Here we first report results of the start of the solid-state reaction at the Rh/Fe(001) interface and the structural and magnetic phase transformations in 52Rh/48Fe(001), 45Rh/55Fe(001), 68Rh/32Fe(001) bilayers from room temperature to 800 °C. For all bilayers the non-magnetic nanocrystalline phase with a B2 structure (nfm-B2) is the first phase that is formed on the Rh/Fe(001) interface near 100 °C. Above 300 °C, without changing the nanocrystalline B2 structure, the phase grows into the low-magnetization modification α l ʹ (M S l ~ 825 emu/cm 3) of the ferromagnetic α ʹ phase which has a reversible α l ʹ ↔ αʺ transition. After annealing 52Rh/48Fe(001) bilayers above 600 °C the α l ʹ phase increases in grain size and either develops into α h ʹ with high magnetization (M S h ~ 1,220 emu/cm 3) or remains in the α l ʹ phase. In contrast to α l ʹ, the α h ʹ ↔ αʺ transition in the α h ʹ films is completely suppressed. When the annealing temperature of the 45Rh/55Fe(001) samples is increased from 450 to 800 °C the low-magnetization nanocrystalline α l ʹ films develop into high crystalline perfection epitaxial α h ʹ(001) layers, which have a high magnetization of ~ 1,275 emu/cm 3. α h ʹ(001) films do not undergo a transition to an antiferromagnetic αʺ phase. In 68Rh/32Fe(001) samples above 500 °C non-magnetic epitaxial γ(001) layers grow on the Fe(001) interface as a result of the solid-state reaction between the epitaxial α l ʹ(001) and polycrystalline Rh films. Our results demonstrate not only the complex nature of chemical interactions at the low-temperature synthesis of the nfm-B2 and α l ʹ phases in Rh/Fe(001) bilayers, but also establish their continuous link with chemical mechanisms underlying reversible α l ʹ ↔ αʺ transitions. An intriguing feature of the equilibrium diagram of the Fe-Rh system is the existence of the low-temperature transition at T K αʺ→αʹ ~ 100 °C between antiferromagnetic (AFM) αʺ and ferromagnetic (FM) αʹ phases in a narrow (0.48 < x Rh < 056) concentration interval in chemically ordered B2-FeRh alloys 1. This transition is accompanied by an isotropic volume expansion of ~ 1% of the B2-FeRh unit cell, which not only radically changes the magnetic properties, but also changes the entropy 2,3 and resistivity 4. The magnetostructural αʺ → αʹ (AFM-FM) transition gives existence to the giant magnetostriction 5 large magnetoresistance 6,7 and magnetocaloric effects 8 in B2-FeRh alloys. Numerous studies of bulk samples indicate that the starting temperature T K αʺ→αʹ and characteristics of the αʺ → αʹ transition may be modified by variations the magnetic field 9,10 , microstructure 11 , thermal treatment 12 , energetic ion irradiation 13 , stress 14 and hydrostatic pressure 15-17 and can also be tuned over a wide temperature range (100-600 K) by chemical substitution 9,18. Although bulk B2-FeRh samples exhibit a sharp transition with a small thermal hysteresis, thin films and nanoparticles often have an incomplete and broad asymmetrical hysteresis AFM-FM transition 1,19-34. The starting transition...