A cold roll-bonding process using AA1050 and AA6061 sheets, in which the initial strain of AA1050 is higher than that of AA6061, was employed to fabricate an AA1050/AA6061 layered sheet. The sheet was then annealed at various temperatures ranging from 200 to 400 °C. The as-roll-bonded sheet exhibited a typical deformation structure in which the grains were elongated along the rolling direction. The evolution of the microstructure in the layered sheets varied significantly depending on the location, resulting in an inhomogeneous distribution of hardness along the thickness direction. After annealing up to 300 °C, both the AA1050 and AA6061 regions still mainly exhibited a deformed structure. Complete recrystallization occurred in the specimens annealed at temperatures above 350 °C. The hardness decreased with increasing annealing temperature in both AA1050 and AA6061, but the decrease was greater in the AA6061 region than in the AA1050 region. Resultantly, at 350 °C or higher, hardness was almost the same in all regions. The specimen annealed at 350 °C exhibited the best mechanical properties in terms of the balance between tensile strength and elongation. It is concluded that AA1050/AA6061 layered Al sheets with excellent mechanical properties can also be fabricated by CRB when AA1050 has a higher initial strain than AA6061, and subsequent annealing.

An AA3003 tube was severely deformed by cold floating plug drawing, and then annealed at temperatures from 210 to 460°C. The as drawn Al tube exhibited a typical deformation structure in which the grains were greatly elongated along the drawing direction. The hardness increased with increasing the reduction of cross-sectional area (RA), became 68Hv after RA= 99%. Up to 310°C, the Al tube still mainly exhibited a deformed structure. While complete recrystallization occurred at temperatures above 360°C. The hardness decreased with increasing the annealing temperature, and it became 33Hv after annealing at 410°C. Both the tensile and yield strengths also decreased with increasing the annealing temperature, but the decrease was larger in yield strength than in tensile strength. The elongation increased with increasing the annealing temperature. The changes in the strength and the elongation with the annealing temperature were the largest at 360°C, in which the complete recrystallization occurred.

The Al-Fe-Mg-Cu-B system aluminum alloy is used for electrical wire, but is severely deformed by the multi-pass drawing process when a rod with a diameter of 12 mm is greatly reduced to 2.0 mm. This study investigated the changes in the microstructure, mechanical properties, and electrical properties of the aluminum wire during the drawing process in detail. The as-drawn aluminum alloy wire exhibited a deformation structure in which the grains were greatly elongated in the drawing direction, particularly in the specimens subjected to more than 80 % reduction in cross-sectional area (RA). For all drawn specimens, the fiber texture of the {110}<111> and {112}<111> components was mainly developed. The hardness tended to increase with increasing RA due to work hardening. In particular, when the RA increased to 97 % a great increase in hardness resulted. The specimen with an RA of 97 % showed the highest tensile strength of 288 MPa, 2.2 times higher than that of the specimen before drawing. The electrical conductivity decreased slightly with increasing RA, even in specimens with extreme increases in RA, and it remained at an average value of 56.6 %IACS.

A cold roll-bonding (CRB) process is applied to fabricate an AA1050/AA5052 layered sheet. In the process, commercial AA1050 and AA5052 sheets of 1 mm thickness, 40 mm width and 300 mm length are stacked onto each other, and then reduced to a thickness of 0.5 mm through a 2-pass cold rolling process without lubricant. The roll-bonded AA1050/AA5052 layered sheet is then annealed for 1 h at various temperatures from 200 to 400 °C. The specimens annealed at temperatures below 250 °C showed a typical deformation structure in which the grains were elongated along the rolling direction. However, the specimens annealed at temperatures higher than 300 °C exhibited recrystallization structures in both the AA1050 and AA5052 regions. All the roll-bonded and subsequently annealed specimens showed an inhomogeneous distribution of hardness in the thickness direction, in which the hardness in the AA5052 regions was higher than that in the AA1050 regions. As the annealing temperature increased, the tensile and yield strengths decreased and the elongation increased gradually. The mechanical properties were compared to those of commercial AA1050 and AA5052 materials and CRBed AA5052-2L materials from a previous study.