Significant strengthening in superlight Al-Mg alloy with an exceptionally large amount of Mg (13 wt%) after cold rolling

Improving fatigue life of 7N01 Al alloy weld by surface spinning strengthening

“…In the early stage of uniform plastic deformation, the work hardening rate of welded sample decreases slowly, which indicates that the work hardening ability of welded sample is stronger than that of matrix sample, which can be mainly attributed to the characteristics of filler metal. In general, as a typical Al–Mg alloy, the work hardening ability of 5356 Al alloy welding wire is strong, and its precipitation strengthening ability is weak due to the relatively low stacking fault energy, and therefore, nanoparticles are difficult to occur in the weld without the addition of Si and Zn elements 34 . However, in the later stage of uniform deformation, the work hardening rate of the welded joint decreases sharply, which is attributed to the local necking of the heterogeneous welded joint during the tensile process, so that the work hardening index of the welded joint before necking is lower than that of the matrix metal.…”

“…In general, as a typical Al-Mg alloy, the work hardening ability of 5356 Al alloy welding wire is strong, and its precipitation strengthening ability is weak due to the relatively low stacking fault energy, and therefore, nanoparticles are difficult to occur in the weld without the addition of Si and Zn elements. 34 However, in the later stage of uniform deformation, the work hardening rate of the welded joint decreases sharply, which is attributed to the local necking of the heterogeneous welded joint during the tensile process, so that the work hardening index of the welded joint before necking is lower than that of the matrix metal. Of course, 3S treatment can still improve the work hardening index and work hardening rate compared with the welded samples before and after 3S, as shown in Figure 8.…”

Effect of Zn and Cu Addition on Microstructure and Mechanical Properties of Al-10wt%Mg Alloy

“…(1) Solid-solution strengthening can be calculated by the following formula: ∆σ ss = HC n , where n and H are constants depending on material. For Mg solid solution of the present study [27][28][29][30], H = 13.8 (MPa/wt%) and n = 1.14. According to the analysis of XRD results, the Mg solute concentration is 6.76 wt% under 150 • C annealing, so its contribution to yield strength is 125 MPa, the content of Zn is 1.0 wt% and its contribution to yield strength is about 2 MPa.…”

“…where k is Hall-Petch slope. With k being taken as 60-280 MPa µm 1/2 [28][29][30], in the present work, k is taken as 73 MPa µm 1/2 , D is the equivalent average size of lamellar boundary for the grain-boundary-strengthening calculation [31], which can be calculated by formula: D = 2/ 1/d T + π/2d L . According to the elongated grains shown in Figure 2 and the statistical distribution diagram shown in Figure 5, the values of d T and d L can be calculated: d T = 170.8 nm, d L = 1167.9 nm, so it can be calculated from the formulas that the grain-boundary strengthening is 138 MPa.…”

Effects of Ce-Rich Mischmetal on Microstructure Evolution and Mechanical Properties of 5182 Aluminum Alloy

“…The microstructure modification of the Ce-rich mischmetal on the cold-rolled 5182 Al alloy was mainly reflected in a larger grain aspect ratio and finer Al 6 (Mn, Fe) particles ( Figure 3e,f and Figure 5e,f) after deformation. It was reasonable to consider that the increment of the strength of the cold-rolled 5182 Al alloy could be determined by cell-size strengthening, dislocation density strengthening, and particle strengthening [26], as the solid solution strengthening could be ignored because not only the Mg 2 Si phase was re-dissolved during the homogenized annealing (Figure 5b,c) but also two alloys have a similar solute element content ( Table 2). The increment of the strength of the recrystallization annealed 5182 Al alloy could be calculated by using the Hall-Petch equation [8,27]:…”