Heat Treatment Optimization in Al-Cu-Mg-Si Alloys, with or without Prior Deformation
Abstract
:1. Introduction
2. Materials and Methods
3. Results and Discussion
4. Conclusions
- The greater the dwell time at 495 °C, the greater the percentage in weight of the transient states associated with the Al2Cu phase during natural ageing.
- Mg is easier to dissolve during the solution treatment than Cu, the latter needing more time.
- Precipitation of the Al7Cu2Fe phase is observed during natural ageing, its content being reduced with increasing dwell time at the solution temperature.
- Regardless of the dwell time at the solution temperature, the maximum hardness obtained during natural ageing only slightly exceeds 130 HV.
- The higher the ageing temperature, the faster the peak hardness is reached, but the lower its value. The ageing temperature that allows a higher hardness value to be obtained is 160 °C.
- The maximum hardness value obtained was 162 HV, after a solution treatment at 495 °C for 4 h and ageing at 160 °C for 50 h.
- During artificial ageing in the 160–180 °C range:
- The peak hardness values are reached more quickly.
- The hardness values exceed those achieved without prior deformation. However, this result is due to the hardness associated with the deformation, as the increase in hardness due to ageing was less than 20 HV in all cases.
- The maximum hardness values are the same regardless of the ageing temperature. The maximum hardness obtained was 168 HV when employing a dwell time of 8 h at 495 °C. The ageing time needed to obtain this hardness would be 6 h if this temperature were 180 °C, and 25 h if it were 160 °C.
- Ageing does not take place at 200 °C, a continuous reduction in hardness being produced due to the recovery softening of the material at this temperature.
Author Contributions
Conflicts of Interest
References
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Cu | Mg | Si | Fe | Ni | Al |
---|---|---|---|---|---|
4.84 | 1.56 | 0.75 | 0.18 | 0.12 | Rem. |
Crystalline Phases. | AsCast. | ST 4 h A 1000 h | ST 8 h A 1000 h | ST 24 h A 1000 h |
---|---|---|---|---|
Al (α) | 98.9 | 92.2 | 92.5 | 92.2 |
Mg2Si | 0.3 | 3.6 | 3.4 | 3.5 |
Al2Cu | 0.6 | 1.1 | 1.4 | 1.7 |
AlFe2 | 0.1 | 0.6 | 0.7 | 0.7 |
Cu3Al | 0.1 | 0.6 | 0.5 | 0.5 |
Al7Cu2Fe | - | 1.9 | 1.6 | 1.5 |
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Alvarez-Antolin, J.F.; Segurado-Frutos, E.; Neira-Castaño, H.; Asensio-Lozano, J. Heat Treatment Optimization in Al-Cu-Mg-Si Alloys, with or without Prior Deformation. Metals 2018, 8, 739. https://doi.org/10.3390/met8100739
Alvarez-Antolin JF, Segurado-Frutos E, Neira-Castaño H, Asensio-Lozano J. Heat Treatment Optimization in Al-Cu-Mg-Si Alloys, with or without Prior Deformation. Metals. 2018; 8(10):739. https://doi.org/10.3390/met8100739
Chicago/Turabian StyleAlvarez-Antolin, Jose Florentino, Elvira Segurado-Frutos, Hilario Neira-Castaño, and Juan Asensio-Lozano. 2018. "Heat Treatment Optimization in Al-Cu-Mg-Si Alloys, with or without Prior Deformation" Metals 8, no. 10: 739. https://doi.org/10.3390/met8100739