Amorphous Fe78Si9B13 Alloy Research Articles

Dipping Paint Curing Amorphous U-Core Used as Reactor

Non-oriented silicon steel (35W310) and amorphous ribbon (Fe78Si9 B13 amorphous alloy) reactor U-cores are made by welding and dipping paint curing, respectively. Amorphous U-core used to make reactor cut sharply eddy current loss due to high electrical resistivity characteristic, thickness of thin ribbon and insulation of dipping paint. The amorphous alloy has high and constant magnetic permeability, and is more suitable for reactor design power to filter high order harmonic component. Keeping off high magnetostriction district with magnetic flux density of 50—100 mT can weaken influence on inductance of inductor due to elongation of magnetostriction. Amorphous alloy has a lower temperature rise using the software Infolytica 7. 2 simulation.

Remelting treatment and heredity phenomenon in the formation of Fe78Si9B13 amorphous alloy

The microstructures of Fe78Si9B13 ingots including the primary master alloy (PMA) and secondary melted alloy (SMA), as well as the precipitates in the annealed amorphous ribbons spun from PMA and SMA ingots have been investigated. The presented data show that SMA ingot performances a better glass forming ability (GFA) than PMA ingot, indicating that remelting treatment can improve the GFA of Fe78Si9B13 alloy. The metastable Fe23B6 phase forms in SMA ribbons after annealing at 600°C and 700°C. The lattice parameter a0 of α-Fe in the annealed SMA ribbons is higher than that in the annealed PMA ribbons, similar to the higher a0 of α-Fe in SMA ingot than that in PMA ingot. The variation of lattice parameter a0 of α-Fe in the present ingots and annealed ribbons shows a heredity phenomenon, which is closely associated with the Fe23B6 structural units (distorted tri-capped trigonal prism clusters) in the melts.

Catalytic oxidation of phenol in wastewater — A new application of the amorphous Fe78Si9B13 alloy

The amorphous Fe78Si9B13 alloy was used as a heterogeneous Fenton catalyst in the process of phenol degradation. The influences of main operating parameters such as reaction temperature, catalyst amount, hydrogen peroxide dosage and initial pH of solution on phenol degradation rate were investigated. The maximum mineralization of phenol was achieved at 60°C, 6 g/L Fe78Si9B13, 0.31 mol/L hydrogen peroxide, with an initial pH of 2.5. More than 99% of phenol was completely removed under the optimum conditions within 10 min for a solution containing 1000 mg/L of phenol. Batch experiments for solutions containing phenol concentrations ranging from 50 to 2000 mg/L were investigated under the above conditions and the same excellent degradation rate was obtained. The Fe78Si9B13 showed better catalytic activity than iron powder and Fe2+. Addition of n-butannol (hydroxyl radical scavenger) decreased the degradation rate of phenol, which demonstrates that hydroxyl radicals were mainly responsible for the removal of phenol. We demonstrated that phenol may be degraded by hydroxyl radicals decomposed by hydrogen peroxide on the surface of Fe78Si9B13 and illustrated the reaction mechanism for this process. This amorphous alloy exhibited high stability in recycling experiments and showed excellent reuse performance even after continuous operations of 8 cycles.

Study on the Magnetic Induction Effect of Rare-Earth La Modified Amorphous Ribbons

Prepared rare-earth La modified amorphous ribbon by doping Rare-earth La in Fe78Si9B13amorphous alloy. Investigated rare-earth content and annealing temperature as well as their influence on the magnetic induction effect and its amplitude. The results show that, when magnetic field is less than 1356 A/m, with the increase of Rare-earth content,the magnetic induction effect first increased and then decreased, when the magnetic field strength greater than 1356 A/m, the Rare-earth content influence little on magnetic induction effect, changing amplitude of magnetic induction effect shows first increased and then decreased with increasing Rare-earth content.

