Influence of retrogression and re-aging treatment on corrosion behaviour of an Al–Zn–Mg–Cu alloy

Selective laser melting of Al-Zn-Mg-Cu: Heat treatment, microstructure and mechanical properties

Corrosion mechanism associated with T1 and T2 precipitates of Al–Cu–Li alloys in NaCl solution

The present study, using advanced Cs-corrected high-angle annular dark field – scanning transmission electron microscopy (HAADF-STEM), reports on a comprehensive investigation into the precipitate structures in an Al-Zn-Mg-Cu alloy aged at 150 ℃, including GP zones, η’ and η precipitates. In the nucleation stage, Zn atoms enrich on the {111}Al-planes abutting spherical Mg clusters that are approximately 3–6 nm in diameter. In the subsequent growth, the as-nucleated structures extend with an increasing diameter and a constant width along [111]Al and grow into platelet precipitates. η’ is proved to be a group of metastable structures existing in the transition from FCC Al to HCP MgZn2 (η). Some metastable structures are assembled by local-ordered rhombohedral units and orthorhombic units as building blocks. Subsequently, the precipitates evolve into η phases with stacking faults.

Precipitation in an Al-Zn-Mg-Cu alloy during isothermal aging: Atomic-scale HAADF-STEM investigation

Constitutive modeling, processing map establishment and microstructure analysis of spray deposited Al-Cu-Li alloy 2195

Mesoscopic structure control of spray formed high strength Al-Zn-Mg-Cu alloys

The aging response of various Al–Zn–Mg–Cu alloys was compared with the reinforced counterpart. The effects of aging temperature and time on the mechanical properties of these alloys, was also determined. Moreover, the effects of quenching rate from solution temperature, time between quench and aging, and heating rate to precipitation temperature were investigated. The study was executed by selecting two different heat treatments for each of three different aging temperatures: one without prior straining, and the other with 2% straining prior to aging to relieve stress. Room temperature tensile testing was conducted to determine these variations of aging on the strength of the spray formed Al–Zn–Mg–Cu alloys. The presence of SiC particles accelerated the aging kinetics of the alloys compared to the unreinforced counterparts. This difference in time to peak aging decreased with decreasing aging temperature. At uniform temperatures, differences for time to peak aging between unreinforced and composite alloys also existed in both the prestrained and unstrained condition. The difference was not as great in the prestrained state. The tensile strengths increased slightly with prestraining, but not significantly. Alloys containing silver maintained high strengths over silver-free counterparts when rapidly heated to precipitation temperatures above 120 °C. At slow heating rates, however, the silver-free alloys matched or were slightly higher than the strength of silver alloys, with increasing heating rate.

Aging response of Al-Zn-Mg-Cu spray formed alloys and their metal matrix composites

Hardening mechanisms of spray formed Al–Zn–Mg–Cu alloys with scandium and other elemental additions

Development of niobium aluminide-based composites with improved toughness using treated reinforcements

Corrigendum to “Hardening mechanisms of spray formed Al–Zn–Mg–Cu alloys with scandium and other elemental additions” [J. Alloys Compd. 416 (2006) 135–142]

M.F. Amateau

Papers

Mesoscopic structure control of spray formed high strength Al-Zn-Mg-Cu alloys

Aging response of Al-Zn-Mg-Cu spray formed alloys and their metal matrix composites

Hardening mechanisms of spray formed Al–Zn–Mg–Cu alloys with scandium and other elemental additions

Development of niobium aluminide-based composites with improved toughness using treated reinforcements

Corrigendum to “Hardening mechanisms of spray formed Al–Zn–Mg–Cu alloys with scandium and other elemental additions” [J. Alloys Compd. 416 (2006) 135–142]