Powder Aluminum Material

Abstract

This disclosure relates to the field of metallurgy, namely, to the composition of an aluminum-based heat-resistant alloy and a powder from it to be used for the production of parts using additive technologies. A new aluminum-based material has been created, which is intended for producing a powder and its utilisation in the additive production of various products, which has high processability at laser melting and high strength characteristics in the heat-treated state: the yield strength exceeding 400 MPa, the ultimate strength exceeding 470 MPa, and elongation at break of at least 4%. The powdered aluminum material contains copper, magnesium, manganese, cerium, silicon, zirconium and/or titanium, where the material contains thermally stable Al.sub.8Cu.sub.4Ce dispersoids with a size of less than 1 μm, which are formed at crystallisation rates of at least 10.sup.3 K/s, which contribute to the material strengthening under operating conditions at room and elevated temperatures.

Claims

1. A powder aluminum material based on an aluminum alloy, the powder aluminum material comprising copper, magnesium, manganese, cerium, silicon, and also zirconium and/or titanium, wherein the powder aluminum material has a component ratio of (wt. %): TABLE-US-00009 Copper 6.0 to 7.0 Magnesium 0.2 to 0.8 Manganese 0.3 to 1.0 Cerium 0.1 to 0.7 Silicon 2.8 to 3.7 Zirconium and/or titanium 0.45 to 0.9 Aluminum and impurities remainder, wherein the powder aluminum material comprises thermally stable Al8Cu4Ce dispersoids each having a size of less than 1 μm, the Al.sub.8Cu.sub.4Ce dispersoids being formed at crystallisation rates of at least 10.sup.3 K/s to contribute to hardening of the powder aluminum material.

2. The powder aluminum material of claim 1, wherein an aluminum-based powder alloy is obtained by atomising the powder aluminum material using a melt superheated to a temperature of at least 150° C. above a liquidus point, by flow of an inert gas, with an oxygen content of 0.01 to 0.8 wt. %.

3. The powder aluminum material of claim 2, wherein at least one element from an element group of H, N, O, and Ar is included in a powder alloy generated using the powder aluminum material based on a purity of the inert gas and on ambient factors influencing the melt, wherein one of: at least one of the H, N, 0, and Ar in an amount of up to 1 wt. % is present in the powder alloy; or at least one of the H, N, O, or Ar in an amount of between 0 to 0.5 wt. % is present in the powder alloy.

4. The powder aluminum material of claim 3, wherein the inert gas is nitrogen or argon.

5. The powder aluminum material of claim 4, wherein the powder aluminum material further comprises D.sub.50 in a range of 5 to 150 μm, the powder aluminum material being used in additive technologies.

6. The powder aluminum material of claim 3, wherein the powder aluminum material further comprises D.sub.50 in a range of 5 to 150 μm, the powder aluminum material being used in additive technologies.

7. The powder aluminum material of claim 2, wherein the powder aluminum material further comprises D50 in a range of 5 to 150 μm, the powder aluminum material being used in additive technologies.

8. The powder aluminum material of claim 2, wherein the inert gas is nitrogen or argon.

9. The powder aluminum material of claim 1, wherein the powder aluminum material further comprises D.sub.50 in a range of 150 μm, the powder aluminum material being used in additive technologies.

10. The powder aluminum material of claim 9, wherein the powder aluminum material is used to generate a product having an ultimate strength of at least 450 MPa at room temperature after quenching and artificial ageing.

Description

BRIEF DESCRIPTION OF THE DRAWINGS

[0026] The figures show:

[0027] FIG. 1: Images of sample structures for alloys Nos 1 to 8 from Example 1, obtained by optical microscopy, showing that the level of porosity of the materials does not exceed 0.5 vol. % and that there are no cracks.

[0028] FIG. 2: Selective laser melting (SLM) process and specimens from the claimed AlCuCe alloy for testing the materials from Example 1.

[0029] FIG. 3: Typical image of the microstructure of a material from the proposed AlCuCe alloy in a scanning electron microscope from Example 1 (A) and a map of the distribution of alloying elements (B) from Example 1.

[0030] FIG. 4: Results of X-ray phase analysis of the AlCuCe material from Example 1 showing the phase composition of the alloy after heat treatment.

