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
• • 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
  • B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
• • 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
  • B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
  • B22F10/20—Direct sintering or melting
  • B22F10/28—Powder bed fusion, e.g. selective laser melting [SLM] or electron beam melting [EBM]
• • 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
  • B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
  • B22F10/60—Treatment of workpieces or articles after build-up
  • B22F10/64—Treatment of workpieces or articles after build-up by thermal means
• • 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
  • B22F12/00—Apparatus or devices specially adapted for additive manufacturing; Auxiliary means for additive manufacturing; Combinations of additive manufacturing apparatus or devices with other processing apparatus or devices
  • B22F12/20—Cooling means
• • 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
  • B22F3/10—Sintering only
  • B22F3/1017—Multiple heating or additional steps
  • B22F3/1028—Controlled cooling
• • 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
  • B22F3/24—After-treatment of workpieces or articles
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B33—ADDITIVE MANUFACTURING TECHNOLOGY
  • B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
  • B33Y10/00—Processes of additive manufacturing
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B33—ADDITIVE MANUFACTURING TECHNOLOGY
  • B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
  • B33Y70/00—Materials specially adapted for additive manufacturing
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B33—ADDITIVE MANUFACTURING TECHNOLOGY
  • B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
  • B33Y80/00—Products made by additive manufacturing
• • 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
  • C22F1/002—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working by rapid cooling or quenching; cooling agents used therefor
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
  • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
  • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
  • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
  • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
  • C22F1/047—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with magnesium as the next major constituent
• • 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
  • B22F3/24—After-treatment of workpieces or articles
  • B22F2003/248—Thermal after-treatment
• • 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
  • B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
  • B22F2998/10—Processes characterised by the sequence of their steps
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
  • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
  • B23K26/00—Working by laser beam, e.g. welding, cutting or boring
  • B23K26/34—Laser welding for purposes other than joining
• • 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
  • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
  • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
  • Y02P10/00—Technologies related to metal processing
  • Y02P10/25—Process efficiency

Definitions

• the present invention relates to a high strength aluminium alloy suitable for use for additive manufacturing, but also applicable to other processes, in particular to other rapid solidification manufacturing processes.
• AM Additive Manufacturing
• AM additive Manufacturing
• AM is not only limited to those technologies, while the present invention can be used not only for AM technologies but also for other rapid solidification manufacturing processes such as Laser Cladding (LC), Thermal Spray (TS), Spark Plasma Sintering (SPS), Gas Atomisation (GA) and Melt Spinning (MS).
• LC Laser Cladding
• TS Thermal Spray
• SPS Spark Plasma Sintering
• G Gas Atomisation
• MS Melt Spinning
• the AM processes use a laser beam, an electron beam or an electric arc as the energy source, with the source precisely controlled by either a CNC driven system or galvanometer based mirror scanning system.
• a laser beam an electron beam or an electric arc
• successive layers can be built up in turn by moving the energy source point by point and step by step according to respective cross- sectional forms corresponding to notional slices of a required component to be manufactured. That is, the component is built up by repeating the layer by layer process and attaining bonding between consecutive layers along a build direction.
• components made from these alloys require solution treatment after fabrication to achieve the required properties, which increases both the lead time and cost for industrial production.
• Other high strength aluminium alloys such as the 2xxx and 7xxx series wrought alloys that are commonly used in aerospace fields, cannot be easily fabricated by AM technologies due to their high solidification crack susceptibility during AM processing. With the presence of large amounts of copper, magnesium and zinc in such alloy systems, the solidification range is expanded, which in turn increases the hot tearing susceptibility.
• the present invention seeks to provide a high strength aluminium alloy suited for use in AM processes, but also applicable to other rapid solidification manufacturing processes.
• an Al-Mn-Sc based alloy wherein the Al-Mn-Sc based alloy has from 2.01 wt% to 15.0 wt% manganese, from 0.3 wt% to 2.0 wt% scandium, with a balance apart from minor alloy elements and incidental impurities of aluminium.
• the invention provides a method for producing components of an aluminium based alloy, wherein the method uses an AM or other rapid solidification process to produce a component by melting and then rapidly solidifying the aluminium based alloy, and wherein the Al-Mn-Sc based alloy has from 2.01 wt% to 15.0 wt% manganese, from 0.3 wt% to 2.0 wt% scandium, with a balance apart from minor alloy elements and incidental impurities of aluminium.
• the manganese level preferably is from 2.5 wt% and 8 wt%, and more preferably between 3 wt% and 5 wt%.