Study on the Activation Energy of Nanocrystallization of Amorphous Fe<sub>78</sub>Si<sub>9</sub>B<sub>13</sub> Alloy Treated by Low Frequency Pulse Magnetic Field

The amorphous Fe78Si9B13 alloy was treated by low frequency pulse magnetic field (LFPMF). The microstructure was observed by Mössbauer spectroscopy and Transmission Electron Microscope. The activation energy of nanocrystallization of amorphous alloy Fe78Si9B13 treated by low frequency pulse magnetic field was determined by differential scanning calorimetry (DSC). The results indicated that the activation energy was decreased from 433.6kJ.mol-1 to less than 200kJ.mol-1 after LFPMF. The nucleating rate of α-Fe(Si) was increased and there was only single phase α-Fe(Si) crystalline formed.

Magnetic Induction Effect of Amorphous Ribbon Modified by Rare-Earth

Prepared rare-earth La modified amorphous ribbon by doping Rare-earth La in Fe78Si9B13 amorphous alloy. Investigated rare-earth content and temperature, as well as their influence on the magnetic induction effect and it’s amplitude. The results show that, when magnetic field is less than 1356 A / m, with the increase of Rare-earth content ,the magnetic induction effect first increased and then decreased, when the magnetic field strength greater than 1356 A / m, the Rare-earth content influence little on magnetic induction effect , changing amplitude of magnetic induction effect shows first increased and then decreased with increasing Rare-earth content; temperature influence little on the magnitude of magnetic induction effect.

Influence of Annealing Process on the Magnetic Induction Effect of FeSiB Amorphous Alloy Ribbons

The influences of frequency, magnetic field density, importing waveform and annealing process on the rangeability of Fe78Si9B13 amorphous alloy ribbon’s magnetic induction effect were studied. The results showed that the rangeability increased with the magnetic field density increased when frequency below 75 kHz, but decreased with the field density increased when frequency over 75 kHz. Compared with quenched ribbons, the rangeability increase after annealed, and the rangeability reached maximum annealed at 300°C for 1.5 hours. When the input waveform is 75 kHz positive pulse and field intensity is 358A/m, the rangeability the quenched ribbons was 2.27V but it reached to 2.85V after annealed at 300°C for 1.5hours.

New Fe-metalloids based nanocrystalline alloys with high Bs of 1.9T and excellent magnetic softness

The melt-spun Fe83.3–84.3Si4B8P3–4Cu0.7 alloys have a heterogeneous amorphous structure including a large amount of α-Fe-like clusters. Compared with the FeSiB alloys, the particle size rapidly decreases from several hundred nanometers to 2–3nm due to the proper amounts of simultaneous P and Cu additions. By controlling the crystallization process, a homogeneous nanocrystalline structure composed by small α-Fe grains with size of 10–17nm in diameter can be realized from the heterogeneous amorphous alloys. The nanocrystallized Fe83.3–84.3Si4B8P3–4Cu0.7 alloys show the extremely high saturation magnetic flux density of 1.88–1.94T sufficiently near to 1.97T of Fe-3.5mass%Si crystalline soft magnetic alloys, and exhibit low coercivity of less than 10A∕m and higher effective permeability of 16 000–25 000 at 1kHz due to the simultaneous realization of the homogeneous nanocrystalline structure and the small magnetostriction of (2–3)×10−6. In addition, the nanocrystalline alloys exhibit the superior core loss to the representative Fe78Si9B13 amorphous alloy at 50Hz.

Plastic deformation behavior of amorphous Fe 78Si 9B 13 alloy at elevated temperature

The plastic deformation behavior of amorphous Fe 78Si 9B 13 alloy was investigated under uniaxial tension and gas pressure bulging. The deformed specimens were studied by means of XRD and SEM. It is shown that amorphous Fe 78Si 9B 13 ribbon has good deformation ability in the temperature range from 450 °C to 500 °C. The elongation of 36.3% and the relative bulging height (RBH) of 0.45 were obtained at 500 °C. In the uniaxial tension test, the amount of the crystalline α-Fe phase increases with deformation temperature below the crystallization temperature, which also suggests that the tensile stress promotes the crystallization of amorphous Fe 78Si 9B 13 ribbon. The suitable gas pressure bulging conditions for the specimens are 500 °C, 3.4 MPa and 30 min.