[0031] FIG. 5: A typical image of the microstructure of a material from the proposed AlCuCe alloy in a transmission electron microscope from Example 1 showing the presence of a strengthening thermally stable Al.sub.8Cu.sub.4Ce phase and a map of the distribution of alloying elements (B).

[0032] FIG. 6: Typical image of the microstructure of the proposed AlCuCe alloy in a scanning electron microscope (A) and maps of the distribution of alloying elements (B) showing that the size of silicon particles after heat treatment does not exceed 10 μm (Example 2).

[0033] FIG. 7: Graphs of the dependence of the ultimate strength (A), the yield strength (B), the elongation at break (C) on the temperature of tensile tests in accordance with GOST 9651-84 showing an increased level of mechanical properties of the proposed alloy in comparison with the prototype when tested within the temperature range from the room temperature up to 350° C. (Example 3).

[0034] FIG. 8: A rupture strength curve of the AlCuCe material after heat treatment showing a good level of mechanical properties of the material under cyclic loading conditions at a temperature of 200° C. in a mutually perpendicular direction (Example 3).

DETAILED DESCRIPTION

Example 1

[0035] Powders of aluminum alloys of various compositions in accordance with Table 1 were produced by gas atomisation in the nitrogen environment with a controlled content of oxygen.

TABLE-US-00002 TABLE 1 No Al Cu Mg Zr Ti Ni Mn Ce Si V 1 Base 6.00 0.2 0.60 0.20 — 0.37 0.70 3.7 — 2 6.00 0.3 0.50 0.00 — 0.30 0.10 3.0 — 3 6.20 0.2 0.60 0.18 — 0.37 0.60 2.9 — 4 6.30 0.75 0.45 0.31 — 0.56 0.22 3.0 — 5 6.50 0.5 0.10 0.45 — 0.48 0.30 3.7 — 6 6.90 0.8 0.20 0.60 — 0.10 0.40 3.2 — 7 7.00 0.6 0.00 0.90 — 0.85 0.50 3.7 — 8 7.00 0.1 0.30 0.10 — 0.60 0.10 2.8 — Pro- 5.90 2.6 0.15 — 0.1 0.50 — 0.1 0.15 to- type

[0036] The melt was prepared in a gas-heated furnace. For preparation, aluminum of at least A7 grade in accordance with GOST 11069-2001, copper of the M1 grade in accordance with GOST 859-2001, electrolytic cerium of the TsEO grade, magnesium of the MG90 grade in accordance with GOST 804-93, silicon of the 4001 grade in accordance with GOST 2169-69, and binary master alloys of the rest of the elements were used. After preparing the melt and testing its chemical composition, the alloy was overheated to the temperature of 870 to 920° C. and then atomised in nitrogen with the oxygen content of 0.1% to 0.8% with the purpose of controlling the oxygen content in the powder and preventing its ignition in the process of dispersion.

[0037] During the atomisation process, the temperature was not allowed to drop below the value of (T.sub.liquidus+100° C.), since it had been found that below this temperature, intermetallic compounds can form in the powder due to local cooling of the melt upon its contact with the nozzle and elements of the metal discharge launder, which are the cause of the process disruption (nozzle clogging, disruption of the chemical composition homogeneity and the powder structure, etc.).

[0038] The resulting powders were screened to separate the fraction of D.sub.50=45 ±5 μm.

[0039] The selective laser melting (SLM) process for the obtained powder was performed on an SLM 280HL selective laser melting system in a nitrogen atmosphere, by varying the energy-speed printing parameters (laser power, scanning speed, track-to-track distance) in order to form a structure without hot cracks and with a controlled porosity level. The porosity of the synthesised material was determined on cube-shaped samples by the metallographic method using a Carl Zeiss Neophot optical microscope, for which the microsections were prepared using a standard technology and without any additional etching of the samples.

[0040] The microstructure of the material was studied using a Tescan Mira 3 scanning electron microscope and a JEOL 2100 transmission electron microscope. The phase composition was studied using a Brucker Advance D8 X-ray diffractometer.

[0041] The results of the studies of the material structure by optical microscopy are shown in FIG. 1. According to the data obtained, the porosity of the materials for the most optimal modes did not exceed 0.5 vol. %.

[0042] Based on the parameters ensuring the lowest porosity, products were made in the form of blanks for samples for tensile tests in accordance with GOST 1497-84 and GOST 9651-84 (FIG. 2). Then the blanks were heat treated: heating to a temperature of 5° C. below the melting point, holding for at least 2 hours, followed by quenching in cold water, and artificial ageing at 170° C.

