load of more than 350 ° C remains largely stable, ie the grain size and the amount of precipitates, as well as their size and distribution remains largely constant, so that the material has similar strength properties at room temperature as before the temperature.
- a "high-temperature-resistant AlSc material” in the context of the present invention preferably exhibits a drop in tensile strength R m of less than 5% and / or after a temperature of 375 ° C. after a temperature exposure of 350 ° C. to the starting material at room temperature the starting material at room temperature, a drop in the tensile strength R m of less than 10%.
- a use of a method for producing a high-temperature scandium-alloyed aluminum material described here comprises the following method steps: (a) introducing a starting material comprising an alloy comprising the metals Al and Sc into a vacuum chamber (b) vacuum gases of the starting material, (c) Gassing the primary material with nitrogen, (d) final vacuum degassing of the primary material, and (e) compacting the primary material immediately following step (d) in the vacuum chamber.
- the primary material used in the process comprises an alloy comprising the metals aluminum and scandium.
- the amount of scandium in the alloy is 0.7% by weight based on the total mass of the alloy.
- the alloy additionally includes Zr, which has properties similar to scandium in aluminum materials. This element can behave additively with the scandium, ie it can be forcibly dissolved with the scandium in the aluminum material and thus allow an increase in solidification by precipitation hardening.
- the Al 3 Sc phase is modified by replacing part of the scandium with Zr.
- the alloy used as the starting material in the present invention additionally comprises, in addition to aluminum and scandium, zirconium in an amount of 0.3% by weight.
- zirconia alters the precipitated Al 3 Sc phase to Al 3 Sc 1 -x Zr x without losing its strength-increasing effect.
- zirconium additive For example, the minimum cooling rate that must be maintained to produce a scandium and zirconium supersaturated solid solution can be reduced. The aging and thus the decline in the hardenability is slowed down. This allows the AlScZr alloy to withstand a certain temperature for an extended period of time before it begins to over age. At the same time, the use of zircon allows some reduction in the amount of scandium in the alloy, which is a relatively expensive alloying element due to its rarity.
- the alloy comprises Mg and Mn.
- the properties of the material produced from the starting material can be specifically influenced.
- the addition of magnesium and manganese increases the strength of the aluminum material and thus enables the production of particularly hard materials.
- the starting material comprises an alloy comprising the metals aluminum, magnesium, manganese, scandium and zirconium.
- impurities are usually always included.
- impurities are elements such as e.g. Alkali metals, Fe, Si, Be or In. These impurities may each be present in an amount of up to about 0.5% by weight, and in total in an amount of up to 2% by weight, based in each case on the total mass of the alloy.
- impurities do not affect either the process of the invention or its use, or the AlSc material according to the invention.
- an AlMgMnScZr alloy is used as a starting material, which consists mainly of aluminum and alloys of 4.3 wt .-% magnesium, 0.7 wt .-% scandium, 0.3 wt .-% zirconium and 0 , 5 wt .-% manganese, each based on the total weight of the alloy, wherein the proportion of impurities such as Fe, Si, Zn, etc., the total weight of the alloy is below 0.5 wt .-%.
- the starting material is used as a particulate material, for example in the form of a powder, a granulate or in the form of flakes.
- the starting material is introduced as a loose bed in the vacuum chamber.
- the bulk density may for example be between 5 and 40%, 10 and 30% or 15 and 20%. However, it is also possible to precompact the starting material to a density of up to 50%.
- the starting material used is a rapidly solidified material which has been obtained by means of a powder metallurgy rapid solidification processing ("rapid solidification processing").
- the accelerated cooling makes it possible to dissolve considerably more scandium in the supersaturated solid solution than would be possible in the equilibrium state.
- the cooling of the starting material at cooling rates of 100 to 10 9 K / s carried out, for example, at cooling rates of 1000 to 10 8 K / s, from 10 4 to 10 7 K / s or from 10 5 to 10 6 K / s.
- Suitable processes for the production of a rapidly solidified starting material are, for example, atomization or atomization, the centrifugal mold process, splat cooling or the melt spinning process.
- the starting material is produced by means of the melt spinning process.
- the molten alloy is poured through a ceramic die onto a rapidly rotating, water-cooled metal cylinder.
- the intimate contact between the forming metal film and the cylinder and its high thermal conductivity cause an extremely rapid cooling.
- the metal film is lifted so that forms a continuous thin band.
- the cooling rate correlates with the strip thickness, which in turn can be controlled by the roll speed.
- the strip thickness can be, for example, between 0.01 and 1.00 mm.
- the strip thickness is less than 0.1 mm.
- the strip thus obtained can be comminuted to produce a particulate material.
- the starting material produced by the melt spinning process can be further processed, for example in the form of granules.
- a granulate produced by the melt spinning method has the advantage that it can be handled much easier and without special safety precautions compared to a powdery starting material, which poses a high risk of explosion due to its large surface area.
- the use of a starting material produced by the melt spinning process allows a simplified and more efficient process management.
- the introduced into the vacuum chamber precursor is degassed according to step (b) of the method according to the invention and / or the use according to the invention in a vacuum.
- the starting material the surface of which may be contaminated with hydrogen, oxides and hydroxides and moisture, is treated in a vacuum so as to remove any such undesired contaminants.
- the vacuum degassing is carried out in a suitable gastight container, also called vacuum chamber or recipient, wherein this one Gas outlet which is connected via a valve with a vacuum system.
- the vacuum degassing is carried out at a vacuum of 0.1 to 10 -8 mbar.
- the vacuum chamber can be controlled so that the vacuum in a range of 8-10 -2 to 10 -7 mbar, 5.10 -2 to 10 -6 mbar, 2.5 ⁇ 10 -2 to 10 -5 mbar or 10 - 2 to 10 -4 mbar.
- the degassing process is carried out to increase the efficiency at an elevated temperature of 275 to 400 ° C, preferably at a temperature of 275 to 380 ° C or 275 to 350 ° C, more preferably at 290 ° C.
- the vacuum degassing is carried out according to process steps (b) and (d) over a period of 15 minutes to 30 minutes.
- the vacuum degassing according to process step (b) and / or (d) is at a vacuum of 0.05 mbar and a temperature of 290 ° C over a period of 15 to 30 minutes.
- the vacuum degassing step (b) is interrupted by a step (c) in which the starting material is sparged with nitrogen.
- the nitrogen is introduced into the vacuum chamber via the gas outlet to which the vacuum system is connected, the gas outlet being provided with a valve suitable for this purpose, e.g. with a 3/2-way valve.
- the nitrogen gas can be inflated, for example, on the surface of the starting material or blown from below through the starting material.
- Suitable is nitrogen containing less than 1000 ppm water, e.g. less than 500 ppm, less than 250 ppm, less than 100 ppm, less than 50 ppm, or less than 5 ppm of water.
- the gassing of the starting material with nitrogen takes place over a period of 1 to 30 minutes, 2 to 20 minutes or 5 to 15 minutes. According to an exemplary embodiment, the gasification of the starting material takes place with nitrogen over a period of 10 min. According to another exemplary embodiment, the starting material is at least as long gassed with nitrogen until there is atmospheric pressure in the vacuum chamber.
- Steps (b) and (c) may be performed one or more times in succession. According to one 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. Preferably, steps (b) and (c) are performed 5 times in succession.
- a final vacuum degassing of the starting material takes place as process step (d).
- the vacuum degassing is carried out as described under step (b).
- the total duration of process steps (b), (c) and (d) is not more than 3000 min, 500 min, 300 min, 150 min or 100 min.
- the starting material is compacted.
- the compression can be done mechanically or by gas pressure.
- suitable mechanical compression methods are cold pressing, isostatic pressing or vacuum pressing.
- An example of a suitable gas pressure compression process is hot isostatic pressing (HIP).
- HIP hot isostatic pressing
- the compression can be done at atmospheric pressure or under vacuum.
- the starting material is compressed in the vacuum chamber following the final degassing step (d).
- the precursor material is compacted after the final degassing step (d) by means of mechanical vacuum pressing in the vacuum chamber.
- the densified AlSc material may have a density greater than 80%, greater than 90%, greater than 95%, greater than 98%, or greater than 99%. According to a preferred embodiment, the density of the densified AlSc material is greater than 95%.
- the resulting AlSc material can be transformed to produce semi-finished products and molded parts.
- suitable forming processes are extruding or extrusion, rolling, forging, ironing, stamping, extrusion or deep drawing.
- the AlSc material produced by the method according to the invention or its use has improved extrudability or extrudability. Due to its high temperature resistance, the extrusion of the AlSc material according to the invention can be carried out at higher temperatures, whereby the flow resistance or deformation resistance of the material decreases and this is better deformed.
- An "AlSc material with improved extrudability" in the context of the present invention may preferably be further processed at a temperature of more than 320 ° C by means of extrusion without the tensile strength R m of the material compared to the starting material at room temperature, ie at 20 ° C, falls significantly.
- the AlSc material according to the invention after being extruded at about 350 ° C.
- the compacted AlSc material is further processed by extrusion at 320 to 400 ° C, preferably at 340 to 375 ° C or at about 350 ° C.
- the materials produced by the method or its use according to the invention can be used, for example, for producing a welded, rolled, forged or extruded or extruded component for an aircraft, a sea-going vehicle or a motor vehicle. According to a preferred embodiment, the materials produced by the method according to the invention or its use are used for producing an extruded or extruded component for an aircraft, a sea-going vehicle or a motor vehicle.
- the starting material used was an AlMgScZr alloy, which consisted mainly of aluminum and alloys of 4.3% by weight of magnesium, 0.7% by weight of scandium, 0.3% by weight of zirconium and 0.5% by weight. -% manganese is, in each case based on the total weight of the alloy.
- the content of impurities such as Fe, Si, Zn, etc. in the total weight of the alloy was below 0.5 wt%.
- the AlMgScZr alloy was used in the form of granules prepared by the melt spinning method.
- the nominal strip thickness, which defines the achievable cooling rate during the melt spinning process, was 0.100 mm. From this, a maximum cooling rate (derived from the so-called dendrite arm spacing, which was determined by metallography) of about 2 ⁇ 10 5 K / s is calculated.
- a material A was produced from the AlMgScZr starting material by a production process for AlMgSc materials according to the prior art (process A) and a material B by the process according to the invention (process B). The further processing of the two materials to round bars by extrusion was the same.
- the starting material was placed in a recipient with a diameter of 31 mm as a loose bed with a height of 150 mm.
- the recipient had a gas outlet, which was connected via a valve to a vacuum system.
- the vacuum degassing was carried out at 5 ⁇ 10 -2 mbar and a temperature of 290 ° C. over a period of 120 minutes.
