Mössbauer study of amorphous Fe40Ni40PxB20−x

The hyperfine field distributions of amorphous Fe₄₀Ni₄₀P_xB_20?x (x=10, 12, 14, 17) samples before and after different heat treatments have been determined by means of Mössbauer spectroscopy. All of these P(H) curves are characterized by a main high field maximum and an additional low field maximum, respectively. The asymmetry of distributions of high field component in P(H) of Fe₄₀Ni₄₀P_xB_20?x increases progressively from Fe₄₀Ni₄₀P₁₀B₁₀ to Fe₄₀Ni₄₀P₁₇B₃. The distributions of low field component in P(H) are affected differently by the annealing temperature. The results indicate that the phospoorus element plays an important role in the hyperfine interactions of amorphous Fe₄₀Ni₄₀P_xB_20?x The influence of annealing atmosphere has been discussed.     

Radio-frequency annealing effects in amorphous Fe40Ni40B20

The influence of radio frequency (rf) magnetic fields on the properties of amorphous Fe₄₀Ni₄₀B₂₀ was studied using Mössbauer spectroscopy. The measurements were performed with frequencies of 67 and 53 MHz and rf field intensity in the range of 1 to 12 Oe. The narrowing of the hyperfine spectra due to the rf field and the formation of rf sidebands were observed. The effect of instability and crystallization of the amorphous metal enhanced by the rf field at temperatures much lower than the crystallization temperature was observed.     

Characterizing structures in the Fe−Ni−B amorphous system

Amorphous alloys Fe₈Ni_80?XB₂₀ (x=20?60) and (Fe_0.5Ni_0.5)_100?yB_y (y=16?25) have been thermally treated between 300k and 800k in a differential scanning calorimeter (DSC). The phases have been determined using Mössbauer spectroscopy and x-ray diffraction methods. The crystallization temperatures, heats of crystallization and the crystallization products of the amorphous(a)-Fe?Ni?B system vary with the composition of Fe and with the that of B. Basing on the variations of these factors the short range order (sro) of the amorphous Fe?Ni?B alloy system is discussed.     

Oxidation state and short range order at the surfaces of amorphous Fe40Ni40P14B6 ribbons

Conversion electron Mössbauer spectroscopy (CEMS) was used to study the oxidation state at the surfaces of amorphous Fe₄₀Ni₄₀P₁₄B₆ ribbons obtained by melt-spinning in air and vacuum heated at 583 K. Different concentrations of ferric and ferrous ions depend on the different behaviour of phosphorous diffusion towards the two surfaces during low annealing temperature.     

Mössbauer study of magnetic anisotropy and structural relaxation in amorphous Fe40Ni40P x B20−x alloys

The amorphous Fe₄₀Ni₄₀P _x B_20?x (x=0, 10, 12, 14, 17) alloys before and after annealing have been studied by means of Mössbauer spectroscopy, etc. Heat treatment of various samples were performed at 225, 250, 275, 300, 325 and 350°C, respectively, for 1 h in a quartz tube in an argon atmosphere. The results show that the magnetic anisotropy and structural relaxation in amorphous Fe₄₀Ni₄₀P _x B_20?x are related to the phosphorus element concentrations involved and the annealing temperatures. A possible mechanism of two-stage relaxation processes below the glass transition temperature is discussed.     

Mössbauer study of corrosion products formed on Fe80B20 and Fe40Ni40(MoB)20 amorphous alloys in an SO2-polluted atmosphere

ICEMS, XPS, XRD, and AES have been used to study the corrosion layers formed on two metallic glasses, Fe₈₀B₂₀ and Fe₄₀Ni₄₀(MoB)₂₀ (2605 and 2826 MB, Allied Company), exposed to an SO₂-polluted humid atmosphere. The iron-containing corrosion products are the same found for pure iron in the same environment, but different relative concentrations were clearly evidenced by ICEMS results. Elemental sulphur, Ni(OH)₂, and B(OH)₃, the latter enriched at the surface, were found by XPS, XRD, and AES.     

Magnetic and structural behaviour of Fe40Ni40B20 alloys as a function of the melt-spinning parameters

Changes in structure and magnetic properties of Fe₄₀Ni₄₀B₂₀ alloys were investigated as a function of the surface velocity, V_u, of the quenching substrates in the range 8 m/s≤V_u≤70 m/s. For V_u>30 m/s no changes were found. Below a “critical” region, 20 m/s≤V_u≤30 m/s, where changes in spin orientation are observed, crystallization processes are frozen in. The structure of one of the crystallization products, (FeNi)₃B, appears to depend on the surface speed V_u.     

Short range order at the surfaces of annealed amorphous Fe40Ni40P14B6 ribbons

Conversion electron Mössbauer spectroscopy (CEMS) and gamma transmission Mössbauer spectroscopy were used to measure the effects of annealing at 583 K in vacuum into about 200 nm thick layer below the two surfaces and on the bulk of theFe ₄₀ Ni ₄₀ P ₁₄ B ₆ amorphous ribbons prepared by means of melt-spinning technique. The results show a large distribution of hyperfine magnetic fields on the bulk and in the surfaces of the samples. By means of selective analysis of hyperfine magnetic field distribution, we have evalueded the correlation between the different degree of short range orders at the surfaces and in the bulk of the samples, and the phosphorus segregation associated with mechanical cubrittlement induced at low annealing temperature.     

