Dislocation ordering and texture strengthening of naturally aged Al-Cu-Mg alloy

doi:10.1016/j.jmst.2021.12.011

Abstract

Abstract:

Stability of grain structure, dislocation ordering and strengthening mechanisms of the naturally aged Al-Cu-Mg alloy after solution treatment are investigated by using optical microscope (OM), scanning electron microscope (SEM), electron back-scattered diffraction (EBSD), X-ray diffraction (XRD) and transmission electron microscope (TEM). Results show that {100}<001>, {100}<110>, {110}<110> and {110}<001> slip systems can be activated after solution treatment, which can promote the formation of {110}<001> Goss texture. The combination effect of T-Al₂₀Cu₂Mn₃ phase and Goss-oriented grains with large Taylor factor makes the solution-treated alloys display excellent stability of grain structure. The enhanced yield strength of the alloy is ascribed to grain-refine strengthening, dispersed particles strengthening, dislocation strengthening and texture strengthening. The coarsening of the second phase is responsible for softening of the alloy after annealing at 400 °C + solution treatment at 475 °C.

Key words: Al-Cu-Mg alloy, Dislocation ordering, Goss texture, Grain structure stability, Texture strengthening

F. Liu, Z.Y. Liu, G.Y. He, L.N. Ou. Dislocation ordering and texture strengthening of naturally aged Al-Cu-Mg alloy[J]. J. Mater. Sci. Technol., 2022, 118: 1-14.

Figures/Tables 16

Fig. 1. Grain microstructure evolution of Al-Cu-Mg alloys. (a) 30-ST sample; (b) 31-ST sample; (c) 32-ST sample; (d) 33-ST sample; (e) 34-ST sample; (f) 35-ST sample; (g) 36-ST sample; (h) 37-ST sample; (i) 38-ST sample; (j) 39-ST sample; (k) 40-ST sample.

Fig. 2. EBSD maps of Al-Cu-Mg alloys. (a) IPF map of 32-ST sample; (b) GOS map of 32-ST sample; (c) GND map of 32-ST sample; (d) IPF map of 36-ST sample; (e) GOS map of 36-ST sample; (f) GND map of 36-ST sample; (g) IPF map of 40-ST sample; (h) GOS map of 40-ST sample; (i) GND map of 40-ST sample.

Fig. 3. SEM images of Al-Cu-Mg alloys. (a), (e) 32-ST sample; (b), (f) 36-ST sample; (c), (g) 37-ST sample; (d), (h) 40-ST sample.

Fig. 4. TEM images of grain boundaries of Al-Cu-Mg alloys, electron beam (EB) directions taken from <011>, <001> and <1(-)12>. (a) 32-ST sample, EB//<011>; (b) 36-ST sample, EB//<011>; (c) 40-ST sample, EB//<011>; (d) 32-ST sample, EB//<001>; (e) 36-ST sample, EB//<011>; (f) 40-ST sample, EB//<011>; (g) 32-ST sample, EB//<1(-)12>; (h) 36-ST sample, EB//<1(-)12>; (i) 40-ST sample, EB//<1(-)12>.

Fig. 5. HAADF images of 40-ST sample, electron beam direction taken from <011>. (a) HAADF image; (b) SAED pattern; (c) EDX mapping of rectangle in Fig. 5(a); (d) EDX point scanning of red and green circles in Fig. 5(a); (e) bright field image of 40-ST sample; (f) dark field image of 40-ST sample; (g) two-beam diffraction, EB//[110]; (h) crystal plane orientation corresponding to Fig. 5(e-g); (i) HAADF image of screw dislocation and EDX mapping of screw dislocation.

Fig. 6. TEM images of grain interior of Al-Cu-Mg alloys, electron beam (EB) directions taken from <110>, <100> and <1(-)12>. (a) 32-ST sample, EB//<110>; (b) 36-ST sample, EB//<110>; (c) 40-ST sample, EB//<110>; (d) 32-ST sample, EB//<100>; (e) 36-ST sample, EB//<100>; (f) 40-ST sample, EB//<100>; (g) 32-ST sample, EB//<1(-)12>; (h) 36-ST sample, EB//<1(-)12>; (i) 40-ST sample, EB//<1(-)12>.

Fig. 7. TEM images of Al20Cu2Mn3 particle, electron beam (EB) direction taken from <110>. (a) 32-ST sample; (b) 36-ST sample; (c), (d) 40-ST sample.

Fig. 8. ODF figure measured by XRD of Al-Cu-Mg alloys. (a) 30-ST sample; (b) 32-ST sample; (c) 34-ST sample; (d) 36-ST sample; (e) 38-ST sample; (f) 40-ST sample.

Fig. 9. ODF figure measured by EBSD of Al-Cu-Mg alloys. (a) 32-ST sample; (b) 36-ST sample; (c) 40-ST sample.

Fig. 10. Yield stress of Al-Cu-Mg alloys after annealing at different temperatures for 120 min + solution treatment at 475 °C for 40 min.

Table 1. Volume fraction of LAGBs and HAGBs.

Alloy number	Grain boundary type	Misorientation angle range (°)	Volume fraction
32-ST	Low angle grain boundaries	1-15	22.9%
32-ST	High angle grain boundaries	15-180	77.1%
36-ST	Low angle grain boundaries	1-15	16.2%
36-ST	High angle grain boundaries	15-180	83.8%
40-ST	Low angle grain boundaries	1-15	17.4%
40-ST	High angle grain boundaries	15-180	82.6%

Fig. 11. Distribution of GOS, misorientation angle and Taylor factor of Al-Cu-Mg alloys. (a) Grain orientation spread angle; (b) average misorientation angle; (c) average Taylor factor.

Fig. 12. Taylor factor maps of Al-Cu-Mg alloys. (a) 32-ST sample; (B) 36-ST sample; (C) 40-ST sample.

Fig. 13. Orientation relation between screw dislocation and slip plane. (a) SAED pattern of 36-ST sample, EB//[110]; (b) Crystal plane orientation corresponding to Fig. 13(a); (c) TEM Bright field image corresponding to Fig. 13(a); (d) Slip systems corresponding to Fig. 13(b).

Table 2. Contribution of grain refinement to strength.

Alloy Number	Grain Diameter (μm)	${{d}^{-\frac{1}{2}}}$ (${{\text{m}}^{-\frac{1}{2}}}$)	${{\delta }_{\text{gb}}}$ (MPa)
30-ST	29.68	183.49	18.35
31-ST	36.55	165.41	16.54
32-ST	36.12	166.39	16.64
33-ST	32.34	175.84	17.58
34-ST	24.26	203.03	20.30
35-ST	21.36	216.37	21.64
36-ST	21.42	216.07	21.61
37-ST	21.92	213.59	21.36
38-ST	18.40	233.13	23.31
39-ST	19.69	225.36	22.54
40-ST	21.65	214.92	21.49

Table 3. Contribution of Goss texture to yield stress.

Alloy	GNDs density (×${{10}^{14}}{{\text{m}}^{-2}}$)	${{\tau }_{\text{d}}}$ (MPa)
36-ST	5.11	192.50
40-ST	5.37	197.34

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