Thus, as the result of multiple cycles of γ-α-γ transformations in the reverted austenite in iron-nickel alloy, the dislocations density increased by three orders, nanoscale level fragments (nanofragmentation) with additional small-angle subboundaries were formed, a quantity of dispersed grains having high-angle boundaries increased, and deformation twins came into existence. Figure 1 Microstructure (A) and electron diffraction pattern of reverted austenite

(B) after 50 γ-α-γ transitions. ×20,000. The phase-hardened alloy was annealed at temperatures of 400°C for 6 h. As the result of phase hardening, the microhardness CAL-101 nmr of the surface layer of the alloy significantly increased. In the initial austenite

state (prior to martensitic transformations), microhardness I-BET-762 chemical structure was equal to 1,159 MPa, and after 10 and 50 γ-α-γ cycles, it increased up to 1,550 and 1,776 MPa, respectively. This pointed to the fact of an increasing degree of reverted austenite strengthening under the consistent reiteration of γ-α-γ cycles. Photosensitive film blackening curves that characterize the concentration distribution of the isotopes 63Ni and 55,59Fe are shown in Figures  2 and 3. Obtained from semilogarithmic curve of the β activity dependence on penetration depth of radioisotopes, the diffusion coefficients of nickel and iron were equal to D Ni = 1.14 × 10-12 and D Fe = 0.86 × 10-12 cm2/s, respectively. It is evident that the diffusion mobility of nickel in the studied alloy is higher than that of iron. The D Ni/D Fe ratio is equal to about 1.3. This result is qualitatively consistent with the data on the diffusion of nickel and iron in iron-nickel alloy obtained under conditions of stationary isothermal annealing at temperatures higher than 900°C [19]. Such high values of

D Ni and D Fe for relatively low temperature of 400°C are associated with high density of dislocations and high length of additional boundaries and subboundaries between the structural elements that were formed as the result of multiple γ-α-γ transformations. Figure 2 Concentration distribution of the 63 Ni radioisotope in reverted austenite. Figure 3 Concentration distribution of the Niclosamide 55,59 Fe radioisotopes in reverted austenite. It was shown, both experimentally and theoretically [6, 20], that the dislocations increase diffusion penetration in solids. The contribution of dislocations to the total diffusion flow must be considered mainly at temperatures below 0.5 of melting point. Analysis of experimental data by different authors shows that diffusion coefficients of substitution atoms and interstitials in this temperature range significantly increase depending on dislocation density and grain boundaries length. Diffusion acceleration in defects area of crystal structure is described in [6, 8, 10, 13, 20].