In recent years, magnesium alloys have attracted attention in view of their low density and high specific strength and are being considered for structural components in aerospace and automobile applications. [1] Out of the wrought magnesium alloys, Mg-3Al-1Zn (AZ31) is considered to be the work-horse and considerable emphasis is being given to develop processing-microstructure-mechanical property correlations for this alloy. [2][3][4][5][6][7][8][9][10][11] Since magnesium alloys have limited ductility at room temperature, forming is generally done at elevated temperatures, the most common method being extrusion. [12][13][14][15] AZ31 alloy is commercially extruded at a temperature of about 300°C, [12] which results in a fine grained microstructure and a fiber texture with <10 1 0>direction parallel to the extrusion direction (ED). [2,6] Deformation at higher temperatures would enhance the hot workability, even to the extent of resulting in superplasticity, [16][17][18] presumably due to extensive occurrence of pyramidal slip and dynamic recrystallization. In addition, higher extrusion temperatures result in an increase in grain size. [9] The hot deformation behavior of AZ31 alloy is sensitive to the initial microstructure and the prior processing history, [2,5,9] and both the above changes in grain size and texture will influence the hot workability of the extruded product. The hot working behavior of Mg-Al-Zn alloys has been reviewed recently, [19] and the apparent activation energy estimated by different investigators has shown some variations and is generally higher than that for self-diffusion. [20][21][22][23][24] The aim of the present investigation is to characterize the hot deformation behavior of AZ31 rod produced by high temperature extrusion (HTX) (450°C) with a view to evaluate the hot working mechanisms and microstructural development in the product. Such a study would assist in achieving microstructural control during the secondary-forming stage of component manufacture in this industrially important magnesium alloy. The hot deformation behavior is explored using the methods of kinetic analysis as well as processing maps. The former one is based on the standard kinetic rate equation relating the flow stress (r) to strain rate (_ e) and temperature (T), given by: [25] _ e Ar n expÀQ=RT (1) where A = constant, n = stress exponent, Q = activation energy, and R = gas constant. The rate-controlling mechanisms are identified on the basis of the activation parameters n and Q. The technique of processing maps is based on the dynamic materials model, the principles of which are described earlier. [26][27][28] Briefly, the work-piece undergoing hot deformation is considered to be a dissipator of power and the strain rate sensitivity (m) of flow stress is the factor that partitions power between deformation heat and microstructural changes. The efficiency of power dissipation occurring through microstructural changes during deformation is derived by comparing the non-linear power dissipation occurring instant...