- the starting material in the recipient was mechanically compacted into a bolt under vacuum in a 200 t press at a temperature of 290 ° C. and a pressing force of about 330 N / mm 2 .
- the obtained stud had a density of about 99% and a height of 25 mm.
- the starting material was placed in a recipient with a diameter of 31 mm as a loose bed with a height of 150 mm.
- the recipient had a gas outlet connected to a vacuum system and a nitrogen source via a 3/2-way valve.
- the vacuum degassing was at 5 ⁇ 10 -2 mbar and a temperature of 290 ° C over a period of 15 min performed.
- dry nitrogen having a water content of less than 100 ppm was introduced into the recipient until atmospheric pressure prevailed in the vacuum chamber.
- the vacuum degassing step described above and the subsequent sparging with nitrogen were carried out a total of 5 times. This was followed by a final vacuum degassing at 5 ⁇ 10 -2 mbar and a temperature of 290 ° C.
- the total duration of the process was 300 min.
- the starting material in the recipient was mechanically compacted into a bolt under vacuum in a 200 t press at a temperature of 290 ° C. and a pressing force of about 330 N / mm 2 .
- the obtained stud had a density of about 99% and a height of 25 mm.
- the obtained according to methods A and B and cooled to room temperature bolts were removed from the recipient and overdriven to a diameter of 30 mm and a length of 22 mm. Subsequently, the bolts were heated in an extrusion device in the oven to about 320 ° C, wherein heating time and holding time totaled 120 min.
- the extrusion was carried out with a 200 t press with a continuously increasing extrusion speed, the initial speed was 250 mm / min and the final speed 4000 mm / min.
- the pressed profile geometry was a round bar with a Diameter of 6 mm and a length of about 500 mm.
- the compression ratio was 25: 1.
- the results of the strength test show that the strength of the material B is largely constant. With increasing pressing speed, and the concomitant additional (adiabatic) material deformation heating, the strength of the material B produced by the process according to the invention is retained for a long time and drops slightly towards the end of the strand (by about 6%). On the other hand, in the material A produced by the method of the prior art, the strength at the end of the rod greatly drops. The loss of strength of the material A is already more than 11% in the strand center and even more than 25% at the strand end.
- the inventive method and / or its use thus enables the production of scandium-alloyed aluminum materials, which have a consistently high material strength even at high deformation rates (extrusion rates).
- the modified AlMgSc material according to the invention can be extruded at higher temperatures than the prior art without suffering the above-described large strength losses.
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Description
Die Erfindung betrifft einen hochtemperaturbelastbaren, mit Scandium legierten Aluminium-Werkstoff, ein Verfahren zu seiner Herstellung sowie die Verwendung eines Verfahrens zu seiner Herstellung.The invention relates to a high-temperature scandium alloyed aluminum material, a process for its preparation and the use of a process for its preparation.
Sowohl in der Luftfahrt als auch in der Fahrzeugtechnik werden spezielle Legierungen benötigt, um Halbzeuge und Bauteile mit hoher Festigkeit sowie Duktilität herzustellen. Daneben spielt das Gewicht und die Korrosionsbeständigkeit eine wichtige Rolle.In aerospace and automotive engineering, special alloys are needed to produce high strength, ductile, and semi-finished products. In addition, the weight and corrosion resistance plays an important role.
In den vergangenen vier Jahrzehnten ist die Herstellung von höherfesten mit Scandium legierten Aluminium-Werkstoffen in verschiedenen Halbzeugformen, wie z.B. Bleche, Profile, Schmiedeteile oder Guss, vielfach beschrieben worden. Diese Werkstoffe weisen eine hohe Festigkeit, eine hohe metallurgische Stabilität und einen sehr guten Korrosionswiderstand auf. Der verbesserten Festigkeit dieser Werkstoffe liegt die Ausscheidung von kohärenten Al3Sc-Phasen zu Grunde, die mittels definierter Wärmebehandlung gezielt erzeugt werden können.Over the past four decades, the production of high-strength aluminum materials scandium-alloyed in various semi-finished shapes, such as sheets, profiles, forgings or cast has been widely described. These materials have a high strength, a high metallurgical stability and a very good corrosion resistance. The improved strength of these materials is based on the excretion of coherent Al 3 Sc phases, which can be specifically produced by means of a defined heat treatment.
Mit Scandium legierte Aluminium-Magnesium-Werkstoffe sind beispielsweise aus
Mit Scandium legierte Aluminium-Werkstoffe weisen allerdings oft keine ausreichend hohe, dauerhafte Festigkeit bei erhöhten Temperaturen auf. Es ist beispielsweise bekannt, dass das Strangpressen von AlMgSc-Legierungen bei relativ niedrigen Temperaturen zwischen 300 und 350°C stattfinden muss, da ansonsten die hohe Temperatur des Pressbolzens zur ungewollten Entfestigen des AlMgSc-Materials infolge von Alterung der Al3Sc-Ausscheidungen führt. Bei diesen Temperaturen ist jedoch der Umformungswiderstand dieser Legierung deutlich erhöht, so dass nur mit einer verringerten Pressgeschwindigkeit gearbeitet werden kann. Diese Problematik wird zusätzlich verstärkt durch die Erwärmung des stranggepressten AlMgSc-Werkstoffs während des Umformungsvorgangs innerhalb der Strangpressmatrize. Dieser als adiabatische Erwärmung bekannte Prozess läuft zwangsläufig während des Strangpressens von Aluminium-Werkstoffen ab und führt zu einer weiteren Erwärmung des AlMgSc-Materials, so dass trotz einer definierten Erwärmung des Pressbolzens auf 350°C in der Legierung auf Grund der Umformarbeit kurzfristig 400°C oder bei großer Pressgeschwindigkeit sogar 450°C erreicht werden. Werkstofftechnisch betrachtet, ist das Ergebnis einer zusätzlichen Wärmezufuhr gleichzusetzen mit einer deutlichen Überalterung und einer damit einhergehenden Entfestigung der Legierung. Ein solches entfestigtes Material zeigt beispielsweise eine deutlich verringerte Zugfestigkeit.However, aluminum materials alloyed with scandium often do not have sufficiently high permanent strength at elevated temperatures. It is known, for example, that the extrusion of AlMgSc alloys must take place at relatively low temperatures between 300 and 350 ° C, otherwise the high temperature of the billet will result in unwanted softening of the AlMgSc material due to aging of the Al 3 Sc precipitates. At these temperatures, however, the deformation resistance of this alloy is significantly increased, so that you can only work with a reduced press speed. This problem is further intensified by the heating of the extruded AlMgSc material during the forming process within the extrusion die. This process known as adiabatic heating inevitably takes place during the extrusion of aluminum materials and leads to a further heating of the AlMgSc material, so that in spite of a defined heating of the billet to 350 ° C in the alloy due to the forming work in the short term 400 ° C. or 450 ° C can be achieved at high pressing speed. Considered from a material point of view, the result of an additional heat supply is equivalent to a marked overaging and concomitant softening of the alloy. Such a softened material shows, for example, a significantly reduced tensile strength.
Es besteht somit Bedarf an einem Aluminium-Werkstoff, der diese Nachteile nicht aufweist.There is thus a need for an aluminum material which does not have these disadvantages.
Aufgabe der vorliegenden Erfindung besteht darin, ein Verfahren zur Herstellung eines mit Scandium legierten Aluminium-Werkstoffs sowie die Verwendung eines solchen Verfahrens bereitzustellen, wodurch die Hochtemperaturbelastbarkeit dieses Werkstoffs verbessert wird. Es ist ferner wünschenswert, ein Verfahren zur Herstellung eines mit Scandium legierten Aluminium-Werkstoffs sowie die Verwendung eines solchen Verfahrens bereitzustellen, das es ermöglicht, die Menge an eingesetztem Scandium zu verringern.The object of the present invention is to provide a method for producing a scandium alloyed aluminum material and the use of such a method, whereby the high temperature load capacity of this material is improved. It is further desirable to provide a method for producing a scandium-alloyed aluminum material and the use of such a method that makes it possible to reduce the amount of scandium used.
Eine weitere Aufgabe der vorliegenden Erfindung ist es, einen mit Scandium legierten Aluminium-Werkstoff sowie ein Verfahren zu seiner Herstellung bereitzustellen, wobei der mit Scandium legierten Aluminium-Werkstoff eine verbesserte Festigkeit und eine verbesserte thermische Stabilität aufweist. Darüber hinaus ist es wünschenswert, einen mit Scandium legierten Aluminium-Werkstoff bereitzustellen, der bei hohen Temperaturen umgeformt werden kann, ohne dass eine Entfestigung der Legierung auftritt. Des Weiteren ist es wünschenswert, dass der mit Scandium legierten Aluminium-Werkstoff eine verbesserte Strangpressbarkeit aufweist und mit hohen Pressgeschwindigkeiten verarbeitet werden kann.Another object of the present invention is to provide a scandium-alloyed aluminum material and a method of making the same, the scandium-alloyed aluminum material having improved strength and thermal stability. In addition, it is desirable to provide a scandium-alloyed aluminum material that can be reshaped at high temperatures without causing the alloy to soften. Furthermore, it is desirable that the scandium alloyed aluminum material have improved extrudability and can be processed at high press speeds.
Eine erfindungsgemäße Lösung wird in den unabhängigen Ansprüchen wiedergegeben. Bevorzugte Ausführungsformen ergeben sich durch Kombination mit den Merkmalen der Unteransprüche.A solution according to the invention is given in the independent claims. Preferred embodiments result from combination with the features of the subclaims.