[0043] The results of the study of the phase composition and the material structure are given in FIGS. 3, 4, and 5.

[0044] According to the results obtained, the material structure is an aluminum matrix with homogeneously distributed dispersed phases, which, according to the XRD results, are silicon (Si) and Al.sub.2Cu and Al.sub.8Cu.sub.4Ce dispersoids. A distinctive feature of the material is the size of the Al.sub.8Cu.sub.4Ce nanodispersed phase, which does not exceed 1 μm, which occurs due to the rapid crystallisation of the material (at a rate of at least 10.sup.3 K/s) during the SLM process (FIG. 4). This phase is characterised by dimensional stability before and after heat treatment, which indicates a high level of performance characteristics of the provided AlCuCe material.

[0045] The results of tensile tests of the samples at room and elevated (250° C.) temperatures are given in Table 2.

TABLE-US-00003 TABLE 2 Results of tests of mechanical properties Ultimate tensile Ultimate tensile Yield Yield strength at strength at strength at strength at No 20° C., MPa 250° C., MPa 20° C., % 250° C., % 1 470 220 390 210 2 475 225 406 208 3 485 225 424 200 4 483 227 416 210 5 478 220 425 215 6 480 225 427 219 7 465 215 415 190 8 450 215 390 188 Prototype 400 200 345 159

[0046] Table 2 shows that the proposed material in the claimed range is characterised by an increased strength and yield compared to the prototype. Additional strengthening is ensured due to the presence of nanosize thermally stable hardening dispersoids in the material structure. In turn, the size of the silicon phase, which does not exceed 10 μm, allows maintaining the high plasticity characteristics of the alloy.

[0047] Thus, the achieved level of mechanical properties makes it promising to use the proposed material for production of parts of loaded elements operating under conditions of process and operational heating as analogues of casting and deformable materials.

Example 2

[0048] Powders of experimental compositions were obtained by a technology similar to Example 1. The chemical composition of the powders obtained is shown in Table 3. The composition of the alloys varied mainly in terms of the silicon content.

TABLE-US-00004 TABLE 3 Chemical composition of experimental alloys No Al Cu Mg Zr Ti Mn Ce Si A Base 6.00 0.22 0.58 0.5 0.5 0.65 2.30 B 6.00 0.3 0.53 0.43 0.40 0.66 2.50 C 6.04 0.20 0.50 0.40 0.40 0.70 2.83 D 6.10 0.25 0.48 0.45 0.44 0.66 2.9 E 6.13 0.34 0.55 0.46 0.41 0.68 3.7 F 6.07 0.27 0.49 0.40 0.45 0.63 3.8 G 6.10 0.31 0.49 0.40 0.45 0.63 3.93

[0049] The printing process was implemented using the SLM Solutions 280 HL selective laser melting equipment. Printing was performed in a range of modes to select an optimal combination of synthesis parameters that ensure the minimum level of porosity and the absence of hot cracks. The structure of the printed samples was studied using an optical microscope similarly to Example 1. The material microstructure was analysed using a Tescan Vega 3LMH SEM scanning electron microscope with an attachment for energy dispersive analysis.

[0050] The porosity measuring results are shown in Table 4.

TABLE-US-00005 TABLE 4 Results of the study of AlCuCe material structure No Porosity, vol. % Macrodefect presence A 0.55 Cracks B 0.49 Cracks C 0.25 None D 0.30 None E 0.27 None F 0.4 None G 0.4 None

[0051] As can be seen from the results, cracks were found on alloys A and B, which were caused by poor casting properties of the material due to the low silicon content. The porosity of alloys from C to G obtained under optimal modes did not exceed 0.5 vol. %. Hot cracks are caused by an insufficient amount of silicon, which is the result of small eutectics amount. Therefore, in order to ensure the printability, it is preferable to maintain the silicon content of at least 2.8 wt. %.

[0052] The developed most optimal parameters were used to produce cylindrical blanks for tensile test samples at room temperature. The ready cylinders were heat treated and quenched at a temperature of 5° C. below the melting point and artificial ageing for maximum strength. Then the blanks were machined to be used as tensile test samples in accordance with GOST 1497-84. The tests were performed on an MTS Criterion testing system. The test results are given in Table 5.

