Defect generation and analysis in mechanically alloyed stoichiometric Fe–Ni alloys

Geng, Yunlong; Ablekim, Tursun; Koten, Mark A.; Weber, Marc H.; Lynn, Kelvin G.; Shield, Jeffrey E.

doi:10.1016/j.jallcom.2015.02.038

Cited by 42 publications

(11 citation statements)

References 29 publications

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“…Calibration was performed for pure metals. Thermo electromotive force changes drastically at 400-450°C which corresponds, in line with the results of X-ray diffractometry, to the formation start of nano-sized nucleus of FeCr solid solution [21][22][23].…”

Section: Methodssupporting

confidence: 82%

D-shell of iron atom of the amorphous FeCr₁₅B₁₅alloy effective charge change during the crystallization

Khmelevsky

Funtikov

Aksenenko

et al. 2017

Mechanics & Industry

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An amorphous metal alloy of the FeCrB system was studied during the crystallization by thermal annealing. Such an alloy is a perspective candidate for the role of an intermediate layer in multilayer covering for cutting tools. By the using of the thermoelectric voltage measurement, positron annihilation spectroscopy, and X-ray photoelectron spectroscopy, the conjoint research was performed for the study of the conduction and delectron band state in the amorphous metallic alloy FeCr 15 B 15 , which intersects each other by the energy. The results of all the studies agree with each other and indicate the change in the effective charge of the d-shell by 1 electron during crystallization.

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Section: Methodssupporting

confidence: 82%

D-shell of iron atom of the amorphous FeCr₁₅B₁₅alloy effective charge change during the crystallization

Khmelevsky

Funtikov

Aksenenko

et al. 2017

Mechanics & Industry

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“…The diffusion coefficients of Fe and Ni are extremely low around this temperature, and in reality, no diffusion takes place, which is why the ordered L1 0 FeNi phase requires billions of years to form in cosmic products (meteorites). Since the discovery of the L1 0 FeNi phase in the 1960 s, several attempts (which might trigger atomic migration) such as irradiation with high-energy beams 7 , a nanoparticle technique 8 , mechanical alloying 9 , thin films comprised of mono-layered atoms 10 , and high-pressure torsion technique 11 have been tried to artificially produce this phase. However, L1 0 FeNi-based hard magnets with high degree of chemical order have yet to be produced.…”

mentioning

confidence: 99%

Artificially produced rare-earth free cosmic magnet

Makino

Sharma

Sato

et al. 2015

Sci Rep

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Chemically ordered hard magnetic L10-FeNi phase of higher grade than cosmic meteorites is produced artificially. Present alloy design shortens the formation time from hundreds of millions of years for natural meteorites to less than 300 hours. Electron diffraction detects four-fold 110 superlattice reflections and a high chemical order parameter (S 0.8) for the developed L10-FeNi phase. The magnetic field of more than 3.5 kOe is required for the switching of magnetization. Experimental results along with computer simulation suggest that the ordered phase is formed due to three factors related to the amorphous state: high diffusion rates of the constituent elements at lower temperatures when crystallizing, a large driving force for precipitation of the L10 phase, and the possible presence of L10 clusters. Present results can resolve mineral exhaustion issues in the development of next-generation hard magnetic materials because the alloys are free from rare-earth elements, and the technique is well suited for mass production.

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“…Also, in the FeAl system, ordering decreases with the increase in milling time. In general, the S value of mechanically alloyed powder can be improved by annealing or heat treatment due to annihilation of defects and subsequent increase in diffusion. ,, However, the FeNi system is an exception, as the heat treatment of the FeNi powder below order–disorder temperature (593 K) will require astronomical time to induce sufficient diffusion for improving the ordering quantity . Therefore, in future, the effect of electric and magnetic fields on the milled FeNi powder during heat treatment below order–disorder transformation temperature toward the formation of L1 0 FeNi will be studied.…”

Section: Resultsmentioning

confidence: 99%

“…The formation of L1 0 FeNi necessitates a very high rate of interdiffusion of Fe and Ni in the FeNi lattice below 593 K (temperature for the order to disorder transformation). In order to induce high rate of diffusion at low temperatures and to achieve the formation of L1 0 FeNi, several processing techniques such as high energy neutron , or electron or ion beam irradiation, severe plastic deformation, − mechanical alloying, , and approaches such as crystallization from amorphous FeNiSiPBCu, , field-assisted heat treatment of FeNi , and chemically induced ordering such as nitrogen insertion and topotactic extraction, pre-ordered precursor reduction, and so forth are studied.…”

Section: Introductionmentioning

confidence: 99%

Formation of L1₀ Ordering in FeNi by Mechanical Alloying and Field-Assisted Heat Treatment: Synchrotron XRD Studies

et al. 2023

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L10-ordered FeNi, tetrataenite, found naturally in meteorites is a predilection for next-generation rare-earth free permanent magnetic materials. However, the synthesis of this phase remains unattainable in an industrially relevant time frame due to the sluggish diffusion of Fe and Ni near the order–disorder temperature (593 K) of L10 FeNi. The present work describes the synthesis of ordered L10 FeNi from elemental Fe and Ni powders by mechanical alloying up to 12 h and subsequent heat treatment at 623 K for 1000 h without a magnetic field and for 4 h in the presence of 1.5 T magnetic field. Also, to address the ambiguity of L10 phase identification caused by the low difference in the X-ray scattering factor of Fe and Ni, synchrotron-based X-ray diffraction is employed, which reveals that 6 h milling is sufficient to induce L10 FeNi formation. Further milling for 12 h is done to achieve a chemically homogeneous powder. The phase fraction of L10-ordered FeNi is quantified to ∼9 wt % for 12 h milled FeNi, which increases to ∼15 wt % after heat treatment. Heat treatment of the milled powder in a magnetic field increases the long-range order parameter (S) from 0.18 to 0.30. Further, the study of magnetic properties reveals a decrease in magnetic saturation and a slight increase in coercivity with the increase in milling duration. At the same time, heat treatment in the magnetic field shows a considerable increase in coercivity.

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Defect generation and analysis in mechanically alloyed stoichiometric Fe–Ni alloys

Cited by 42 publications

References 29 publications

D-shell of iron atom of the amorphous FeCr₁₅B₁₅alloy effective charge change during the crystallization

D-shell of iron atom of the amorphous FeCr₁₅B₁₅alloy effective charge change during the crystallization

Artificially produced rare-earth free cosmic magnet

Formation of L1₀ Ordering in FeNi by Mechanical Alloying and Field-Assisted Heat Treatment: Synchrotron XRD Studies

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Defect generation and analysis in mechanically alloyed stoichiometric Fe–Ni alloys

Cited by 42 publications

References 29 publications

D-shell of iron atom of the amorphous FeCr15B15alloy effective charge change during the crystallization

D-shell of iron atom of the amorphous FeCr15B15alloy effective charge change during the crystallization

Artificially produced rare-earth free cosmic magnet

Formation of L10 Ordering in FeNi by Mechanical Alloying and Field-Assisted Heat Treatment: Synchrotron XRD Studies

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Product

Resources

About

D-shell of iron atom of the amorphous FeCr₁₅B₁₅alloy effective charge change during the crystallization

D-shell of iron atom of the amorphous FeCr₁₅B₁₅alloy effective charge change during the crystallization

Formation of L1₀ Ordering in FeNi by Mechanical Alloying and Field-Assisted Heat Treatment: Synchrotron XRD Studies