Gemäß einem Aspekt der Erfindung wird eine Verwendung eines Verfahrens, umfassend die Schritte: (a) Einbringen eines Vormaterials umfassend eine Legierung umfassend die Metalle Aluminium und Scandium in eine Vakuumkammer,wobei das Vormaterial eine AlMgMnScZr-Legierung ist, bestehend aus 4.3 Gew.-% Magnesium, 0.7 Gew.-% Scandium, 0.3 Gew.-% Zirkon und 0.5 Gew.-% Mangan, jeweils bezogen auf das Gesamtgewicht der Legierung, wobei der Anteil an Verunreinigungen an dem Gesamtgewicht der Legierung unterhalb von 0.5 Gew.-% liegt, der Rest ist Aluminium, (b) Vakuumentgasen des Vormaterials bei einem Vakuum von 0,1 bis 10-8 mbar und einer Temperatur von 275 bis 400 °C über eine Dauer von 15 bis 30 min, (c) Begasen des Vormaterials mit Stickstoff über eine Dauer von 1 bis 30 min, wobei der Stickstoff einen Wassergehalt von weniger als 1000 ppm enthält, und (d) abschließendes Vakuumentgasen des Vormaterials bei einem Vakuum von 0,1 bis 10-8 mbar und einer Temperatur von 275 bis 400 °C über eine Dauer von 15 bis 30 min, zur Herstellung eines hochtemperaturbelastbaren, mit Scandium legierten Aluminium-Werkstoffs, wobei das Verfahren einen weiteren, zusätzlichen Schritt (e) umfasst, in dem das Vormaterial direkt in Anschluss an Schritt (d) in der Vakuumkammer verdichtet wird, angegeben.According to one aspect of the invention there is provided a use of a method comprising the steps of: (a) introducing a precursor comprising an alloy comprising the metals aluminum and scandium into a vacuum chamber, said precursor being an AlMgMnScZr alloy consisting of 4.3 wt% Magnesium, 0.7% by weight scandium, 0.3% by weight zirconium and 0.5% by weight manganese, in each case based on the total weight of the alloy, the proportion of impurities in the total weight of the alloy being below 0.5% by weight, the rest is aluminum, (b) vacuum gases of the starting material at a vacuum of 0.1 to 10 -8 mbar and a temperature of 275 to 400 ° C over a period of 15 to 30 minutes, (c) gassing the starting material with nitrogen a duration of 1 to 30 minutes, where the nitrogen contains a water content of less than 1000 ppm, and (d) final vacuum degassing of the raw material at a vacuum of 0.1 to 10 -8 mbar and a temperature of 275 to 400 ° C over a period of 15 to 30 minutes, to produce a high temperature scandium alloyed aluminum material, the method comprising a further, additional step (e) of densifying the precursor material immediately after step (d) in the vacuum chamber is specified.
Gemäß einem weiteren Aspekt der Erfindung wird ein Verfahren zur Herstellung eines hochtemperaturbelastbaren, mit Scandium legierten Aluminium-Werkstoffs angegeben umfassend die Schritte: (a) Einbringen eines Vormaterials umfassend eine Legierung umfassend die Metalle Aluminium und Scandium in eine Vakuumkammer, wobei das Vormaterial eine AlMgMnScZr-Legierung ist, bestehend aus 4.3 Gew.-% Magnesium, 0.7 Gew.-% Scandium, 0.3 Gew.-% Zirkon und 0.5 Gew.-% Mangan, jeweils bezogen auf das Gesamtgewicht der Legierung, wobei der Anteil an Verunreinigungen an dem Gesamtgewicht der Legierung unterhalb von 0.5 Gew.-% liegt, der Rest ist Aluminium, wobei das Vormaterial nach dem Schmelzspinn-Verfahren hergestellt wurde, (b) Vakuumentgasen des Vormaterials bei einem Vakuum von 0,1 bis 10-8 mbar und einer Temperatur von 275 bis 400 °C über eine Dauer von 15 bis 30 min, (c) Begasen des Vormaterials mit Stickstoff über eine Dauer von 1 bis 30 min, wobei der Stickstoff einen Wassergehalt von weniger als 1000 ppm enthält, und (d) abschließendes Vakuumentgasen des Vormaterials bei einem Vakuum von 0,1 bis 10-8 mbar und einer Temperatur von 275 bis 400 °C über eine Dauer von 15 bis 30 min, wobei das Verfahren einen weiteren, zusätzlichen Schritt (e) umfasst, in dem das Vormaterial direkt in Anschluss an Schritt (d) in der Vakuumkammer verdichtet wird.According to another aspect of the invention, there is provided a method of making a high temperature scandium alloyed aluminum material comprising the steps of: (a) introducing a precursor material comprising an alloy comprising the metals aluminum and scandium into a vacuum chamber, the precursor material comprising an AlMgMnScZr; Alloy consisting of 4.3 wt .-% magnesium, 0.7 wt .-% scandium, 0.3 wt .-% zirconium and 0.5 wt .-% manganese, each based on the total weight of the alloy, wherein the proportion of impurities in the total weight of the Alloy below 0.5 wt .-%, the rest is aluminum, wherein the starting material (b) vacuum gases of the starting material at a vacuum of 0.1 to 10 -8 mbar and a temperature of 275 to 400 ° C over a period of 15 to 30 minutes, (c) gasification of the starting material with nitrogen for a period of 1 to 30 minutes, the nitrogen having a water content of less than 1000 ppm, and (d) final vacuum degassing of the starting material at a vacuum of 0.1 to 10 -8 mbar and a temperature of 275 to 400 ° C over a period of 15 to 30 minutes, the method comprising a further, additional step (e), in which the starting material is compacted in the vacuum chamber immediately after step (d).
Gemäß einem weiteren Aspekt der vorliegenden Erfindung, wird ein hochtemperaturbelastbarer, mit Scandium legierter Aluminium-Werkstoff bereitgestellt, der durch ein Verfahren erhältlich ist, das die folgenden Schritte umfasst: (a) Einbringen eines Vormaterials umfassend eine Legierung umfassend die Metalle Aluminium und Scandium in eine Vakuumkammer, wobei das Vormaterial eine AlMgMnScZr-Legierung ist, bestehend aus 4.3 Gew.-% Magnesium, 0.7 Gew.-% Scandium, 0.3 Gew.-% Zirkon und 0.5 Gew.-% Mangan, jeweils bezogen auf das Gesamtgewicht der Legierung, wobei der Anteil an Verunreinigungen an dem Gesamtgewicht der Legierung unterhalb von 0.5 Gew.-% liegt, der Rest ist Aluminium, wobei das Vormaterial nach dem Schmelzspinn-Verfahren hergestellt wurde, (b) Vakuumentgasen des Vormaterials bei einem Vakuum von 0,1 bis 10-8 mbar und einer Temperatur von 275 bis 400 °C über eine Dauer von 15 bis 30 min, (c) Begasen des Vormaterials mit Stickstoff über eine Dauer von 1 bis 30 min, wobei der Stickstoff einen Wassergehalt von weniger als 1000 ppm enthält, und (d) abschließendes Vakuumentgasen des Vormaterials bei einem Vakuum von 0,1 bis 10-8 mbar und einer Temperatur von 275 bis 400 °C über eine Dauer von 15 bis 30 min, wobei das Verfahren einen weiteren, zusätzlichen Schritt (e) umfasst, in dem das Vormaterial direkt in Anschluss an Schritt (d) in der Vakuumkammer verdichtet wird.According to another aspect of the present invention there is provided a high temperature scannable aluminum alloy material obtainable by a process comprising the steps of: (a) incorporating a primary material comprising an alloy comprising the metals aluminum and scandium in a vacuum chamber, wherein the starting material is an AlMgMnScZr alloy consisting of 4.3 wt .-% magnesium, 0.7 wt .-% scandium, 0.3 wt .-% zirconium and 0.5 wt .-% manganese, each based on the total weight of the alloy, wherein the proportion of impurities in the total weight of the alloy is less than 0.5 wt .-%, the balance is aluminum, wherein the starting material was prepared by the melt spinning method, (b) vacuum gases of the starting material at a vacuum of 0.1 to 10 -8 mbar and a temperature of 275 to 400 ° C over a period of 15 to 30 minutes, (c) gassing the starting material with nitrogen over a period of 1 to 30 minutes, the nitrogen having a water content of less than 1000 ppm, and (d) finally vacuum degassing the primary material at a vacuum of 0.1 to 10 -8 mbar and a temperature of 275 to 400 ° C over a period of 15 to 30 minutes, the method comprising a further, additional step (e) in which the starting material di is compacted in the vacuum chamber immediately after step (d).
Bevorzugte Ausführungsformen sind in den entsprechenden, abhängigen Ansprüchen offenbart.Preferred embodiments are disclosed in the respective dependent claims.
Das erfindungsgemäße Verfahren und/oder dessen Verwendung erlaubt die Herstellung von AlSc-Werkstoffen, die ein größeres Verarbeitungsfenster für die Herstellung von Halbzeugen aufweisen. Beispielsweise können die nach dem erfindungsgemäßen Verfahren und/oder dessen Verwendung hergestellten Werkstoffe bei höheren Temperaturen, schnelleren Auspressgeschwindigkeiten und höheren Verpress-Verhältnissen verarbeitet werden. Dies ist beispielsweise für die Herstellung von Halbzeugen mittels des Strangpress-Verfahrens von Vorteil.The inventive method and / or its use allows the production of AlSc materials, which have a larger processing window for the production of semi-finished products. For example, the materials produced by the process according to the invention and / or its use can be processed at higher temperatures, faster extrusion rates and higher injection ratios. This is for example advantageous for the production of semi-finished products by means of the extrusion process.
Des Weiteren ermöglicht die Erfindung die Herstellung leichter und korrosionssicherer AlSc-Werkstoffe mit sehr hoher Warmfestigkeit. Diese erfindungsgemäß hergestellten Werkstoffe weisen eine hohe Zähigkeit und Schadenstoleranz auf und ermöglichen eine kostengünstige Prozessführen. Das erfindungsgemäße Verfahren und dessen Verwendung hat den Vorteil, dass die Verstärkung "in situ" erfolgt und beispielsweise keine nanoskaligen Verstärkungsphasenpulver eingesetzt werden müssen, die schwer zu verarbeiten und explosionsgefährlich sind.Furthermore, the invention enables the production of lightweight and corrosion-resistant AlSc materials with very high heat resistance. These materials according to the invention have a high toughness and damage tolerance and allow cost-effective process leading. The inventive method and its use has the advantage that the reinforcement takes place "in situ" and, for example, no nanoscale reinforcing phase powder must be used, which are difficult to process and explosive.
Unter einem "Aluminium-Werkstoff" wird im Sinne der vorliegenden Erfindung ein metallisches Material verstanden, das im Wesentlichen aus Aluminium besteht und mit weiteren Metallen legiert sein kann.For the purposes of the present invention, an "aluminum material" is understood to mean a metallic material which consists essentially of aluminum and may be alloyed with other metals.
