The magnetic and structural transformations in the Heusler-based system ${\mathrm{Ni}}_{0.50}{\mathrm{Mn}}_{0.50\ensuremath{-}x}{\mathrm{In}}_{x}$ are studied in the composition range $0.05\ensuremath{\leqslant}x\ensuremath{\leqslant}0.25$. While the cubic phase is preserved in the range $0.165\ensuremath{\leqslant}x\ensuremath{\leqslant}0.25$, we find the presence of martensitic transformations in alloys with $x\ensuremath{\leqslant}0.16$. In a critical composition range $0.15\ensuremath{\leqslant}x\ensuremath{\leqslant}0.16$, the magnetic coupling in both austenitic and martensitic states is ferromagnetic. Magnetic field-induced structural transitions are also found in the $x=0.16$ alloy, whereby the structural transition temperature shifts by $42\phantom{\rule{0.3em}{0ex}}\mathrm{K}$ in a field of $50\phantom{\rule{0.3em}{0ex}}\mathrm{kOe}$.

/pdf/ferromagnetism-in-the-austenitic-and-martensitic-states-of-2ixgukki05.pdf

Ferromagnetism in the austenitic and martensitic states of Ni-Mn-In alloys

We have modelled the phase diagram of magnetic shape memory alloys of the Heusler type by using the phenomenological Ginzburg–Landau theory. When fixing the parameters by realistic values taken from experiment we are able to reproduce most details of, for example, the phase diagram of Ni2+xMn1−xGa in the (T, x) plane. We present the results of ab initio calculations of the electronic and phonon properties of several ferromagnetic Heusler alloys, which allow one to characterize the structural changes associated with the martensitic instability leading to the modulated and tetragonal phases. From the ab initio investigations emerges a complex pattern of the interplay of magic valence electron per atom numbers (Hume–Rothery rules for magnetic ternary alloys), Fermi surface nesting and phonon instability. As the main result, we find that the driving force for structural transformations is considerably enhanced by the extremely low lying optical modes of Ni in the Ni-based Heusler alloys, which interfere with the acoustical modes enhancing phonon softening of the TA2 mode. In contrast, the ferromagnetic Co-based Heusler alloys show no tendency for phonon softening.

https://iopscience.iop.org/article/10.1088/0022-3727/39/5/S13/pdf

Modelling the phase diagram of magnetic shape memory Heusler alloys

Crystal structure of 7M modulated Ni–Mn–Ga martensitic phase

Giant heterogeneous magnetostriction in Fe–Ga alloys: Effect of trace element doping

Magnetoelectric (ME) effect experimentally discovered about 60 years ago remains one of the promising research fields with the main applications in microelectronics and sensors. However, its applications to biology and medicine are still in their infancy. For the diagnosis and treatment of diseases at the intracellular level, it is necessary to develop a maximally non-invasive way of local stimulation of individual neurons, navigation, and distribution of biomolecules in damaged cells with relatively high efficiency and adequate spatial and temporal resolution. Recently developed ME materials (composites), which combine elastically coupled piezoelectric (PE) and magnetostrictive (MS) phases, have been shown to yield very strong ME effects even at room temperature. This makes them a promising toolbox for solving many problems of modern medicine. The main ME materials, processing technologies, as well as most prospective biomedical applications will be overviewed, and modern trends in using ME materials for future therapies, wireless power transfer, and optogenetics will be considered.

Magnetoelectric effect: principles and applications in biology and medicine– a review

Composition dependence on the martensitic structures of the Mn-rich NiMnGa alloys

Giant magnetostriction is achieved in the slightly Tb-doped Fe83Ga17 melt-spun ribbons. The tested average perpendicular magnetostriction is -886 ppm along the melt-spun ribbon direction in the Fe82.89Ga16.88Tb0.23 alloy. The calculated parallel magnetostriction is 1772 ppm, more than 4 times as large as that of binary Fe83Ga17 alloy. The enhanced magnetostriction should be attributed to a small amount of Tb solution into the A2 matrix phase during rapid solidification. The localized strong magnetocrystalline anisotropy of Tb element is suggested to cause the giant magnetostriction.

Giant magnetostriction in Tb-doped Fe83Ga17 melt-spun ribbons

Giant magnetostriction is achieved in lightly Tb-doped Fe83Ga17 melt-spun ribbons. The average perpendicular magnetostriction λ⊥ is −886 ppm along the melt-spun ribbon direction in the Fe82.89Ga16.88Tb0.23 alloy and the calculated parallel magnetostriction λ|| is 1772 ppm. These values are more than four times as large as those found in binary Fe83Ga17. The enhanced magnetostriction is attributed to a small amount of Tb entering solution in the A2 matrix phase during rapid solidification. The strong localized magnetocrystalline anisotropy of terbium is thought to cause the giant magnetostriction.

Improved magnetostriction of Fe83Ga17 ribbons doped with Sm

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Composition dependence on the martensitic structures of the Mn-rich NiMnGa alloys

Giant heterogeneous magnetostriction in Fe–Ga alloys: Effect of trace element doping

Giant magnetostriction in Tb-doped Fe83Ga17 melt-spun ribbons

Giant magnetostriction in Tb-doped Fe83Ga17 melt-spun ribbons

Improved magnetostriction of Fe83Ga17 ribbons doped with Sm