Precipitates in aluminium alloys

The upper bounds of the range of rotation angles exhibited by S-phase precipitates sit- uated away from T-phase interfaces corresponds well with the noted rotation that occur at

Considering the ADF STEM image in figure 5a, in which the precipitate has likely been sheared by a sin- gle dislocation close to the specimen surface (and possibly more times

condition. HAADF STEM images of precipitates from the three investigated alloys. The precipitates chosen are typical for the respective alloy and shows that the addition of Ge and

The images labelled ‘ Sum’ correspond to the sum of all loading maps used in the phase identification. By comparing the sum with the corresponding area in the VDF image, it is

For alloy S, the precipitates typically showed a predominantly Al-Mg-Si containing β″ phase and U2 phase interior, and some Cu enrichment, as well as a few sub-units of β Cu ′

Assuming similar interface energies for the precipitates in all three Li-added alloys (which is reasonable since the hardening phase is the same), we expect RXL0 to have a

It is observed that the precipitate statistics in the studied region of the in situ heated lamella (thickness ∼ 90 nm) showed a more refined microstructure of smaller

The image contrast of sheared needle-like β precipitates in the Al-Mg-Si alloy system is investigated with respect to shear- plane positions, the number of shear-planes, and the