Ein "hochtemperaturbelastbarer AlSc-Werkstoff" im Sinne der vorliegenden Erfindung ist ein mit Scandium und gegebenenfalls noch weiteren Metallen legierter Aluminium-Werkstoff, dessen Gefüge oder Mikrostruktur bei einer Temperaturbelastung von mehr als 350°C weitestgehend stabil bleibt, d.h. die Korngröße und die Menge der Ausscheidungen, sowie deren Größe und Verteilung bleibt weitgehend konstant, so dass der Werkstoff bei Raumtemperatur ähnliche Festigkeitseigenschaften besitzt wie vor der Temperaturbeaufschlagung. Ein "hochtemperaturbelastbarer AlSc-Werkstoff" im Sinne der vorliegenden Erfindung weist vorzugsweise nach einer Temperaturbeaufschlagung von 350°C gegenüber dem Ausgangsmaterial bei Raumtemperatur einen Abfall in der Zugfestigkeit Rm von weniger als 5% auf und/oder nach einer Temperaturbeaufschlagung von 375°C gegenüber dem Ausgangsmaterial bei Raumtemperatur einen Abfall in der Zugfestigkeit Rm von weniger als 10% auf.For the purposes of the present invention, a "high-temperature-loadable AlSc material" is an aluminum material alloyed with scandium and, if appropriate, even further metals, whose structure or microstructure is at a Temperature load of more than 350 ° C remains largely stable, ie the grain size and the amount of precipitates, as well as their size and distribution remains largely constant, so that the material has similar strength properties at room temperature as before the temperature. A "high-temperature-resistant AlSc material" in the context of the present invention preferably exhibits a drop in tensile strength R m of less than 5% and / or after a temperature of 375 ° C. after a temperature exposure of 350 ° C. to the starting material at room temperature the starting material at room temperature, a drop in the tensile strength R m of less than 10%.
Ein hier beschriebene Verwendung eines Verfahren zur Herstellung eines hochtemperaturbelastbaren, mit Scandium legierten Aluminium-Werkstoffs umfasst die folgenden Verfahrensschritte: (a) Einbringen eines Vormaterials umfassend eine Legierung umfassend die Metalle Al und Sc in eine Vakuumkammer (b) Vakuumentgasen des Vormaterials, (c) Begasen des Vormaterials mit Stickstoff, (d) abschließendes Vakuumentgasen des Vormaterials, und (e) Verdichten des Vormaterials direkt im Anschluss an Schritt (d) in der Vakuumkammer.A use of a method for producing a high-temperature scandium-alloyed aluminum material described here comprises the following method steps: (a) introducing a starting material comprising an alloy comprising the metals Al and Sc into a vacuum chamber (b) vacuum gases of the starting material, (c) Gassing the primary material with nitrogen, (d) final vacuum degassing of the primary material, and (e) compacting the primary material immediately following step (d) in the vacuum chamber.
Das in dem Verfahren eingesetzte Vormaterial umfasst eine Legierung umfassend die Metalle Aluminium und Scandium. Die Menge an Scandium in der Legierung ist 0,7 Gew.-% bezogen auf die Gesamtmasse der Legierung.The primary material used in the process comprises an alloy comprising the metals aluminum and scandium. The amount of scandium in the alloy is 0.7% by weight based on the total mass of the alloy.
Die Legierung umfasst zusätzlich Zr, das in Aluminium-Materialien ähnliche Eigenschaften wie Scandium aufweist. Dieses Element kann sich mit dem Scandium additiv verhalten, d.h. es kann mit dem Scandium in dem Aluminium-Material zwangsgelöst werden und so eine Festigungssteigerung durch Ausscheidungshärtung ermöglichen. Dabei wird die Al3Sc Phase dadurch modifiziert, dass ein Teil des Scandiums durch Zr ersetzt wird.The alloy additionally includes Zr, which has properties similar to scandium in aluminum materials. This element can behave additively with the scandium, ie it can be forcibly dissolved with the scandium in the aluminum material and thus allow an increase in solidification by precipitation hardening. The Al 3 Sc phase is modified by replacing part of the scandium with Zr.
Die in der vorliegenden Erfindung als Vormaterial eingesetzte Legierung umfasst, neben Aluminium und Scandium, zusätzlich Zirkon in einer Menge von 0,3 Gew.-%.The alloy used as the starting material in the present invention additionally comprises, in addition to aluminum and scandium, zirconium in an amount of 0.3% by weight.
Es wird angenommen, dass durch den Zusatz von Zirkon in eine AlSc-Legierung die ausgeschiedene Al3Sc-Phase zu Al3Sc1-xZrx modifiziert wird, ohne dass sie an ihrer festigkeitssteigernden Wirkung verliert. Durch den Zirkon-Zusatz kann z.B. die minimale Abkühlungsgeschwindigkeit verringert werden, die eingehalten werden muss, um einen mit Scandium und Zirkon übersättigten Mischkristall zu erzeugen. Die Überalterung und damit der Rückgang der Verfestigungsfähigkeit wird verlangsamt. Dadurch kann die AlScZr-Legierung über einen längeren Zeitraum eine bestimmte Temperatur aushalten, bevor sie zu überaltern beginnt. Gleichzeitig erlaubt der Einsatz von Zirkon eine gewisse Verringerung der Menge an Scandium in der Legierung, welches auf Grund seiner Seltenheit ein relativ teures Legierungselement ist.It is believed that the addition of zirconia to an AlSc alloy alters the precipitated Al 3 Sc phase to Al 3 Sc 1 -x Zr x without losing its strength-increasing effect. Through the zirconium additive For example, the minimum cooling rate that must be maintained to produce a scandium and zirconium supersaturated solid solution can be reduced. The aging and thus the decline in the hardenability is slowed down. This allows the AlScZr alloy to withstand a certain temperature for an extended period of time before it begins to over age. At the same time, the use of zircon allows some reduction in the amount of scandium in the alloy, which is a relatively expensive alloying element due to its rarity.
Die Legierung umfasst zusätzlich zu den vorgenannten Legierungselementen Mg und Mn Durch den Zusatz dieser Elemente können die Eigenschaften des aus dem Vormaterial hergestellten Werkstoffs gezielt beeinflusst werden. Der Zusatz von Magnesium und Mangan erhöht die Festigkeit des Aluminium-Werkstoffs und ermöglicht so die Herstellung besonders harter Werkstoffe.In addition to the aforementioned alloying elements, the alloy comprises Mg and Mn. By adding these elements, the properties of the material produced from the starting material can be specifically influenced. The addition of magnesium and manganese increases the strength of the aluminum material and thus enables the production of particularly hard materials.
Das Vormaterial umfasst eine Legierung umfassend die Metalle Aluminium, Magnesium, Mangan, Scandium und Zirkon.The starting material comprises an alloy comprising the metals aluminum, magnesium, manganese, scandium and zirconium.
In kommerziell erhältlichen Aluminium-Legierungen sind in der Regel immer auch unerwünschte, aber meist tolerierbare, Verunreinigungen enthalten. Beispiele für solche Verunreinigungen sind Elemente wie z.B. AlkaliMetalle, Fe, Si, Be oder In. Diese Verunreinigungen können jeweils in einer Menge bis zu etwa 0,5 Gew.-% vorhanden sein, und insgesamt in einer Menge bis zu 2 Gew.-%, jeweils bezogen auf die Gesamtmasse der Legierung. Solche Verunreinigungen beeinträchtigen jedoch weder das erfindungsgemäße Verfahren oder dessen Verwendung, noch den erfindungsgemäßen AlSc-Werkstoff.In commercially available aluminum alloys, undesirable, but usually tolerable, impurities are usually always included. Examples of such impurities are elements such as e.g. Alkali metals, Fe, Si, Be or In. These impurities may each be present in an amount of up to about 0.5% by weight, and in total in an amount of up to 2% by weight, based in each case on the total mass of the alloy. However, such impurities do not affect either the process of the invention or its use, or the AlSc material according to the invention.
In der vorliegenden Erfindung wird eine AlMgMnScZr-Legierung als Vormaterial eingesetzt, die in der Hauptsache aus Aluminium sowie Zulegierungen von 4,3 Gew.-% Magnesium, 0,7 Gew.-% Scandium, 0,3 Gew.-% Zirkon und 0,5 Gew.-% Mangan besteht, jeweils bezogen auf das Gesamtgewicht der Legierung, wobei der Anteil an Verunreinigungen wie Fe, Si, Zn, usw. An dem Gesamtgewicht der Legierung unterhalb von 0,5 Gew.-% liegt.In the present invention, an AlMgMnScZr alloy is used as a starting material, which consists mainly of aluminum and alloys of 4.3 wt .-% magnesium, 0.7 wt .-% scandium, 0.3 wt .-% zirconium and 0 , 5 wt .-% manganese, each based on the total weight of the alloy, wherein the proportion of impurities such as Fe, Si, Zn, etc., the total weight of the alloy is below 0.5 wt .-%.
Gemäß einer Ausführungsform wird das Vormaterial als partikelförmiges Material eingesetzt, z.B. in Form eines Pulvers, eines Granulats oder in Form von Flocken. Gemäß einer Ausführungsform wird das Vormaterial als lose Schüttung in die Vakuumkammer eingebracht. Die Schüttdichte kann beispielsweise zwischen 5 und 40%, 10 und 30 % oder 15 und 20% liegen. Es besteht jedoch auch die Möglichkeit das Vormaterial auf eine Dichte von bis zu 50% vorzukompaktieren.According to one embodiment, the starting material is used as a particulate material, for example in the form of a powder, a granulate or in the form of flakes. According to In one embodiment, the starting material is introduced as a loose bed in the vacuum chamber. The bulk density may for example be between 5 and 40%, 10 and 30% or 15 and 20%. However, it is also possible to precompact the starting material to a density of up to 50%.
Gemäß einer Ausführungsform wird als Vormaterial ein schnell erstarrtes Material eingesetzt, das mittels eines pulvermetallurgischen Schnellerstarrungs-Verfahrens (engl. "rapid solidification processing") erhalten wurde. Die beschleunigte Abkühlung ermöglicht es, erheblich mehr Scandium in dem übersättigten Mischkristall zu lösen, als dies im Gleichgewichtszustand möglich wäre. Beispielsweise kann die Abkühlung des Vormaterials bei Abkühlgeschwindigkeiten von 100 bis 109 K/s erfolgen, z.B. bei Abkühlungsgeschwindigkeiten von 1000 bis 108 K/s, von 104 bis 107 K/s oder von 105 bis 106 K/s. Geeignete Verfahren zur Herstellung eines schnell erstarrten Vormaterials sind beispielsweise Verdüsen oder Atomisieren, das Schleuder-Kokillen-Verfahren, Splat-Cooling oder das Schmelzspinn-Verfahren.According to one embodiment, the starting material used is a rapidly solidified material which has been obtained by means of a powder metallurgy rapid solidification processing ("rapid solidification processing"). The accelerated cooling makes it possible to dissolve considerably more scandium in the supersaturated solid solution than would be possible in the equilibrium state. For example, the cooling of the starting material at cooling rates of 100 to 10 9 K / s carried out, for example, at cooling rates of 1000 to 10 8 K / s, from 10 4 to 10 7 K / s or from 10 5 to 10 6 K / s. Suitable processes for the production of a rapidly solidified starting material are, for example, atomization or atomization, the centrifugal mold process, splat cooling or the melt spinning process.