The activation energy of crystallization of amorphous Fe40Ni40P14B6

The isothermal crystallization of Fe₄₀Ni₄₀P₁₄B₆ (Metglas 2826) has been studied by transmission electron microscopy, using static observations of partially crystallized ribbons at room temperature and in situ dynamic registration of the crystallization process at elevated temperatures. At all temperatures crystallization takes place by the nucleation and growth of individual crystals. Analysis of the transformation kinetics allowed to determine the nucleation rates and the activation energy for crystal growth. The growth velocity of the crystal phase was found to be controlled by the diffusion coefficient of phosphorus in this alloy withD ₀=2.5×10^10±1cm{swu2}/s andQ=(3.4±0.15)eV.     

Diffusion of Au and Cu in amorphous Fe80B20 and Fe82B18 alloys

Diffusion rates (D) of Au in two amorphous alloys, Fe₈₀B₂₀ and Fe₈₂B₁₈, and of Cu in amorphous Fe₈₂B₁₈ alloy were measured in the temperature range 546–645 K by using the technique of Rutherford backscattering spectrometry (RBS) and Auger electron spectroscopy (AES), respectively. The diffusion of Au was found to be 3 to 6 times faster in Fe₈₀B₂₀ than in Fe₈₂B₁₈, though both the alloys had almost similar crystallization temperatures. The observed differences in the diffusion rates corroborate the fact that Fe₈₀B₂₀ has a more open structure than Fe₈₂B₁₈ as revealed from the reported values of the metal packing fractions of these two alloys. Also, the diffusivities of smaller sized Cu atoms (radius: 0.128 nm) were found to be higher by more than an order of magnitude than those of larger sized Au atoms (radius: 0.146 nm), suggesting a dependence ofD on the size of the diffusing species.     

Investigations of Ar+ implantation and proton irradiation of amorphous Fe40Ni40B20 samples by Mössbauer techniques

The effect of the implantation of 150 keV Ar⁺ ions at different doses on the surface of amorphous Fe₄₀Ni₄₀B₂₀ and the changes in the bulk properties following proton irradiations are investigated by conversion electron and transmission Mössbauer spectroscopy respectively. In the former case a correlation between the total Mössbauer absorption and the total energy deposited by incident Ar⁺ ions is established, indicating the development of certain stresses in the material, affecting the inter and intra molecular bonding in the near surface region. On the other hand, the proton irradiation seems to cause a reorientation of the atomic spins and also the formation of an additional Fe or Fe?Ni rich phase in the sample. Also the low field A.C. susceptibility is found to decrease as a function of the dose of incident protons. Possible reasons for the above behaviour are discussed.     

Magnetic properties of Fe and Ni films evaporated in poor vacuum

To examine the pressure dependence of magnetic characteristics of Fe and Ni films, the films were prepared in vacuum ranging from 10^–5 to 10^–2 torr.Saturation magnetizationM _s ^* , perpendicular anisotropyK ^* and coercive forceH _c for Fe and Ni films deposited at around 10^–5 torr were in good agreement with the values obtained by others. When the film thickness was less than 500 ,M _s ^* for Fe films increased with pressure, while it decreased monotonically for Ni films. At pressures between 2×10^–3 and 10^–2 torr,M _s ^* decreased rapidly for Fe but it increased slightly for Ni. This interesting behaviour was most marked with film thickness of about 500 . Corresponding to the change inM _s ^* , bothK ^* andH _c also changed with deposition pressure.The result should be explained in terms of the presence of Fe₄N, Fe₈N and Ni₃N, as well as the macroscopic and microscopic structures of films.     

The influence of the metalloid elements on the magnetic properties of amorphous Fe40Ni40PyB20−y

The Curie temperatures (T_C) and the hyperfine interactions of amorphous Fe₄₀Ni₄₀P_yB_20?y(0≤y>≤20) have been determined by ⁵⁷Fe Mössbauer spectroscopy. In this series of amorphous solid with a fixed transition-metal content, the metalloid atoms are shown to have a noticeable effect on T_C, isomer shift and hyperfine field distribution.     

Hyperfine interactions, structure and magnetic properties of nanocrystalline Co–Fe–Ni alloys prepared by mechanical alloying

Mechanical alloying method was used to prepare nanocrystalline Co₅₀Fe₄₀Ni₁₀, Co₅₂Fe₂₆Ni₂₂ and Co₆₅Fe₂₃Ni₁₂ alloys. X-ray diffraction proved that during milling Co–Fe-based solid solution with b.c.c. lattice was formed in the case of Co₅₀Fe₄₀Ni₁₀, while for Co₅₂Fe₂₆Ni₂₂ and Co₆₅Fe₂₃Ni₁₂ compositions Co–Ni-based solid solutions with f.c.c. lattice were obtained. Mössbauer spectroscopy revealed similar values of the average hyperfine magnetic fields for all alloys, e.g. 32.17, 32.24 and 31.21 T for Co₅₀Fe₄₀Ni₁₀, Co₅₂Fe₂₆Ni₂₂ and Co₆₅Fe₂₃Ni₁₂ alloys, respectively. Magnetization measurements allowed to determine the effective magnetic moment, Curie temperature, saturation magnetization and coercive field for the obtained alloys.     