• the scandium level preferably is from 0.4 wt% and 1.5 wt%, and more preferably from 0.6 wt% to 1.2 wt%.
• the Al-Mn-Sc based alloy of the invention preferably in the form of a suitable grade of powder, can be used to manufacture components by additive manufacturing or other rapid solidification manufacturing processes.
• the components may be directly age hardened to achieve simultaneously optimised properties and elimination of residual stresses generated during the manufacturing fabrication process.
• the Al-Mn-Sc based alloy starting material includes higher manganese and scandium contents than in conventional aluminium alloys, and parts made from the alloy of the invention enable the provision of superior mechanical properties under both room temperature and elevated temperature conditions.
• the alloy of the invention in addition to preferably being comprised of 2.01 -15.0 wt% manganese and 0.3-2.0 wt% scandium, also may have further alloy constituents comprising up to 6.0 wt% magnesium, up to 4.0 wt% zirconium, other elements able to substitute for or are complementary elements to any of aluminium, manganese, scandium, magnesium and zirconium, and combinations of two or more of the further alloy constituents.
• the Al-Mn-Sc based alloy of the invention can be used to directly manufacture structural components for a wide variety of industrial applications by either AM processing or by use of another rapid solidification manufacturing processes.
• the components manufactured from the alloy of the invention can be subjected to a simple artificial ageing treatment directly without solution treatment to achieve optimum properties.
• the components are able to exhibit high strength and thermal stability properties that can further enhance the application potential for AM fabricated aluminium parts.
• SCALMALLOY® sought to further strengthen the base alloy by utilising the high cooling rate advantage of AM processes.
• the Al-Mn-Sc based alloy of the invention is not known to have been proposed or used previously for AM processes or for other rapid solidification manufacturing processes. Elimination of magnesium, or substantial reduction in the magnesium content, enables the present invention to effectively lower the risks of evaporation and resultant high porosity problems. Introducing manganese to the aluminium alloys has no known corrosion or evaporation issues during AM or other rapid solidification manufacturing processes. By virtue of the high cooling rate derived from the manufacturing process, the use of high amounts of manganese and scandium is enabled by highly improved solubility.
• the manganese in the alloy of the invention plays a major role in solid solution strengthening, while scandium forms thermally stable L12 structured nano-sized precipitates after post heat treatment that can strengthen the alloy significantly and maintain the advanced mechanical properties up to high temperatures.
• manganese has a higher solid solution strengthening effect than magnesium on a wt% basis [6].
• the decomposition and formation of a high volume fraction of nano-sized AbSc precipitates during ageing can remarkably strengthen the alloy of the invention.
• AbSc precipitates have a face-centred cubic structure and maintain extremely low lattice mismatch and high coherency with the aluminium matrix, and the low diffusion rate of scandium impedes precipitate coarsening at elevated temperatures.
• the high mismatch strain and antiphase boundary energy of AbSc precipitates contributes to the high strength of the alloy of the invention by pinning the grain boundaries and inhibiting dislocation movement.
• the alloy of the invention also has been found to demonstrate superior corrosion resistance, weldability, thermal stability and mechanical properties after AM processing or other rapid solidification processing.
• the properties of the Al-Mn-Sc based alloy of the invention can be further improved by introducing other, substitutive or complementary, alloying elements to the alloy of the invention.
• alloying elements For example, at least one of silicon, zinc, magnesium, copper, nickel, cobalt, iron, silver, chromium, lithium, vanadium, titanium, calcium, tantalum, zirconium, hafnium, yttrium, ytterbium and erbium may be added to the alloy of the invention.
• the benefits offered by one or more of these elements are (i) solid solution strengthening; (ii) grain refinement effect; (iii) grain structure control; (iv) further dispersion strengthening or precipitation strengthening; or (v) a combination of these benefits.
• the content of the above alloying elements should be less than 4 wt% individually and, at most, 15 wt% in total.
• alloying elements including at least one of chromium, vanadium, titanium, tantalum, zirconium, hafnium and yttrium may be further added into the Al-Mn-Sc based alloy of the invention for improved high temperature stability.
• These alloying elements have an exceptionally low diffusion coefficient in aluminium, thus low diffusion rates and high particle coarsening resistance are expected at elevated temperatures.
• These alloying elements also have a high tendency to segregate and surround the AbSc precipitates to form a protective shell that can stabilize the AbSc precipitates from coarsening during exposure at elevated temperatures.