Gemäß einer bevorzugten Ausführungsform wird das Vormaterial mittels des Schmelzspinn-Verfahrens hergestellt. Bei diesem Verfahren wird die aufgeschmolzene Legierung durch eine keramische Düse auf einen rasch rotierenden, wassergekühlten Metallzylinder aufgegossen. Der innige Kontakt zwischen dem sich bildenden Metallfilm und dem Zylinder sowie dessen hohe Wärmeleitfähigkeit bewirken eine extrem schnelle Abkühlung. Vor einer vollen Umdrehung des Metallzylinders wird der Metallfilm abgehoben, so dass sich ein kontinuierliches dünnes Band bildet. Die Abkühlungsgeschwindigkeit korreliert mit der Banddicke, die wiederum durch die Walzengeschwindigkeit gesteuert werden kann. Die Banddicke kann beispielsweise zwischen 0,01 und 1,00 mm liegen. Vorzugsweise beträgt die Banddicke weniger als 0,1 mm. Das so erhaltene Band kann zur Herstellung eines partikelförmigen Materials zerkleinert werden. Das nach dem Schmelzspinn-Verfahren hergestellte Vormaterial kann beispielsweise in Form eines Granulats weiterverarbeitet werden. Ein solches nach dem Schmelzspinn-Verfahren hergestelltes Granulat hat im Vergleich zu einem pulverförmigen Vormaterial, von dem auf Grund seiner großen Oberfläche eine hohe Explosionsgefahr ausgeht, den Vorteil, dass es sich wesentlich einfacher und ohne besondere Sicherheitsvorkehrungen handhaben lässt. Somit erlaubt der Einsatz eines nach dem Schmelzpinn-Verfahren hergestellten Vormaterials eine vereinfachte und effizientere Prozessführung.According to a preferred embodiment, the starting material is produced by means of the melt spinning process. In this process, the molten alloy is poured through a ceramic die onto a rapidly rotating, water-cooled metal cylinder. The intimate contact between the forming metal film and the cylinder and its high thermal conductivity cause an extremely rapid cooling. Before a full turn of the metal cylinder The metal film is lifted so that forms a continuous thin band. The cooling rate correlates with the strip thickness, which in turn can be controlled by the roll speed. The strip thickness can be, for example, between 0.01 and 1.00 mm. Preferably, the strip thickness is less than 0.1 mm. The strip thus obtained can be comminuted to produce a particulate material. The starting material produced by the melt spinning process can be further processed, for example in the form of granules. Such a granulate produced by the melt spinning method has the advantage that it can be handled much easier and without special safety precautions compared to a powdery starting material, which poses a high risk of explosion due to its large surface area. Thus, the use of a starting material produced by the melt spinning process allows a simplified and more efficient process management.
Das in die Vakuumkammer eingebrachte Vormaterial wird gemäß Schritt (b) des erfindungsgemäßen Verfahrens und/oder der erfindungsgemäßen Verwendung im Vakuum entgast. Bei dem Entgasungsprozess wird das Vormaterial, dessen Oberfläche mit Wasserstoff, Oxiden sowie Hydroxiden und Feuchtigkeit kontaminiert sein kann, in einem Vakuum behandelt, um so diese eventuell vorhandenen, unerwünschten Kontaminationen zu entfernen. Die Vakuumentgasung wird in einem geeigneten gasdichten Behälter, auch Vakuumkammer oder Rezipient genannt, durchgeführt, wobei dieser einen Gasauslass aufweist, der über ein Ventil mit einem Vakuumsystem verbunden ist.The introduced into the vacuum chamber precursor is degassed according to step (b) of the method according to the invention and / or the use according to the invention in a vacuum. In the degassing process, the starting material, the surface of which may be contaminated with hydrogen, oxides and hydroxides and moisture, is treated in a vacuum so as to remove any such undesired contaminants. The vacuum degassing is carried out in a suitable gastight container, also called vacuum chamber or recipient, wherein this one Gas outlet which is connected via a valve with a vacuum system.
In der vorliegenden Erfindung wird das Vakuumentgasen bei einem Vakuum von 0,1 bis 10-8 mbar durchgeführt. Beispielsweise kann die Vakuumkammer so gesteuert werden, dass das Vakuum in einem Bereich von 8-10-2 bis 10-7 mbar, 5.10-2 bis 10-6 mbar, 2,5·10-2 bis 10-5 mbar oder 10-2 bis 10-4 mbar liegt.In the present invention, the vacuum degassing is carried out at a vacuum of 0.1 to 10 -8 mbar. For example, the vacuum chamber can be controlled so that the vacuum in a range of 8-10 -2 to 10 -7 mbar, 5.10 -2 to 10 -6 mbar, 2.5 · 10 -2 to 10 -5 mbar or 10 - 2 to 10 -4 mbar.
Der Entgasungsprozess wird zur Steigerung der Effizienz bei einer erhöhten Temperatur von 275 bis 400°C durchgeführt, vorzugsweise bei einer Temperatur von 275 bis 380°C oder von 275 bis 350°C, besonders bevorzugt bei 290°C.
Das Vakuumentgasen wird gemäß Verfahrensschritt (b) und (d) über eine Dauer von 15 min bis 30 min durchgeführt.The degassing process is carried out to increase the efficiency at an elevated temperature of 275 to 400 ° C, preferably at a temperature of 275 to 380 ° C or 275 to 350 ° C, more preferably at 290 ° C.
The vacuum degassing is carried out according to process steps (b) and (d) over a period of 15 minutes to 30 minutes.
Gemäß einer beispielhaften Ausführungsform der vorliegenden Erfindung wird das Vakuumentgasen gemäß Verfahrensschritt (b) und/oder (d) bei einem Vakuum von 0,05 mbar und einer Temperatur von 290°C über eine Dauer von 15 bis 30 min durchgeführt.According to an exemplary embodiment of the present invention, the vacuum degassing according to process step (b) and / or (d) is at a vacuum of 0.05 mbar and a temperature of 290 ° C over a period of 15 to 30 minutes.
In dem erfindungsgemäßen Verfahren oder dessen Verwendung wird der Vakuumentgasungsschritt (b) durch einen Schritt (c) unterbrochen, in dem das Vormaterial mit Stickstoff begast wird. Gemäß einer Ausführungsform wird der Stickstoff in die Vakuumkammer über den Gasauslass eingeleitet, an dem das Vakuumsystem angeschlossen ist, wobei der Gasauslass mit einem für diesen Zweck geeigneten Ventil versehen ist, z.B. mit einem 3/2-WegeVentil. Es besteht jedoch auch die Möglichkeit den Stickstoff über einen separaten Gaseinlass in die Vakuumkammer einzuleiten. Je nach Ausgestaltung der Vakuumkammer kann das Stickstoffgas beispielsweise auf die Oberfläche des Vormaterials aufgeblasen oder auch von unten durch das Vormaterial hindurch geblasen werden.In the method according to the invention or its use, the vacuum degassing step (b) is interrupted by a step (c) in which the starting material is sparged with nitrogen. According to one embodiment, the nitrogen is introduced into the vacuum chamber via the gas outlet to which the vacuum system is connected, the gas outlet being provided with a valve suitable for this purpose, e.g. with a 3/2-way valve. However, it is also possible to introduce the nitrogen via a separate gas inlet in the vacuum chamber. Depending on the design of the vacuum chamber, the nitrogen gas can be inflated, for example, on the surface of the starting material or blown from below through the starting material.
Zur Begasung des Vormaterials wird trockener Stickstoff verwendet. Hierdurch kann eine erneute Kontamination des Vormaterials mit Wasserstoff und Wasser verhindert werden. Geeignet ist Stickstoff, der weniger als 1000 ppm Wasser enthält, z.B. weniger als 500 ppm, weniger als 250 ppm, weniger als 100 ppm, weniger als 50 ppm oder weniger als 5 ppm Wasser.For the aeration of the starting material dry nitrogen is used. As a result, a renewed contamination of the starting material with hydrogen and water can be prevented. Suitable is nitrogen containing less than 1000 ppm water, e.g. less than 500 ppm, less than 250 ppm, less than 100 ppm, less than 50 ppm, or less than 5 ppm of water.
Das Begasen des Vormaterials mit Stickstoff erfolgt über eine Dauer von 1 bis 30 min, 2 bis 20 min oder 5 bis 15 min. Gemäß einer beispielhaften Ausführungsform erfolgt das Begasen des Vormaterials mit Stickstoff über eine Dauer von 10 min. Gemäß einer anderen beispielhaften Ausführungsform wird das Vormaterial mindestens solange mit Stickstoff begast bis in der Vakuumkammer Atmosphärendruck herrscht.The gassing of the starting material with nitrogen takes place over a period of 1 to 30 minutes, 2 to 20 minutes or 5 to 15 minutes. According to an exemplary embodiment, the gasification of the starting material takes place with nitrogen over a period of 10 min. According to another exemplary embodiment, the starting material is at least as long gassed with nitrogen until there is atmospheric pressure in the vacuum chamber.
Die Schritte (b) und (c) können einmal oder mehrmals hintereinander durchgeführt werden. Gemäß einer Ausführungsform der vorliegenden Erfindung werden die Schritte (b) und (c) mehrmals hintereinander durchgeführt, beispielsweise 1 bis 10mal, 2 bis 9mal, 3 bis 8mal, 4 bis 7 mal, oder 5 bis 6mal. Vorzugsweise werden die Schritte (b) und (c) 5mal nacheinander durchgeführt.Steps (b) and (c) may be performed one or more times in succession. According to one 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. Preferably, steps (b) and (c) are performed 5 times in succession.
Ohne auf eine bestimmte Theorie festgelegt zu sein, wird angenommen, dass während der Vakuumentgasung eine Aktivierung der Oberfläche des Vormaterials stattfindet, welche dann die Adsorption sowie eine chemische Reaktion des Stickstoffs mit der AlSc-Legierung ermöglicht. Hierdurch scheinen sich thermisch sehr stabile Scandiumnitrid-Phasen auszubilden. Bei Anwesenheit von Elementen, die das Scandium ergänzen oder ersetzen können, wie z.B. Zirkon, besteht auch die Möglichkeit, dass mit diesen entsprechende Nitrid-Phasen ausgebildet werden, z.B. Zirkonnitrid-Phasen bei Anwesenheit von Zirkon in der Legierung.Without wishing to be bound by theory, it is believed that activation of the surface of the primary material takes place during vacuum degassing which then permits adsorption as well as chemical reaction of the nitrogen with the AlSc alloy. As a result, thermally stable scandium nitride phases appear to form. In the presence of elements capable of supplementing or replacing the scandium, e.g. Zirconium, it is also possible that corresponding nitride phases may be formed therewith, e.g. Zirconium nitride phases in the presence of zirconium in the alloy.
