Manipulating Precipitation Through Thermomechanical Treatment to Control Corrosion Behavior of an Al-Cu-Mg Alloy

doi:10.1007/s40195-022-01385-8

Abstract

Abstract:

Controlling the precipitation through thermomechanical treatment is an important method to improve the corrosion resistance of Al-Cu-Mg alloys. In this study, the corrosion behaviors of Al-Cu-Mg alloys in the solution-treated state and retrogression-treated state under cold rolling deformation and then natural aging were investigated. In the solution-treated series alloys, the cold-rolled deformation improved the resistance to intergranular corrosion by suppressing the precipitation of the S-phase on the grain boundaries. The increased pitting potential and corrosion potential were related to the increased concentration of solute atoms within the grain interiors and the eliminated S-phase on grain boundaries. In the retrogression-treated series alloys, the 30% cold rolling deformation stimulated the growth of the S-phase and transformed the S-phase distribution from discontinuous to continuous on the grain boundaries, thereby changing the pitting corrosion to the network corrosion morphology. The precipitation of the S-phase with large dimension within the grain interiors contributed to the decreased pitting potential and corrosion potential.

Key words: Thermomechanical treatment, Precipitation, Intergranular corrosion, Pitting corrosion

Xiu-Rong Zhu, Jun Wang, Wei-Ning Shi, Xue-Bing Liu, Xin-Fang Zhang, Hai-Fei Zhou. Manipulating Precipitation Through Thermomechanical Treatment to Control Corrosion Behavior of an Al-Cu-Mg Alloy[J]. Acta Metallurgica Sinica (English Letters), 2022, 35(9): 1547-1558.

Figures/Tables 11

Table 1 Detailed processing parameters of the studied Al-Cu-Mg alloys

Sample ID	Solution treatment (495 °C)	Peak aging (190 °C)	Retrogression treatment (280 °C)	Cold rolling deformation	Natural aging (NA)
A	1 h	-	-	-	7 days
B	1 h	-	-	30%	7 days
C	1 h	-	-	50%	7 days
D	1 h	-	-	70%	7 days
E	1 h	20 h	20 min	-	7 days
F	1 h	20 h	20 min	30%	7 days
G	1 h	20 h	20 min	50%	7 days
H	1 h	20 h	20 min	70%	7 days

Fig. 1 Typical corrosion morphologies of samples a A, b B, c C, d D after IGC tests

Fig. 2 Typical corrosion morphologies of samples a E, b F, c G, d H after IGC tests

Fig. 3 Potentiodynamic polarization results of samples A, B, E, F

Fig. 4 Precipitates and dislocation structures on grain boundaries of samples a A, b B, c C, d D, e line scanning analysis at yellow line position of sample B, f composition at yellow line position in e

Fig. 5 Secondary phases and dislocation structures within the grain interiors in the solution-treated series Al-Cu-Mg alloys. a sample A, b sample B (inset shows the SAED pattern of the T-phase), c sample C, d sample D (inset shows the SAED pattern of the matrix), e composition of the T-phase shown in a

Fig. 6 S-phase precipitates and dislocations on grain boundaries of retrogression-treated series Al-Cu-Mg alloy: a sample E, b sample F, c dislocations near the grain boundaries of sample F, d composition of the S-phase shown in a, e sample G, f sample H

Fig. 7 Line scanning analyses on grain boundaries of sample F: a, b S-phase positions; c, d spacing positions between adjacent S-phases

Fig. 8 Dislocations and secondary phases in grain interiors of retrogression-treated series Al-Cu-Mg alloy: a sample E, b sample F, c S-phase in grain interiors of sample F (inset shows the SAED pattern of the S-phase), d composition of S-phase shown in (c), e sample G, f sample H

Fig. 9 Coherent relationship between S-phase and Al matrix in sample F: a morphology of S-phase, b composition of S-phase shown in a, c HRTEM of S-phase shown in a, d partially enlarged view of c, e FFT results of S-phase in c, f FFT results of Al matrix in c

Fig. 10 XRD test and analysis results of the alloys with retrogression treatment, 30-70% cold rolling deformation and natural aging: a XRD test results, b fitting result of sample F, c fitting result of sample G, d fitting result of sample H

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