In-Depth Comparison of an Industrially Extruded Powder and Ingot Al Alloys
Abstract
:1. Introduction
2. Materials and Methods
2.1. Industrial Hot Extrusion and Annealing Heat Treatments
2.2. Hot Workability and Mechanical Properties
2.3. Microstructural Characterization
3. Results
3.1. Microstructure
3.1.1. Initial Microstructure
3.1.2. Microstructure after Extrusion
3.2. Industrial Hot-Extrusion Tests
3.2.1. Direct-Extrusion Press
3.2.2. Indirect-Extrusion Press
3.3. Mechanical Properties of Extruded Material
3.4. Hot-Compression Tests
Processing Maps
4. Discussion
5. Conclusions
- A density of 85% was obtained after cold isostatic pressing (green pellet) when processing Al powder. After hot extrusion, this density increased to about 95%, and after hot compression, we approached 100% of the theoretical density. The conventionally cast alloy AA 1050 had a theoretical density of 100% immediately after casting.
- In an industrial environment, it was found that the use of an induction furnace to heat the green pellet to extrusion temperature was not suitable because the oxides present on the surface of the powder grains limit the heating rate. The use of gas and electric furnaces is better and our recommendation.
- A better tensile strength of the consolidated material was achieved by direct extrusion, while ductility was better when indirect extrusion was used. Although the highest values of elongation at failure were obtained in the samples of the conventional alloy AA 1050, the tensile strength in these samples was about three times lower.
- Annealing of extruded Al powder did not significantly increase the ductility, while UTS and YTS decreased slightly.
- Hot workability of powdered material is not recommended at low strain rates. Surface cracking occurred during single-hit hot-compression tests at strain rates below 0.1 s−1. The yield stress of extruded Al powder was several times higher compared to the conventionally cast AA 1050 alloy. The calculated apparent activation energies for hot deformation for the material in the extruded state are 232 kJ mol−1 for Al 1080 powder and 158.6 kJ mol−1 for AA 1050.
- After annealing heat treatment at 300 °C for 20 h, the apparent activation energy for hot deformation decreased more for powdered Al and was calculated to be 209.7 kJ mol−1, while a slight change was observed for the alloy AA 1050 at 154 kJ mol−1.
- Optimum hot-forming conditions are at temperatures above 550 °C and strain rates above 1 s−1, based on the processing maps for strains 0.4 and 0.6.
Author Contributions
Funding
Acknowledgments
Conflicts of Interest
References
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Material | Si | Fe | Cu | Mg | Mn | O | Al |
---|---|---|---|---|---|---|---|
Al 1080 | 0.054 | 0.159 | 0.001 | 0.005 | 0.001 | 1.95 | base |
AA 1050 | 0.114 | 0.148 | 0.002 | 0.02 | 0.008 | - | base |
Billet Material | Al 1080 Powder | AA 1050 | ||
---|---|---|---|---|
Billet Mark | D1 | D2 | D3 | D4 |
Billet length/mm | 500 | 500 | 500 | 700 |
Ram speed/mm·s−1 | 3.5 | 2.1 | 1 | 5.7 |
Puller (bar) speed/m·s−1 | 0.062 | 0.035 | 0.017 | 0.1 |
Peak press pressure/MPa | 23 | 27.4 | 28.7 | 5.3 |
Press rest/mm | 50 | 50 | 50 | 130 |
Die furnace temperature/°C | 460 | 450 | 440 | 500 |
Container temperature/°C | 450 | 450 | 450 | 450 |
