Increasing the fraction of {111}/{111} near-singular boundaries ({111}/{111}-NSBs) has been reported as a primary solution to intergranular corrosion failure in Al-Zn-Mg-Cu alloys. The authors' previous work demonstrates that continuous static recrystallization resulting from a specific prestrain and annealing is conducive to the formation of {111}/{111}-NSBs in Al-Zn-Mg-Cu alloys. Therefore, the development of such boundaries in the alloys during dynamic recrystallization (DRX), particularly during discontinuous DRX (DDRX) and continuous DRX (CDRX) at elevated temperatures, should be elucidated. In the present work, an Al-Zn-Mg-Cu alloy containing 7.79%Zn, 1.53%Mg, and 1.68%Cu (mass fraction) was selected as the experimental material. A hot-rolled plate of the alloy was subjected to a two-stage solution treatment at 470^oC for 12 h and 520^oC for 6 h followed by cold rolling and recrystallization annealing. Three parallel samples cut from the recrystallized plate were compressed at 450, 480, and 520^oC at a strain rate of 0.001 s^-1 to a true strain of 1.20. The samples were water quenched immediately after the compression. Electron backscatter diffraction and grain boundary inter-connection measurement based on five-parameter analysis were performed to examine the microstructures and grain boundary character distributions of the compressed samples. The results indicate that the microstructures of the samples were uneven, exhibiting fine- and coarse-grained regions. Low-angle grain boundaries are dominant in the fine-grained regions, whereas high-angle grain boundaries are dominant in the coarse-grained regions. The fraction of {111}/{111}-NSBs increases with the compression temperature in fine- and coarse-grained regions. In the sample compressed at 520^oC, the {111}/{111}-NSBs from the low-angle grain boundaries constitute 8.77% of all grain boundaries, while those from the high-angle grain boundaries constitute 4.53%. The stress-strain curves and the microstructures of the sample compressed at 450^oC to a true strain of 0.36 show that primary DRX occurs at strains from 0.05 to 0.70. Furthermore, the coarse-grained microstructures and high-angle grain boundaries develop during the stage involving steady-state flow. When the strain increases from 0.70 to 1.20, secondary DRX (including DDRX and CDRX) occurs in some regions, leading to dramatic grain refinement and a sharp increase in flow stress. In this stage, CDRX intensifies with increasing compression temperature, and {111}/{111}-NSBs in the low-angle grain boundaries increase rapidly.