TABLE-US-00006 TABLE 5 Mechanical properties of tension test samples in accordance with GOST 1497-84 in the XY temper after quenching and artificial ageing (average values) Ultimate tensile Yield Elongation Alloy strength, MPa strength, MPa at break, % C 470 400 5.1 D 482 405 5.2 E 465 400 7.0 F 440 391 7.0 G 445 375 9.4

[0053] It can be seen from the results that an increased silicon content in F and G alloys leads to a decrease in the strength of the AlCuCe material, which is caused by the partial incorporation of copper into the composition of the silicon phase and, as a consequence, a decrease in its content in the solid solution. In turn, in alloys C, D, and E, the size of silicon particles does not exceed 10 μm, and materials obtained after quenching and artificial ageing for maximum strength are characterised by a combination of a high ultimate strength (at least 450 MPa) and plasticity at a room temperature and can be recommended to replace the known cast and wrought alloys of the Al—Cu system.

Example 3

[0054] An aluminum alloy powder according to Table 6 was obtained by atomising from a temperature exceeding the liquidus point of the alloy by 150° C. (to prevent the precipitation of primary intermetallic compounds in the melt) in a nitrogen atmosphere with the addition of oxygen in an amount of 0.3%, where the content of the chemical elements was controlled during their atomising in the melt:

TABLE-US-00007 TABLE 6 Chemical composition of melt before atomising No Al Cu Mg Zr Ti Ni Mn Ce Si 3 base 6.20 0.2 0.60 0.18 — 0.37 0.60 2.9

[0055] The resulting powder passed the standard screening procedure to obtain a fraction of +15/−63 μm with D.sub.50=45±2 μm.

[0056] The chemical analysis of the resulting powder was determined by atomic emission spectroscopy; the gas content was determined using a gas analyser in a G8 Galileo system. According to the analysis results, the composition of the obtained powder corresponded to the melt composition, while the oxygen content was 0.038 wt. % and the nitrogen content was less than 0.0001 wt. %.

[0057] The process of selective laser melting (SLM) of the obtained powder was implemented on an SLM Solutions 280HL selective laser melting system in a nitrogen atmosphere under the following energy-speed printing parameters: scanning speed of 200 to 400 mm/s, laser power of 250 to 350 W, track-to-track distance of 0.15 to 0.20 mm at the maximum layer thickness of 50 μm. The material was synthesised with an additional heating of the platform at a temperature not exceeding 160° C.

[0058] Based on the above parameters, cylindrical blanks were produced as products to be used as samples for tensile tests at room and elevated temperatures in accordance with GOST 1497-84 and GOST 9651-84, respectively.

[0059] After the completion of the printing process, the products were heat treated: heating to a temperature of 5° C. below the melting point, holding for at least 2 hours followed by quenching in cold water, artificial ageing at the temperature of 170° C., and also machining with the purpose of obtaining test samples.

[0060] The test results are given in Table 7.

TABLE-US-00008 TABLE 7 Mechanical properties of materials Test Ultimate tensile Yield strength Elongation temperature, ° C. strength σ.sub.B, MPa σ.sub.0, 2, MPa at break δ.sub.5, % 20 485 424 7.0 150 371 357 16.5 200 317 315 15.0 250 225 219 16.3 300 133 131 34.8 350 59 58 34.0

[0061] As can be seen from Table 7, the AlCuCe material proposed is able to maintain sufficiently high strength characteristics at elevated temperatures.

[0062] FIG. 7 shows graphs of changes in the level of mechanical properties under tensile strain (tensile strength, yield strength, and elongation) of the AlCuCe alloy in comparison with the prototype (US patent 2017/0016096 A1, the properties are given for a material with a chemical composition similar to that in Example 1). Compared with the prototype, the proposed AlCuCe material has increased strength characteristics in the temperature range of 20 to 350° C.

[0063] Further, with the specified characteristics, products were produced in the form of cylinders with a diameter of 18 mm and a length of 113 mm for rupture tests in accordance with GOST 10145-81. The tests were performed on an ATS Creep Tester at the temperature of 200° C.

[0064] Based on the results obtained, a creep rupture curve was built for the provided material (FIG. 8). It can be seen from the test results that the material has good ultimate creep rupture strength values based on 100 hours (100 MPa), and is promising for use in operating conditions under the combined effects of cyclic loads and elevated temperatures.