• the content of the above alloying elements also should be less than 4 wt% individually and, at most, 15 wt% in total.
• the Al-Mn-Sc based alloy of the invention may be used for manufacture of mechanical device components, and also as a base material for manufacturing composites admixtures of metallic or non-metallic materials through either in-situ or ex-situ reactions.
• the alloy of the invention can be made into semi-finished products like powders, wires and other forms for other production purposes.
• any possible energy source or combination of sources can be used, such as lasers, electron beam sources, plasmas, and electric arc sources, or suitable chemical reaction, or conductive or inductive process associated with rapid solidification technologies.
• the cooling rate within the manufacturing process should be such as to achieve a supersaturated solid solution for the main elements in order to maintain the properties of the fabricated components.
• the preferred cooling rate within the manufacturing process chain is in excess of 100 K/s.
• the cooling nature within the process can be directly from the manufacturing process itself, as in AM technologies or from other subsidiary processes like using water, liquid nitrogen or any other suitable cooling medium.
• the invention includes a post-heat treatment after SLM in which a component manufactured by the AM process, using the Al-Mn-Sc based alloy of the invention is subjected to heating, preferably in a single heat treatment process, to a temperature range between 200 °C and 500 °C for an accumulated time of between 0.10 h and 100 h.
• heat treatments with similar temperature-corrected times, multistep treatments or treatments under special environments are also applicable. This can include hot isostatic pressing (HIP) under appropriate pressure.
• HIP hot isostatic pressing
• a direct ageing treatment by simple direct ageing treatment without a separate solution treatment is most preferred, with this being another point of difference from other age hardening systems.
• cooling may range from slow furnace cooling to a rapid water quench cooling.
• the residual stresses generated due to high cooling rates during the AM manufacturing process can effectively be released by the heat treatment.
• decomposition of the supersaturated solid solution resulting from the high cooling rates generates precipitation of a large volume fraction of nano-sized particles or other dispersions, thereby greatly improving mechanical properties of the components produced by the AM process.
• the AM manufacturing process using the Al-Mn-Sc based alloy of the invention, some other beneficial control aspects are preferred. For example, by carefully adjusting the parameters (such as the laser type, laser parameters, scan strategy, substrate temperature, etc) in the AM technologies to maintain a suitable cooling rate and better processability, using protective gas environments to protect the fabricated parts from oxidation, removing the so-called smoke or spatter occurring during the AM process, or any other necessary controls for AM techniques and other rapid solidification techniques are expected to further improve the properties of the fabricated products.
• the parameters such as the laser type, laser parameters, scan strategy, substrate temperature, etc
• Example 1 The production of components of Al-Mn-Sc based alloys according to the present invention, by AM processing, was simulated using two alloy compositions.
• the first Al-Mn-Sc based alloy had a composition of AI-4.18Mn-2Mg- 0.9Sc-0.18Zr (wt%), while that for the second alloy had a composition of AI-3Mn- 1.5Mg-1 Sc-0.05Zr (wt%).
• These alloys were produced by melting master alloys of the compositions AI-60Mn, AI-50Mg, AI-2Sc and AM OZr (all wt%) in a resistively heated furnace at 800 °C, casting the successive melts and cooling the castings at a solidification cooling rate of approximately of 10 3 K/s.
• the cast alloys were cut into 5 mm thick samples and the samples were then ground, using abrasive paper to maintain the same surface roughness.
• the samples so produced were placed onto the substrate of a commercial EOSINT M280 SLM machine for laser scanning.
• a total of 30 laser scans were conducted on the ground sample surface to generate parallel adjacent melt pools without added powder, resulting in a scanned area of approximately 3mm by 18mm.
• the laser scan process was conducted with a laser power of 370 W, a scan speed of 500 mm/s, a spot size of 0.1 mm and a hatch distance of 0.1 mm.
• the samples were aged in a salt bath at 300 °C for various times up to 168 hrs. Samples then were cut using a low speed saw and subsequently mounted to reveal the melt pools on a cross-section for following investigations.
• Samples for microstructure observations and microhardness testing were prepared according to standard metallography sample preparation methods.
• the Vickers hardness was measured within the melt pool cross-section area using a Duramin A300 hardness tester with 0.5 Kg load for 10s.
