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In this study, microstructural evolution of Mg–Ni alloy during mechanical alloying(MA) was investigated.Also, a thermodynamic approach was utilized to predict the most stable phases formed in Mg–Ni alloy after MA. The phase composition and microstructural properties of Mg–Ni alloy were assessed by X-ray diffractometry, high-resolution field emission scanning electron microscopy and high-resolution transmission electron microscopy. The results showed that ball milling of magnesium and nickel powder mixture for 70 h yields nanostructural Mg2Ni compound with an average grain size of ~20 nm. Thermodynamic calculations revealed that in the composition ranges of 0.0 XMg 0.03(at.%)and 0.97 XMg 1, there is no driving force for amorphous phase formation. In the composition range of 0.07 XMg 0.93, the change of Gibbs free energy for amorphous phase formation was more negative than solid solution.While for XMg= 0.66(nominal composition of Mg2Ni intermetallic phase), the change of Gibbs free energy for intermetallic phase was found to be more negative than both amorphous and solid solution phases indicating that Mg2Ni intermetallic compound is the most stable phase, in agreement with the experimental observations.
In this study, microstructural evolution of Mg-Ni alloy during mechanical alloying (MA) was investigated. Also, a thermodynamic approach was utilized to predict the most stable phases formed in Mg-Ni alloy after MA. The phase composition and microstructural properties of Mg -Ni alloy were assessed by X-ray diffractometry, high-resolution field emission scanning electron microscopy and high-resolution transmission emission microscopy and high-resolution transmission electron microscopy. The results showed that ball milling of magnesium and nickel powder mixture for 70 h yields nanostructural Mg2Ni compound with an average grain size of ~ 20 nm. Thermodynamic calculations revealed that in the composition ranges of 0.0 XMg 0.03 (at.%) and 0.97 XMg 1, there is no driving force for amorphous phase formation. In the composition range of 0.07 XMg 0.93, the change of Gibbs free energy for amorphous phase formation was more negative than solid solution. Window for XMg = 0.66 (nominal composition of Mg2Ni intermetallic phase), the chang e of Gibbs free energy for intermetallic phase was found to be more negative than both amorphous and solid solution phases indicating that Mg2Ni intermetallic compound is the most stable phase, in agreement with the experimental observations.