Billet temperature/°C | 460 | 450 | 445 | 460 |
Maximum bar temperature/°C | 587 | 570 | 555 | 560 |
Billet Material | Al 1080 Powder | ||
---|---|---|---|
Billet Mark | I1 | I2 | I3 |
Billet length/mm | 500 | 500 | 500 |
Ram speed/mm·s−1 | 7.1 | 6.2 | 3.9 |
Puller (bar) speed/m·s−1 | 0.118 | 0.082 | 0.052 |
Peak press pressure/MPa | 17.7 | 20.5 | 21.4 |
Press rest/mm | 50 | 50 | 50 |
Die furnace temperature/°C | 340 | 340 | 320 |
Induction furnace temperature/°C | 420 | - | - |
Container temperature/°C | 360 | 360 | 360 |
Billet temperature/°C | 420 | 340 | 320 |
Material | Annealing Time/h | Q/kJ·mol−1 | α/MPa−1 | n/- | A/s−1 |
---|---|---|---|---|---|
Al 1080 powder | As extruded | 232.08 | 0.027177 | 3.97 | 6.28 × 1011 |
1 | 252.5 | 0.028282 | 4.25 | 1.81 × 1015 | |
20 | 209.7 | 0.025506 | 3.99 | 9.03 × 1012 | |
Conventional AA 1050 | As extruded | 158.6 | 0.01572 | 6.89 | 2.87 × 1013 |
1 | 165.1 | 0.023924 | 6.28 | 1.90 × 1012 | |
20 | 154.0 | 0.023347 | 6.18 | 4.02 × 1011 |
Material | YTS/MPa | UTS/MPa | Strain/% | Reference |
---|---|---|---|---|
Al-4Y-4Ni (ultra-fine grains) | 394 | 422 | 16.3 | [2] |
Al-4Y-4Ni-0.9Fe (ultra-fine grains) | 470 | 478 | 7.2 | |
Al-graphite (0.5 wt.%) composite | 147 | 176 | 25 | [3] |
Al-graphite (1 wt.%) composite | 164 | 199 | 22 | |
Al powder + 10 vol.% TiC (10 µm) | 129 | 32 | [4] | |
Air atomized pure Al (100 µm) + γ-Al2O3 in matrix | 288 | [30] | ||
Mixture of large (1–10 µm) and ultra-fine (100 nm) Al grains | 390 + | 480 + | 17 | [31] |
Al powder (40 µm) + 20 vol.% SiC (70 µm) | 117 | 146 | 9.6 | [33] |
Al + 10 wt.% Mg powders (100 µm) | 137 | 147 | 7 | [32] |
Pure Al + Bi2O3 coated Al18B4O33 whiskers composite | 302 | 8.8 | [35] | |
Ultrafine Al-Mg (7.5 wt.%) grains (120 nm) | 600 + | 0.2–0.4 ‡ | [38] | |
AA 2214 + 26 wt.% SiC (3 µm) − forged | 290 | 446 | 3.1 | [36] |
AA 2214 + SiC (26 wt.%) − forged + T4 | 451 | 641 | 2.5 | |
Nanocrystalline bulk Al (48 nm) | 500 | 1 | [34] | |
Nanocrystalline bulk Al (56 nm) | 460 | 3 | ||
Nanocrystalline bulk Al (72 nm) | 279 | 5 | ||
AA 2618 + Al2O3 (20 vol.%)–as-cast | 347 | 361 | 0.5 | [37] |
AA 2618 + Al2O3 (20 vol.%)–forged | 373 | 453 | 1.3 | |
Al powder (10 µm) + 16 vol.% B4C (7 µm) | 160 | 198 | 18.7 | [6] |
Al nanoflake (0.5 µm) + 16 vol.% B4C (7 µm) | 260 | 364 | 4.8 | |
Al powder (31 µm) + 8.9 vol.% AlN (1 µm) | 180 | 332 | 3 | [20] |
Al powder (1.31 µm) + 13 vol.% AlN | 347 | 421 | 5 | [21] |
Al powder (<63 µm) + 12.7 vol.% AlN | 290 | 474 | 3 | |
Al powder (1.31 µm) + 2.3 vol.% Al2O3 | 242 | 296 | 10 | |
Al powder (ball milled) + 9.6 vol.% Al2O3 | 207 | 345 | 12 | |
Extruded Al 1080 powder (1 µm) | 243 | 253 | 8.6 | Present study |
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Bombač, D.; Cvahte, P.; Balog, M.; Kugler, G.; Terčelj, M. In-Depth Comparison of an Industrially Extruded Powder and Ingot Al Alloys. Metals 2020, 10, 1483. https://doi.org/10.3390/met10111483
Bombač D, Cvahte P, Balog M, Kugler G, Terčelj M. In-Depth Comparison of an Industrially Extruded Powder and Ingot Al Alloys. Metals. 2020; 10(11):1483. https://doi.org/10.3390/met10111483
Chicago/Turabian StyleBombač, David, Peter Cvahte, Martin Balog, Goran Kugler, and Milan Terčelj. 2020. "In-Depth Comparison of an Industrially Extruded Powder and Ingot Al Alloys" Metals 10, no. 11: 1483. https://doi.org/10.3390/met10111483