• Backscattered electron micrograph (BSE) images of the cross-sectional area were obtained on a JEOL 7001 FEG scanning electron microscope (SEM). The following characteristics were obtained: a) The maximum hardness achieved for the first alloy AI-4.18Mn-2Mg-0.9Sc-0.18Zr after ageing at 300 ° C for 10 hrs was 186.3 ⁇ 2 HVo.s; and
• Example 2 Prism type samples were produced by SLM fabrication, from gas atomised powder with a wt% composition of AI-4.52Mn-1 32Mg-0.79Sc 0.74Zr. The samples were produced on an EOSINT M290 commercial SLM machine, with a laser power of 370 W, scanning speed of 1000 mm/s, hatch distance of 0.1 mm and layer thickness of 30 pm. The samples were built on a 6061 aluminium alloy substrate from which they were removed by electric discharge machining (EDM) cutting. Some of the samples were heat treated in a salt bath at 300 ⁇ 2 °C for 5 hrs and all samples, with and without heat treatment, were then machined into tensile samples of the geometry shown in Figure 3, according ASTM E8M.
• EDM electric discharge machining
• Figure 1 is a BSE image showing hardness indentations in a sample of the second Al-Mn-Sc based alloy
• Figure 2 provides a plot showing the development of hardness with ageing time for each of the first and second Al-Mn-Sc based alloys
• Figure 3 is a schematic illustration of tensile sample geometries, in accord with ASTM E8M;
• Figure 4 shows engineering stress/strain curves of non-heat treated samples, as produced by SLM fabrication, and of heat treated samples.
• Figure 1 shows the cut surface, of a sample of the second Al-Mn-Sc based alloy, as revealed by metallographic preparation in a backscattered electron micrograph (BSE) image.
• the lower zone of the image shows the microstructure of the casting of the second alloy, while the upper zone shows the microstructure of the rapidly solidified melt pool produced by remelting of the alloy by laser scanning.
• the hardness measurements were taken in the upper, remelted zone.
• Figure 1 shows clearly that the upper zone resulting from the laser remelted melt pool is different compared with the initial cast zone, as no white needle or rod shaped primary A Mn or A Sc type precipitates can be observed. This makes clear that manganese and scandium have been successfully trapped within the aluminium matrix after the very fast cooling laser remelting process and a supersaturation status has been achieved.
• the Al-Mn-Sc based alloys of the invention show very promising properties and a high potential for application in a wide range of structural, industrial, engineering, aerospace and transportation components made by the AM process, or by other rapid solidification manufacturing processes.
• Figure 3 shows appropriately produced tensile samples from which the stress/strain curves of Figure 4 were derived.
• the yield strength of 427 MPa for the as fabricated (non-heat treated) samples itself is excellent, although the markedly enhanced yield strength of 577 MPa for the heat treated samples highlights the potential for the alloys of the present invention.
• the most favourable yield strength quoted for heat treated SCALMALLOY® is believed to be in the range of 459 to 479 MPa (see www.citim.de/en/metal-additive-manufacturina).
• the alloy benefits from the slow diffusion rates referred to earlier herein for both scandium and manganese, as well as certain other added elements such as zirconium. These slow rates facilitate the ability of the alloy after high cooling rates with thermal cycling to undergo precipitation hardening by precipitation of thermally stable nano-sized precipitates or dispersoids. With manganese this is possible from the lower effective limit of 2.01 wt%, up to the relatively high upper limit of 15.0 wt%, without undesirable precipitate coarsening, such as can tend to occur at levels of manganese addition above 15 wt%.
• the alloy also is characterised by enhanced property development achievable on the basis of a simple heat treatment, without a requirement for solution treatment as in the complex heat treatment regimes required for some other precipitation hardenable aluminium alloys.
• the simple heat treatment which preferably involves only a single stage operation, effectively doubles as a stress relieving step and precipitation hardening heat treatment.
• the heat treatment can be conducted before or after a resultant component manufactured by the process is cut from the build platform on which it is built up.
• Example 1 and Figures 1 and 2 show the suitability of the alloy for use in an alternative rapid solidification process.
• the component can be scanned by an energy source such as a laser or electron beam to achieve melting of a scanned region of the surface of the component, with the body of the component then providing a heat sink giving rise to rapid solidification to enhance the properties of the alloy of the scanned surface region.
• This includes surface treatments such as laser cladding or repair of components using the Al-Mn-Sc based alloy of the invention as part of the component and/or deposited surface materials.
• Li RD Wang MB, Yuan TC, Song Bo, Chen C, Zhou KC, Cao P:“Selective laser melting of a novel Sc and Zr modified AI-6.2 Mg alloy: Processing, microstructure, and properties”, Powder Technology 319 (2017) 117-128.

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