Gemäß des erfindungsgemäßen Verfahrens findet im Anschluss an die Schritte (b) und (c) ein abschließendes Vakuumentgasen des Vormaterials als Verfahrensschritt (d) statt. Das Vakuumentgasen wird wie unter Schritt (b) beschrieben durchgeführt.According to the inventive method, following the steps (b) and (c), a final vacuum degassing of the starting material takes place as process step (d). The vacuum degassing is carried out as described under step (b).
Gemäß einer beispielhaften Ausführungsform beträgt die Gesamtdauer der Verfahrensschritte (b), (c) und (d) nicht mehr als 3000 min, 500 min, 300 min, 150 min oder 100 min.According to an exemplary embodiment, the total duration of process steps (b), (c) and (d) is not more than 3000 min, 500 min, 300 min, 150 min or 100 min.
Nach dem abschließenden Vakuumentgasen wird das Vormaterial verdichtet. Die Verdichtung kann mechanisch oder mittels Gasdruck erfolgen. Beispiele für geeignete mechanische Verdichtungsverfahren sind Kaltpressen, Isostatisches Pressen oder Vakuumpressen. Ein Beispiel für ein geeignetes Verdichtungsverfahren mittels Gasdruck ist das Heiß-Isostatische-Pressen (HIP). Das Verdichten kann bei Atmosphärendruck oder unter Vakuum erfolgen.After the final vacuum degassing, the starting material is compacted. The compression can be done mechanically or by gas pressure. Examples of suitable mechanical compression methods are cold pressing, isostatic pressing or vacuum pressing. An example of a suitable gas pressure compression process is hot isostatic pressing (HIP). The compression can be done at atmospheric pressure or under vacuum.
Das Vormaterial wird in Anschluss an den abschließenden Entgasungsschritt (d) in der Vakuumkammer verdichtet. Gemäß einer beispielhaften Ausführungsform wird das Vormaterial in Anschluss an den abschließenden Entgasungsschritt (d) mittels mechanischem Vakuumpressen in der Vakuumkammer verdichtet.The starting material is compressed in the vacuum chamber following the final degassing step (d). According to an exemplary embodiment, the precursor material is compacted after the final degassing step (d) by means of mechanical vacuum pressing in the vacuum chamber.
Der verdichtete AlSc-Werkstoff kann beispielsweise eine Dichte größer als 80%, größer als 90%, größer als 95 %, größer als 98% oder größer als 99% aufweisen. Gemäß einer bevorzugten Ausführungsform ist die Dichte des verdichteten AlSc-Werkstoff größer als 95%.For example, the densified AlSc material may have a density greater than 80%, greater than 90%, greater than 95%, greater than 98%, or greater than 99%. According to a preferred embodiment, the density of the densified AlSc material is greater than 95%.
Im Anschluss an das Verdichten kann der erhaltene AlSc-Werkstoff zur Herstellung von Halbzeug und Formteilen umgeformt werden. Beispiele für geeignete Umformungsverfahren sind Extrudieren oder Strangpressen, Walzen, Schmieden, Streckziehen, Stanzen, Fließpressen oder Tiefziehen.Following compaction, the resulting AlSc material can be transformed to produce semi-finished products and molded parts. Examples of suitable forming processes are extruding or extrusion, rolling, forging, ironing, stamping, extrusion or deep drawing.
Der nach dem erfindungsgemäßen Verfahren oder dessen Verwendung hergestellte AlSc-Werkstoff weist eine verbesserte Strangpressbarkeit oder Extrudierbarkeit auf. Auf Grund seiner Hochtemperaturbelastbarkeit kann das Strangpressen des erfindungsgemäßen AlSc-Werkstoffs bei höheren Temperaturen durchgeführt werden, wodurch der Fließwiderstand oder Umformungswiderstand des Werkstoffs abnimmt und dieser so besser verformbar wird. Ein "AlSc-Werkstoff mit verbesserter Strangpressbarkeit" im Sinne der vorliegenden Erfindung kann vorzugsweise bei einer Temperatur von mehr als 320°C mittels Strangpressen weiterverarbeitet werden, ohne dass die Zugfestigkeit Rm des Werkstoffs gegenüber dem Ausgangsmaterial bei Raumtemperatur, d.h. bei 20°C, signifikant abfällt. Beispielsweise weist der erfindungsgemäße AlSc-Werkstoff nach einer Strangpressung bei etwa 350°C gegenüber dem Ausgangsmaterial bei Raumtemperatur einen Abfall in der Zugfestigkeit Rm von weniger als 5% auf und/oder nach einer Strangpressung bei etwa 375°C gegenüber dem Ausgangsmaterial bei Raumtemperatur einen Abfall in der Zugfestigkeit Rm von weniger als 10% auf.The AlSc material produced by the method according to the invention or its use has improved extrudability or extrudability. Due to its high temperature resistance, the extrusion of the AlSc material according to the invention can be carried out at higher temperatures, whereby the flow resistance or deformation resistance of the material decreases and this is better deformed. An "AlSc material with improved extrudability" in the context of the present invention may preferably be further processed at a temperature of more than 320 ° C by means of extrusion without the tensile strength R m of the material compared to the starting material at room temperature, ie at 20 ° C, falls significantly. For example, the AlSc material according to the invention after being extruded at about 350 ° C. relative to the starting material at room temperature has a drop in tensile strength R m of less than 5% and / or after extrusion at about 375 ° C. compared to the starting material at room temperature Drop in tensile strength R m of less than 10%.
Gemäß einer beispielhaften Ausführungsform wird der verdichtete AlSc-Werkstoff mittels Strangpressen bei 320 bis 400°C, vorzugsweise bei 340 bis 375°C oder bei etwa 350°C weiterverarbeitet.According to an exemplary embodiment, the compacted AlSc material is further processed by extrusion at 320 to 400 ° C, preferably at 340 to 375 ° C or at about 350 ° C.
Die nach dem erfindungsgemäßen Verfahren oder seiner Verwendung hergestellten Werkstoffe können beispielsweise zur Herstellung eines geschweißten, gewalzten, geschmiedeten oder stranggepressten oder extrudierten Bauteils für ein Luftfahrzeug, ein Seefahrzeug oder ein Kraftfahrzeug verwendet werden. Gemäß einer bevorzugten Ausführungsform werden die nach dem erfindungsgemäßen Verfahren oder seiner Verwendung hergestellten Werkstoffe zur Herstellung eines stranggepressten oder extrudierten Bauteils für ein Luftfahrzeug, ein Seefahrzeug oder ein Kraftfahrzeug verwendet.The materials produced by the method or its use according to the invention can be used, for example, for producing a welded, rolled, forged or extruded or extruded component for an aircraft, a sea-going vehicle or a motor vehicle. According to a preferred embodiment, the materials produced by the method according to the invention or its use are used for producing an extruded or extruded component for an aircraft, a sea-going vehicle or a motor vehicle.
Als Vormaterial wurde eine AlMgScZr-Legierung eingesetzt, die in der Hauptsache aus Aluminium sowie Zulegierungen von 4,3 Gew.-% Magnesium, 0,7 Gew.-% Scandium, 0,3 Gew.-% Zirkon und 0,5 Gew.-% Mangan besteht, jeweils bezogen auf das Gesamtgewicht der Legierung. Der Anteil an Verunreinigungen wie Fe, Si, Zn, usw. an dem Gesamtgewicht der Legierung lag unterhalb von 0,5 Gew.-%.The starting material used was an AlMgScZr alloy, which consisted mainly of aluminum and alloys of 4.3% by weight of magnesium, 0.7% by weight of scandium, 0.3% by weight of zirconium and 0.5% by weight. -% manganese is, in each case based on the total weight of the alloy. The content of impurities such as Fe, Si, Zn, etc. in the total weight of the alloy was below 0.5 wt%.
Die AlMgScZr-Legierung wurde in Form eines Granulats eingesetzt, das mittels des Schmelzspinn-Verfahrens hergestellt wurde. Die nominelle Banddicke, welche die erreichbare Abkühlgeschwindigkeit während des Schmelzspinn-Verfahrens definiert, betrug 0,100 mm. Hieraus errechnet sich eine maximale Abkühlungsgeschwindigkeit (abgeleitet von dem sogenannten Dendritenarmabstand, der metallografisch ermittelt wurde) von etwa 2·105 K/s.The AlMgScZr alloy was used in the form of granules prepared by the melt spinning method. The nominal strip thickness, which defines the achievable cooling rate during the melt spinning process, was 0.100 mm. From this, a maximum cooling rate (derived from the so-called dendrite arm spacing, which was determined by metallography) of about 2 × 10 5 K / s is calculated.
Aus dem AlMgScZr-Vormaterial wurde nach einem Herstellungsverfahren für AlMgSc-Werkstoffe nach dem Stand der Technik (Verfahren A) ein Werkstoff A und nach dem erfindungsgemäßen Verfahren (Verfahren B) ein Werkstoff B hergestellt. Die Weiterverarbeitung der beiden Werkstoff zu Rundstäben mittels Strangpressen war gleich.A material A was produced from the AlMgScZr starting material by a production process for AlMgSc materials according to the prior art (process A) and a material B by the process according to the invention (process B). The further processing of the two materials to round bars by extrusion was the same.
Das Vormaterial wurde in einem Rezipienten mit einem Durchmesser von 31 mm als lose Schüttung mit einer Höhe von 150 mm vorgelegt. Der Rezipient wies einen Gasauslass auf, der über ein Ventil an ein Vakuumsystem angeschlossen wurde. Die Vakuumentgasung wurde bei 5·10-2 mbar und einer Temperatur von 290°C über eine Dauer von 120 min durchgeführt.The starting material was placed in a recipient with a diameter of 31 mm as a loose bed with a height of 150 mm. The recipient had a gas outlet, which was connected via a valve to a vacuum system. The vacuum degassing was carried out at 5 × 10 -2 mbar and a temperature of 290 ° C. over a period of 120 minutes.
Im Anschluss an die Entgasung wurde das Vormaterial im Rezipienten unter Vakuum in einer 200 t Presse bei einer Temperatur von 290°C und einer Presskraft von etwa 330 N/mm2 mechanisch zu einem Bolzen kompaktiert. Der erhaltene Bolzen wies eine Dichte von etwa 99% und eine Höhe von 25 mm auf.Following degassing, the starting material in the recipient was mechanically compacted into a bolt under vacuum in a 200 t press at a temperature of 290 ° C. and a pressing force of about 330 N / mm 2 . The obtained stud had a density of about 99% and a height of 25 mm.
