Lanthanum hexaaluminate (LHA), with an ideal stoichiometry LaAl 11 O 18 is a candidate coating material for fibermatrix interface adjustment in fiber reinforced ceramic composites as well as an in situ platelet reinforcement for dispersion reinforced composites. [1,2] Fields of application are, e.g., thermal barrier coatings and combustion catalysts. [3,4] LHA is one of the main compounds which is normally formed in addition to the lanthanum aluminate, LaAlO 3 , in the La 2 O 3 -Al 2 O 3 system studied by Bondar and Vinogradova. [5] The reaction sequence for formation of the LHA phase requires formation of LaAlO 3 at lower temperature, been followed by a solid-state reaction between LaAlO 3 and Al 2 O 3 at higher temperatures. [5] According to thermodynamic calculations for the stoichiometric composition, initial temperature of the solid-state reaction between LaAlO 3 and Al 2 O 3 is 1170 8C. [6] Despite the low thermodynamically calculated temperature, the formation of LaAl 11 O 18 in comparison with many solid-state reactions is extremely slow and requires higher temperatures and hours of dwelling. Ropp and Carroll have proposed that the rate-limiting step in formation kinetics is conversion of O 2 to 2O 2À at the phase boundary of LHA that accompanies La 3þ diffusion into A1 2 O 3 building blocks. [7] In addition to its importance as an engineering material, LHA is of intrinsic scientific interest because of its inherent defective structure. This arises because its molecular stoichiometry, LaAl 11 O 18 , is incompatible with the stoichiometries of its putative parent structures, MAl 11 O 17 (b-alumina) and MAl 12 O 19 (magnetoplumbite). The structures of both of these compounds consist of spinel-like blocks [Al 11 O 16 ] þ separated by mirror planes containing the large cations [M þ O] À and [M 2þ AlO 3 ] À , respectively, in which the stabilizing cations (M þ or M 2þ ) reside. [8] Park and Cormack [9] by using computerbased atomistic simulation techniques, elucidated that for the stoichiometric LHA, the mixed b/MP-type phase would be most likely. The energetically most favored structure of this phase has ideal b-type and MP-type mirror planes alternating in the c direction, with aluminum vacancies (one per the basic cell) at the central spinel block to provide the electroneutrality. However, they discussed that these structures are less stable than the nonstoichiometric ones and LHA will not form an ideal stoichiometric phase, but most likely an MP-type nonstoichiometric phase La 0.83 Al 11.83 O 19 (Al/La ¼ 14.2). Their calculations also revealed that the nonstoichiometric LHA contains defect complex composed of a vacancy pair (V La and V Al ) on the mirror plane, and a pair of Al Frenkel defects (V Al and Al i ) formed doubly above and below the center of the vacancy pair.Two aspects in LHA ceramics motivated utilization of microwave heating in reaction sintering of alumina/LHA ceramics: (i) the solid-state reaction of LHA formation can be enhanced by an additional driving force for mass transport while heat...