Recently a theoretical model for roughness induced crack closure during threshold fatigue crack growth in metallic systems has been developed [1]. The model closely predicts the functional dependence of crack closure stress intensity level, K d at threshold on grain size. Basically, the model assumes the establishment of a slip band inclined at a certain angle to the crack plane at threshold. The size of the slip band was first assumed to be of the order of grain size. The major closure mechanism is essentially presumed to be due to fracture surface roughness formed by crack growth with periodic deflections across the grain boundary along the crack path. The magnitude of roughness induced disregistry behind the crack tip was then deduced by assuming that continuous dislocation distribution in the slip band is a close approximate of the slip band piled-up at the grain boundary and slip is completely irreversible upon unloading• This facilitates the calculation of crack tip sliding displacement from which the mode disregistry responsible for closure can be calculated. The magnitude of K d at threshold can be expressed in terms of the critical resolved shear stress, h~ ~cr~s for (hkl) slip system, the macroscopic yield stress, o V, the angle '0' subtended by the slip band with the crack plane and '1', the length of the slip band which is considered to be equal to grain size 'd' as: Kct [28.17(1-2 he = aJ )%rs, oy sin 01] 1/2 (1) where a9 is Poisson's ratio. The predictions offered by the above expression are in good agreement [ 1] with the experimental results on titanium alloys, nickel base alloys and iron base klloys. In (1), K d is also a direct function of % apart from grain size While analyzing grain size effects on K d, the effect of d also has to be • ° . . . . Y considered since o is dependent on gram saze as expressed by the well known • Y • Hall-Petch relation. In the previous study [1], an average value of % was taken (850 MPa for titanium alloys, 900 Mpa for nickel base alloys and 350 MPa for iron base alloys) for the prediction of K d as a function of grain size. These values represent the yield strength better in the case of titanium and nickel base alloys which do not exhibit strong sensitivity of o to variations in grain size• In • . . Y , .addiuon, these alloys belong to a high strength category where small varlatxons in grain size do not affect yield strength adversely. However other systems such as iron base alloys are known for the strong grain size dependence of yield stress. Further, in low strength microstructures, the grain size induced variations in yield Int Journ of Fracture 44 (1990)