Das Vormaterial wurde in einem Rezipienten mit einem Durchmesser von 31 mm als lose Schüttung mit einer Höhe von 150 mm vorgelegt. Der Rezipient wies einen Gasauslass auf, der über ein 3/2-Wege-Ventil an ein Vakuumsystem und eine Stickstoffquelle angeschlossen wurde. Die Vakuumentgasung wurde bei 5·10-2 mbar und einer Temperatur von 290°C über eine Dauer von 15 min durchgeführt. Anschließend wurde zur Begasung des Vormaterials trockener Stickstoff mit einem Wassergehalt von weniger als 100 ppm in den Rezipienten eingeleitet bis in der Vakuumkammer Atmosphärendruck herrschte. Der zuvor beschriebene Vakuumentgasungsschritt und die nachfolgende Begasung mit Stickstoff wurden insgesamt 5mal durchgeführt. Danach erfolgte eine abschließende Vakuumentgasung bei 5·10-2 mbar und einer Temperatur von 290°C. Die Gesamtdauer des Verfahrens betrug 300 min.The starting material was placed in a recipient with a diameter of 31 mm as a loose bed with a height of 150 mm. The recipient had a gas outlet connected to a vacuum system and a nitrogen source via a 3/2-way valve. The vacuum degassing was at 5 × 10 -2 mbar and a temperature of 290 ° C over a period of 15 min performed. Subsequently, to feed the starting material, dry nitrogen having a water content of less than 100 ppm was introduced into the recipient until atmospheric pressure prevailed in the vacuum chamber. The vacuum degassing step described above and the subsequent sparging with nitrogen were carried out a total of 5 times. This was followed by a final vacuum degassing at 5 × 10 -2 mbar and a temperature of 290 ° C. The total duration of the process was 300 min.
Im Anschluss wurde das Vormaterial im Rezipienten unter Vakuum in einer 200 t Presse bei einer Temperatur von 290°C und einer Presskraft von etwa 330 N/mm2 mechanisch zu einem Bolzen kompaktiert. Der erhaltene Bolzen wies eine Dichte von etwa 99% und eine Höhe von 25 mm auf.Subsequently, the starting material in the recipient was mechanically compacted into a bolt under vacuum in a 200 t press at a temperature of 290 ° C. and a pressing force of about 330 N / mm 2 . The obtained stud had a density of about 99% and a height of 25 mm.
Die gemäß Verfahren A bzw. B erhaltenen und auf Raumtemperatur abgekühlten Bolzen wurden aus dem Rezipienten entnommen und auf einen Durchmesser von 30 mm und eine Länge von 22 mm überdreht. Anschließend wurden die Bolzen in eine Strangpressvorichtung im Ofen auf etwa 320°C aufgeheizt, wobei Aufheizdauer und Haltezeit insgesamt 120 min betrugen. Die Strangpressung erfolgte mit einer 200 t Presse mit einer kontinuierlich steigenden Auspressgeschwindigkeit, wobei die Anfangsgeschwindigkeit 250 mm/min und die Endgeschwindigkeit 4000 mm/min betrug. Die gepresste Profilgeometrie war ein Rundstab mit einem Durchmesser von 6 mm und einer Länge von etwa 500 mm. Das Verpressverhältnis lag bei 25:1.The obtained according to methods A and B and cooled to room temperature bolts were removed from the recipient and overdriven to a diameter of 30 mm and a length of 22 mm. Subsequently, the bolts were heated in an extrusion device in the oven to about 320 ° C, wherein heating time and holding time totaled 120 min. The extrusion was carried out with a 200 t press with a continuously increasing extrusion speed, the initial speed was 250 mm / min and the final speed 4000 mm / min. The pressed profile geometry was a round bar with a Diameter of 6 mm and a length of about 500 mm. The compression ratio was 25: 1.
Aus den gepressten Rundstäben werden jeweils 3 Rundzugproben gemäß DIN 50125 aus dem Anfangs-, Mitte- und Endbereich des jeweiligen Stabs entnommen. Die Ergebnisse der Festigkeitsprüfung sind in Tabelle 1 dargestellt.
(Vergleichsbeispiel)
(Comparative Example)
Die Ergebnisse der Festigkeitsprüfung zeigen, dass die Festigkeit des Werkstoffs B weitgehend konstant ist. Mit zunehmender Pressgeschwindigkeit, und der damit einhergehenden zusätzlichen (adiabatischen) Materialverformungserwärmung, bleibt die Festigkeit des nach dem erfindungsgemäßen Verfahren hergestellten Werkstoffs B lange erhalten und fällt erst gegen Strangende geringfügig (um etwa 6%) ab. Dagegen fällt bei dem nach dem Verfahren nach dem Stand der Technik hergestellten Werkstoff A die Festigkeit zum Ende des Stabs stark ab. Der Festigkeitsverlust des Werkstoffs A beträgt in der Strangmitte bereits mehr als 11% und am Strangende sogar mehr als 25%.The results of the strength test show that the strength of the material B is largely constant. With increasing pressing speed, and the concomitant additional (adiabatic) material deformation heating, the strength of the material B produced by the process according to the invention is retained for a long time and drops slightly towards the end of the strand (by about 6%). On the other hand, in the material A produced by the method of the prior art, the strength at the end of the rod greatly drops. The loss of strength of the material A is already more than 11% in the strand center and even more than 25% at the strand end.
Das erfindungsgemäße Verfahren und/oder dessen Verwendung ermöglicht somit die Herstellung von mit Scandium legierten Aluminium-Werkstoffen, die auch bei hohen Umformungsgeschwindigkeiten (Strangpressgeschwindigkeiten) eine gleich bleibend hohe Werkstofffestigkeit aufweisen. Zudem kann das erfindungsgemäß modifizierte AlMgSc-Material bei höheren Temperaturen stranggepresst werden als der Stand der Technik ohne dabei die zuvor beschriebenen großen Festigkeitsverluste zu erleiden.The inventive method and / or its use thus enables the production of scandium-alloyed aluminum materials, which have a consistently high material strength even at high deformation rates (extrusion rates). In addition, the modified AlMgSc material according to the invention can be extruded at higher temperatures than the prior art without suffering the above-described large strength losses.
Weitere Ausführungsbeispiele oder Aspekte der vorliegenden Erfindung sind im Folgenden wiedergegeben:
- 1. Verfahren zur Herstellung eines hochtemperaturbelastbaren, mit Scandium legierten Aluminium-Werkstoffs umfassend die Schritte:
- a) Einbringen eines Vormaterials umfassend eine Legierung umfassend die Metalle Aluminium und Scandium in eine Vakuumkammer, wobei das Vormaterial eine AlMgMnScZr-Legierung ist, bestehend aus 4.3 Gew.-% Magnesium, 0.7 Gew.-% Scandium, 0.3 Gew.-% Zirkon und 0.5 Gew.-% Mangan, jeweils bezogen auf das Gesamtgewicht der Legierung, wobei der Anteil an Verunreinigungen an dem Gesamtgewicht der Legierung unterhalb von 0.5 Gew.-% liegt, der Rest ist Aluminium, wobei das Vormaterial nach dem Schmelzspinn-Verfahren hergestellt wurde,
- b) Vakuumentgasen des Vormaterials bei einem Vakuum von 0,1 bis 10-8 mbar und einer Temperatur von 275 bis 400 °C über eine Dauer von 15 bis 30 min,
- c) Begasen des Vormaterials mit Stickstoff über eine Dauer von 1 bis 30 min, wobei der Stickstoff einen Wassergehalt von weniger als 1000 ppm enthält, und
- d) abschließendes Vakuumentgasen des Vormaterials bei einem Vakuum von 0,1 bis 10-8 mbar und einer Temperatur von 275 bis 400 °C über eine Dauer von 15 bis 30 min,
- 2. Verfahren gemäß Aspekt 1, wobei das Vormaterial als Granulat vorliegt.
- 3. Verfahren gemäß Aspekt 1 oder 2, wobei die Schritte (b) und (c) 1 bis 10mal hintereinander durchgeführt werden.
- 4. Hochtemperaturbelastbarer, mit Scandium legierter Aluminium-Werkstoff, erhältlich durch das Verfahren umfassend die Schritte:
- a) Einbringen eines Vormaterials umfassend eine Legierung umfassend die Metalle Aluminium und Scandium in eine Vakuumkammer, wobei das Vormaterial eine AlMgMnScZr-Legierung ist, bestehend aus 4.3 Gew.-% Magnesium, 0.7 Gew.-% Scandium, 0.3 Gew.-% Zirkon und 0.5 Gew.-% Mangan, jeweils bezogen auf das Gesamtgewicht der Legierung, wobei der Anteil an Verunreinigungen an dem Gesamtgewicht der Legierung unterhalb von 0.5 Gew.-% liegt, der Rest ist Aluminium, wobei das Vormaterial nach dem Schmelzspinn-Verfahren hergestellt wurde,
- b) Vakuumentgasen des Vormaterials bei einem Vakuum von 0,1 bis 10-8 mbar und einer Temperatur von 275 bis 400 °C über eine Dauer von 15 bis 30 min,
- c) Begasen des Vormaterials mit Stickstoff über eine Dauer von 1 bis 30 min, wobei der Stickstoff einen Wassergehalt von weniger als 1000 ppm enthält, und
- d) abschließendes Vakuumentgasen des Vormaterials bei einem Vakuum von 0,1 bis 10-8 mbar und einer Temperatur von 275 bis 400 °C über eine Dauer von 15 bis 30 min,
- 5. Verwendung eines Werkstoffs gemäß Aspekt 4 zur Herstellung eines geschweißten, gewalzten, stranggepressten oder geschmiedeten Bauteils für ein Luftfahrzeug, ein Seefahrzeug oder ein Kraftfahrzeug.
- 6. Geschweißtes, gewalztes, stranggepresstes oder geschmiedetes Bauteil für ein Luftfahrzeug, ein Seefahrzeug oder ein Kraftfahrzeug bestehend aus einem Werkstoff gemäß Aspekt 4.
- 1. A method of making a high temperature scandium alloyed aluminum material comprising the steps of:
- a) introducing a starting material comprising an alloy comprising the metals aluminum and scandium in a vacuum chamber, wherein the starting material is an AlMgMnScZr alloy consisting of 4.3 wt .-% magnesium, 0.7 wt .-% scandium, 0.3 wt .-% zirconium and 0.5% by weight of manganese, based in each case on the total weight of the alloy, the proportion of impurities in the total weight of the alloy being less than 0.5% by weight, the remainder being aluminum, the starting material being produced by the melt-spinning method,
- b) vacuum gases of the starting material at a vacuum of 0.1 to 10 -8 mbar and a temperature of 275 up to 400 ° C over a period of 15 to 30 minutes,
- c) gassing the starting material with nitrogen for a period of 1 to 30 minutes, wherein the nitrogen has a water content of less than 1000 ppm, and
- d) final vacuum degassing of the starting material at a vacuum of 0.1 to 10 -8 mbar and a temperature of 275 to 400 ° C over a period of 15 to 30 minutes,
- 2. The method according to aspect 1, wherein the starting material is present as granules.
