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In order to improve the corrosion and heat resistance of Al-Mg-Si alloy conductor materials, Ce, Sc, Y and Zr were added in Al-Mg-Si alloy to regulate the microstructure. The Al-Mg-Si-Ce-Sc-Y alloy was designed with excellent pitting and intergranular corrosion resistance by obtaining the micron-sized Fe-containing second phase with a lower potential difference to Al matrix, more dispersed grain boundary precipitates with a higher proportion of Si particles, narrower width of PFZ and ideal distribution of intergranular precipitates. The Al-Mg-Si-Ce-Sc-Y alloy also maintained higher hardness, strength and electrical conductivity after overaging and annealing and the corrosion/heat resistance mechanisms were proposed. • The corrosion and heat resistance of Al-Mg-Si alloy conductors were further enhanced. • The mechanisms of pitting and intergranular corrosion mechanisms in Al-Mg-Si alloys were proposed. • The microalloying of Ce，Sc and Y in Al-Mg-Si alloys with high electrical conductivity was established. [ABSTRACT FROM AUTHOR]

In the present work, laser shock peening was applied to the ultra-high strength Al-Zn-Mg-Cu alloys prepared by ingot metallurgy and spray forming. The microstructural evolution, pitting corrosion, intergranular corrosion resistance and electrochemical analysis were systematically investigated. The depth and number of corrosion pits caused by Al matrix, Al 7 Cu 2 Fe and Al 2 CuMg particles can be successfully reduced by laser shock peening. The depth of intergranular corrosion and the width of intergranular cracks also decreased. Cyclic polarization and electrochemical impedance spectroscopy tests also indicated the improved corrosion resistance caused by laser shock peening. The relationship between microstructural evolution and corrosion resistance was studied. • Corrosion resistance of ultra-high strength Al-Zn-Mg-Cu alloys is promoted by laser shock peening. • Al 2 CuMg and Al 7 Cu 2 Fe phases act as preferred sites for pitting corrosion. • Al 2 CuMg phase can cause deeper corrosion pits than Al 7 Cu 2 Fe phase. • Depth of pitting and intergranular corrosion are ameliorated by laser shock peening. • Residual compressive stress, line and surface defects is conducive to corrosion resistance. [ABSTRACT FROM AUTHOR]

Stress corrosion cracking (SCC) behavior and mechanism of a friction stir welded Al–Zn–Mg–Zr alloy with 0.25 wt.% Sc were investigated. Impurity intermetallics and primary Al 3 Sc x Zr 1− x particles both crack perpendicular to tensile direction, whereas anodic dissolution only occurs around the former, initiating SCC. During cracking propagation, both anodic dissolution and hydrogen embrittlement operate. The thermo-mechanically affected zone on advancing side adjacent to weld nugget zone is most susceptible to SCC, which can be ascribed to the enrichment of impurity intermetallics, continuously distributed grain boundary precipitates and its stronger galvanic coupling with weld nugget zone from their greater microstructure and micro-chemistry differences. [ABSTRACT FROM AUTHOR]

Corrosion behaviour, residual stress, intermetallics and microstructure of friction stir welded aerospace Al–Zn–Mg and Al–Zn–Mg–0.10Sc–0.10Zr (wt.%) alloys were investigated comparatively and in detail. The thermo-mechanically affected zones adjacent to weld nugget are most susceptible to corrosion in two weld joints. In addition to the enrichment of coarse Si and Fe intermetallics, wide precipitate free zones (in Al–Zn–Mg weld joint) and high tensile residual stress are the key factors. Secondary Al 3 Sc x Zr 1− x nanoparticles can effectively improve stress corrosion cracking resistance and decrease exfoliation corrosion rates of Al–Zn–Mg weld joints by restraining the formation of precipitate free zones and refining grains. [ABSTRACT FROM AUTHOR]