Abstract

Atomic scale characterization of fine precipitates in an under-aged Cu added Al-Mg-Si alloy was carried out by combination of atomically-resolved annular dark-field scanning transmission electron microscopy and energy dispersive X-ray spectroscopy. Two types of precipitates were observed in the alloy. In the case of ordered β” precipitates, β” was proposed as Mg5-xAl2+xSi4 (x ≈ 1) with solute Cu atoms replacing Al site of β” precipitate. In the case of disordered precipitates, the precipitates were found to consist of β” sub-unit cells, three-fold symmetric structure without Cu atoms, Cu containing structures termed as “Cu sub-unit cluster”, and Q’ sub-unit cells. Among these structures, the morphologies of three-fold symmetric structure without Cu atoms, Cu sub-unit cluster, and Q’ sub-unit cell were almost the same, so that these structures should be the clusters of Q’ phase. Since the areal density, length and diameter of precipitates were almost equal between Cu free Al-Mg-Si alloy and Cu added Al-Mg-Si alloy, the increase of hardness by Cu addition should be due to the precipitation of Cu related precipitates, such as Cu sub-unit clusters and Q’ sub-unit cells.

Highlights

  • Precipitation hardening is one of the most effective routes to improve the strength of age-hardening aluminum alloys due to the movement of dislocations being hampered by the precipitates[1,2,3,4,5,6,7,8,9]

  • We present the microstructures and compositions of fine precipitates and discuss the effect of Cu addition for the precipitation sequences in under-aged Al-Mg-Si alloys

  • We found that β” and Q’ were present at under-aged period as dominant precipitates

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Summary

Introduction

Precipitation hardening is one of the most effective routes to improve the strength of age-hardening aluminum alloys due to the movement of dislocations being hampered by the precipitates[1,2,3,4,5,6,7,8,9]. Addition of Cu to the Al-Mg-Si alloys shows large enhancement of the age-hardening kinetics and improvement of the peak hardness, and have been widely applicable for the industrial applications owing to their good mechanical properties compared with the one without Cu15–17. The cause of these phenomena have been considered as the change of precipitation sequences as[29,30,31,32,33,34,35]: SSSS → atomic clusters → G.P. zones → metastable β’’, L, C, QP, QC phases →metastable β’, Q’ phases → stable Q phase. Composition Mg2+xAl7-x-yMg2+y (1 < x + y < 3) Mg5Si6 Al2Mg5Si4 Al3Mg4Si4 MgAl2Si2 MgAlSi Mg9Al3Si7 Mg1.8Si Unknown Unknown Unknown Unknown Al3Cu2Mg9Si7 Al6Mg6Si7Cu2 Mg2Si Al3Cu2Mg9Si7

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