- 3. Process according to aspect 1 or 2, wherein steps (b) and (c) are carried out 1 to 10 times in succession.
- 4. High temperature scannable aluminum material obtainable by the process comprising the steps of:
- a) introducing a starting material comprising an alloy comprising the metals aluminum and scandium in a vacuum chamber, wherein the starting material is an AlMgMnScZr alloy consisting of 4.3 wt .-% magnesium, 0.7 wt .-% scandium, 0.3 wt .-% zirconium and 0.5% by weight of manganese, based in each case on the total weight of the alloy, the proportion of impurities in the total weight of the alloy being less than 0.5% by weight, the remainder being aluminum, the starting material being produced by the melt-spinning method,
- b) vacuum gases of the starting material at a vacuum of 0.1 to 10 -8 mbar and a temperature of 275 to 400 ° C over a period of 15 to 30 minutes,
- c) gassing the starting material with nitrogen for a period of 1 to 30 minutes, wherein the nitrogen has a water content of less than 1000 ppm, and
- d) final vacuum degassing of the starting material at a vacuum of 0.1 to 10 -8 mbar and a temperature of 275 to 400 ° C over a period of 15 to 30 minutes,
- 5. Use of a material according to aspect 4 for producing a welded, rolled, extruded or forged component for an aircraft, a vessel or a motor vehicle.
- 6. Welded, rolled, extruded or forged component for an aircraft, a vessel or a motor vehicle consisting of a material according to aspect 4.
Claims (9)
- Use of a method comprising the steps:a) introducing a primary material comprising an alloy comprising aluminium and scandium into a vacuum chamber, wherein the primary material is an AlMgMnScZr alloy consisting of 4.3 weight-% magnesium, 0.7 weight-% scandium, 0.3 weight-% zircon and 0.5 weight-% manganese, each relative to the overall weight of the alloy, wherein the content of contaminants of the overall weight of the alloy lies under 0.5 weight-%, the remainder being aluminium,b) vacuum degassing the primary material under a vacuum of 0.1 to 10-8 mbar and a temperature from 275 to 400°C over a period of 15 to 30 min,c) gassing the primary material with nitrogen over a period of 1 to 30 min, wherein the nitrogen contains a water content of less than 1000 ppm, andd) subjecting the primary material to final vacuum degassing under a vacuum of 0.1 to 10-8 mbar and a temperature from 275 to 400°C over a period of 15 to 30 min,for producing a high temperature-loadable aluminium material alloyed with scandium, wherein the method comprises another, additional step (e) in which the primary material is compacted in the vacuum chamber immediately after step (d).
- Use according to claim 1, wherein the high temperature-loadable aluminium material alloyed with scandium has improved extrusion moldability.
- Use according to claim 1 or 2, wherein the primary material was produced via the melt-spinning method.
- Use according to any of the preceding claims, wherein the primary material is present in the form of granules.
- Use according to any of the preceding claims, wherein steps (b) and (c) are performed 1 to 10 times in succession.
- Method for producing a high temperature-loadable aluminium material alloyed with scandium, comprising the steps:a) introducing a primary material comprising an alloy comprising aluminium and scandium into a vacuum chamber, wherein the primary material is an AlMgMnScZr alloy consisting of 4.3 weight-% magnesium, 0.7 weight-% scandium, 0.3 weight-% zircon and 0.5 weight-% manganese, each relative to the overall weight of the alloy, wherein the content of contaminants of the overall weight of the alloy lies under 0.5 weight-%, the remainder being aluminium, wherein the primary material was produced via the melt-spinning method,b) vacuum degassing the primary material under a vacuum of 0.1 to 10-8 mbar and a temperature from 275 to 400°C over a period of 15 to 30 min,c) gassing the primary material with nitrogen over a period of 1 to 30 min, wherein the nitrogen contains a water content of less than 1000 ppm, andd) subjecting the primary material to final vacuum degassing under a vacuum of 0.1 to 10-8 mbar and a temperature from 275 to 400°C over a period of 15 to 30 min,wherein the method comprises another, additional step (e) in which the primary material is compacted in the vacuum chamber immediately after step (d).
- High temperature-loadable aluminium material alloyed with scandium, obtainable by a method comprising the steps:a) introducing a primary material comprising an alloy comprising aluminium and scandium into a vacuum chamber, wherein the primary material is an AlMgMnScZr alloy consisting of 4.3 weight-% magnesium, 0.7 weight-% scandium, 0.3 weight-% zircon and 0.5 weight-% manganese, each relative to the overall weight of the alloy, wherein the content of contaminants of the overall weight of the alloy lies under 0.5 weight-%, the remainder being aluminium, wherein the primary material was produced via the melt-spinning method,b) vacuum degassing the primary material under a vacuum of 0.1 to 10-8 mbar and a temperature from 275 to 400°C over a period of 15 to 30 min,c) gassing the primary material with nitrogen over a period of 1 to 30 min, wherein the nitrogen contains a water content of less than 1000 ppm, andd) subjecting the primary material to final vacuum degassing under a vacuum of 0.1 to 10-8 mbar and a temperature from 275 to 400°C over a period of 15 to 30 min,wherein the method comprises another, additional step (e) in which the primary material is compacted in the vacuum chamber immediately after step (d).
- Use of a material according to claim 7 for producing a welded, rolled, extrusion molded or forged component for an aircraft, ship or motor vehicle.
- Welded, rolled, extrusion welded or forged component for an aircraft, ship or motor vehicle consisting of a material according to claim 7.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| DE102010032768A DE102010032768A1 (en) | 2010-07-29 | 2010-07-29 | High-temperature scandium alloyed aluminum material with improved extrudability |
| PCT/DE2011/001504 WO2012013185A1 (en) | 2010-07-29 | 2011-07-25 | Aluminium material which can be exposed to high temperatures, is alloyed with scandium and has improved extrudability |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| EP2598664A1 EP2598664A1 (en) | 2013-06-05 |
| EP2598664B1 true EP2598664B1 (en) | 2017-01-18 |
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| EP11761484.2A Active EP2598664B1 (en) | 2010-07-29 | 2011-07-25 | High temperature scandium-containing aluminium alloy with improved extrudability |
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| Country | Link |
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| US (1) | US20130143070A1 (en) |
| EP (1) | EP2598664B1 (en) |
| DE (1) | DE102010032768A1 (en) |
| WO (1) | WO2012013185A1 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP3456853A1 (en) | 2017-09-13 | 2019-03-20 | Univerza v Mariboru Fakulteta za strojnistvo | Manufacturing of high strength and heat resistant aluminium alloys strengthened by dual precipitates |
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| GB201112028D0 (en) | 2011-07-13 | 2011-08-31 | Gas2 Ltd | Fixed bed fischer tropsch reactor |
| EP2871642B1 (en) * | 2013-11-06 | 2019-08-28 | Airbus Defence and Space GmbH | Solar cell interconnector and manufacturing method thereof |
| US9945018B2 (en) | 2014-11-26 | 2018-04-17 | Honeywell International Inc. | Aluminum iron based alloys and methods of producing the same |
| DE202016001530U1 (en) * | 2016-03-09 | 2017-06-12 | TWI GmbH | Manganese-containing starting material produced by powder metallurgy for producing a light metal alloy and its use |
| CN107081507A (en) * | 2017-07-05 | 2017-08-22 | 合肥万之景门窗有限公司 | A kind of welding procedure of door and window aluminium alloy |
| CN114672686B (en) * | 2022-03-21 | 2022-10-28 | 华中科技大学 | Preparation method of additional nano-particle reinforced cast aluminum-lithium alloy |
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| US3619181A (en) | 1968-10-29 | 1971-11-09 | Aluminum Co Of America | Aluminum scandium alloy |
| US4104061A (en) | 1976-10-21 | 1978-08-01 | Kaiser Aluminum & Chemical Corporation | Powder metallurgy |
| US5211910A (en) * | 1990-01-26 | 1993-05-18 | Martin Marietta Corporation | Ultra high strength aluminum-base alloys |
| DK0918095T3 (en) | 1997-11-20 | 2003-07-21 | Alcan Tech & Man Ag | Process for preparing a structural component of an aluminum die casting alloy |
| DE19838017C2 (en) | 1998-08-21 | 2003-06-18 | Eads Deutschland Gmbh | Weldable, corrosion resistant AIMg alloys, especially for traffic engineering |
| DE10248594B4 (en) | 2001-12-14 | 2006-04-27 | Eads Deutschland Gmbh | Making aluminum sheet alloyed with scandium and zirconium and having high fracture resistance in e.g. aerospace applications, employs roller casting process and specified hot-working |
| US7648593B2 (en) * | 2003-01-15 | 2010-01-19 | United Technologies Corporation | Aluminum based alloy |
| EP1848835A2 (en) * | 2005-02-01 | 2007-10-31 | Timothy Langan | Aluminum-zinc-magnesium-scandium alloys and methods of fabricating same |
| US7875132B2 (en) * | 2005-05-31 | 2011-01-25 | United Technologies Corporation | High temperature aluminum alloys |
| US8778099B2 (en) * | 2008-12-09 | 2014-07-15 | United Technologies Corporation | Conversion process for heat treatable L12 aluminum alloys |
| US20100143177A1 (en) * | 2008-12-09 | 2010-06-10 | United Technologies Corporation | Method for forming high strength aluminum alloys containing L12 intermetallic dispersoids |
| US20110044844A1 (en) * | 2009-08-19 | 2011-02-24 | United Technologies Corporation | Hot compaction and extrusion of l12 aluminum alloys |
-
2010
- 2010-07-29 DE DE102010032768A patent/DE102010032768A1/en not_active Withdrawn
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- 2011-07-25 EP EP11761484.2A patent/EP2598664B1/en active Active
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| EP3456853A1 (en) | 2017-09-13 | 2019-03-20 | Univerza v Mariboru Fakulteta za strojnistvo | Manufacturing of high strength and heat resistant aluminium alloys strengthened by dual precipitates |
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| DE102010032768A1 (en) | 2012-02-02 |
| EP2598664A1 (en) | 2013-06-05 |
| WO2012013185A1 (en) | 2012-02-02 |
| US20130143070A1 (en) | 2013-06-06 |
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