Phase transition in metallic glasses Fe66Co12Si9B13 and Fe66Ni12Si9b13

Phase transitions were analysed during annealing of amorphous metallic glasses Fe₆₆Co₁₂Si₉B₁₃ and Fe₆₆Ni₁₂Si₉B₁₃. They were measured by means of X-ray diffraction, electrical and Hall resistivity methods. Forming crystalline phases were identified. Those for metallic glasses with cobalt are α-Fe, Fe₃B and Co₂B while those with nickel are α-Fe, Fe₂B, Ni₂B.     

Influence of doping with titanium on the electronic structure of Ni3Fe and Ni3Mn in ordering

The specific electrical resistance , mean magnetic moment of an atom of the alloy, and the anomalous Hall (R_s) and Nernst-Ettinghausen (Q_s) constants of ordered alloys Ni₃(Fe, Ti) and Ni₃(Mn, Ti) are investigated. It is suggested that there is an additional degree of delocalization of the 3d electrons of the system Ni₃(Mn, Ti) and increase in the degree of localization of 3d electrons of the system Ni₃(Fe, Ti) with small additions of Ti, with increase in the long-range-order parameter. A model of the electronic structure of the given alloys is discussed.Translated from Izvestiya Vysshikh Uchebnykh Zavedenii, Fizika, No. 10, pp. 56–59, October, 1981.     

High-magnetic-field magnetization and magnetoresistance of some amorphous ferromagnets

Measurements of isothermal magnetization and magnetoresistance at T = 4.0-4.2 K and 15 ? H ? 132 kG on the amorphous ferromagnets Fe₈₀B₂₀, Fe₇₈Mo₂B₂₀, Fe₄₀Ni₄₀P₁₄B₆, and Fe₃₂Ni₃₆Cr₁₄P₁₂B₆ indicate a relatively large H-induced increase (3.6%) in the high-magnetic-field magnetization of the latter alloy, and marked differences in the magnitude and sign of the high-field magnetoresistance of the four alloys. The results are qualitatively interpreted in terms of internal effective field distributions which include a small fraction of atomic spins in negative field sites.     

Magnetic properties of lithographically defined lateral Co/Ni80Fe20 wires

A novel micro-fabrication technique has been used to create an array of lateral magnetic multilayers consisting of micron-sized sputtered Co and Ni₈₀Fe₂₀ wires. The structures were fabricated using conventional optical lithography and a combination of hard and soft lift-off methods. For the field applied parallel to the wires intrinsic easy axis, we observed two switching fields corresponding to the distinct coercive field of the Ni₈₀Fe₂₀ wires (H_c1) and Co wires (H_c2) constituting the lateral multilayer wire array. A state of anti-parallel relative alignment of magnetization was observed when the applied field is greater than the switching field of Ni₈₀Fe₂₀ wires but less than the switching field of Co wires. We found the region of anti-parallel alignment of magnetization between the Co and Ni₈₀Fe₂₀ wires to be very sensitive to the relative orientation of the applied magnetic field.     

Study of spin-wave dynamics in Fe65Ni35 ferromagnetic via small-angle polarized-neutron scattering

The results of studying the spin dynamics of a classical Fe₆₅Ni₃₅ invar alloy are presented and analyzed. The investigations are performed via small-angle polarized-neutron scattering in the oblique geometry of a magnetic field at various temperatures (T < T _C). This approach is based on the analysis of left-right asymmetry in the magnetic scattering of polarized neutrons. The asymmetry effect arises when the magnetization direction of a sample is inclined with respect to the wave vector of the incident beam. The spin-wave scattering is concentrated within a range bounded by the cutoff angle θ_c determined by the magnetic field: θ _c ² (H) = θ ₀ ² ?(gμ_B H)θ₀/E, where \(\theta _0 = \hbar ^2 \frac{1} {{2Dm_n }}\) , H is the external magnetic field, E is the initial neutron energy, D is the spin-wave stiffness constant, and m _n is the neutron mass. The scattering is blurred by spinwave damping in the vicinity of the cutoff angle. The spin-wave stiffness constant can be obtained from a comparison of the asymmetric contribution to scattering and a model function. The temperature dependence D = D(T) is well defined by the expression D = D ₀ |τ| ^x , where \(\tau = 1 - \frac{T} {{T_C }}\) , x = 0.47 ± 0.01, D ₀ = 137 ± 3 meVŲ, and τ > 0.1 in the entire temperature range. The given method enables us to construct the temperature dependence of the spin-wave stiffness constant with a high accuracy and a small step.