On the distinct tensile flow of amorphous Fe78Si9B13 alloy at 430°C during continuous annealing

Abstract It was reported in previous paper that there appears a distinct tensile flow of amorphous Fe78Si9B13 ribbon at 430 °C during a continuous heating. In order to investigate the distinct tensile flow, further works were conducted in present work. The broken fracture surface and the side face of the tensile flowed ribbon were observed using SEM. The structural change of the ribbon was detected by means of in situ XRD. The effects of tensile stress, heating rate and preannealing on the distinct tensile flow were tested. The results show that the distinct tensile flow is resulted from a structural transition and annealing condition affects it markedly. It is concluded that the structural transition occurring at 430 °C is the nucleation of α-Fe (Si) crystallites and the effect of heating rate on the distinct tensile flow is closely related to the structural relaxation of amorphous Fe78Si9B13 alloy.

Gas Pressure Forming of Amorphous Fe<sub>78</sub>Si<sub>9</sub>B<sub>13</sub> Alloy

The deformation behavior of gas pressure forming of amorphous Fe78Si9B13 alloy was investigated under equibiaxial tension. The gas pressure forming was carried out in the temperature range of 430°C~530°C below the crystallization temperature Tx and die apertures of 5mm~10mm. The dome height and amorphous ribbon thickness of deformed specimens at the pole was measured. It was found that amorphous Fe78Si9B13 alloy had exhibited good plasticity in the experimental temperature range. The near-semisphere specimens of the radius 5mm and the height 4.5mm were obtained from the gas-pressure forming at 450°C and 530°C for 30min, which is similar to the superplastic forming.

Evolution of a sharp {110} texture in microcrystalline Fe78Si9B13 during magnetic crystallization from the amorphous phase

The effect of magnetic crystallization on texture evolution and control in nanocrystalline materials has been studied using a melt-spun amorphous Fe78Si9B13 alloy. The magnetic crystallization was conducted at temperatures ranging from 653 to 853 K in a magnetic field up to 6 T. The temperatures used for magnetic crystallization were chosen on the basis of the Curie and crystallization temperatures of the amorphous phase, and the Curie temperature of the crystallized phase. The resultant microstructure was characterized by X-ray diffraction and FE-SEM/EBSP/OIM techniques. It was found that a sharp {110} texture developed when the amorphous precursor was crystallized at 853 K in a magnetic field of 6 T applied in a direction parallel to the ribbon surface.

The Control of Texture and Grain Boundary Microstructure by Magnetic Annealing

This paper gives an overview of our recent works on the effect of magnetic annealing, i.e. annealing in a magnetic field, on the evolution of texture and grain boundary microstructure in ultra-fine grained and nanocrystalline magnetic materials differently produced; rapidly solidified Fe-6.5mass%Si ribbons, electrodeposited nanocrystalline nickel, and nanocrystalline Fe78Si9B13 alloy ribbon crystallized from the amorphous state. It was found that the effect of magnetic annealing was powerful and useful for controlling grain growth resulting in the evolution of different types of texture and grain boundary microstructure, depending on the condition of magnetic annealing. In particular, the magnetic crystallization of amorphous Fe78Si9B13 alloy was found to be powerful for producing a nanocrystalline material with a sharp texture and a special grain boundary microstructure.

Vickers Microhardness and Hyperfine Magnetic Field Variations of Heat Treated Amorphous Fe78Si9B13 Alloy Ribbons

Amorphous Fe78Si9B13 alloy ribbons were heat treated between 296 and 763 K, using heating rates between 1 and 4.5 K/min. Whereas one ribbon partially crystallized at T x = 722 K, the other one partially crystallized at T x = 763 K. The partially crystallized ribbon at 722 K, heat treated using a triangular form for the heating and cooling rates, was substantially less fragile than the partially crystallized at 763 K where a tooth saw form for the heating and cooling rates was used. Vickers microhardness and hyperfine magnetic field values behaved almost concomitantly between 296 and 673 K. The Mossbauer spectral line widths of the heat-treated ribbons decreased continuously from 296 to 500 K, suggesting stress relief in this temperature range where the Vickers microhardness did not increase. At 523 K the line width decreased further but the microhardness increased substantially. After 523 K the line width behave in an oscillating form as well as the microhardness, indicating other structural changes in addition to the stress relief. Finally, positron lifetime data showed that both inner part and surface of Fe78Si9B13 alloy ribbons were affected distinctly. Variations on the surface may be the cause of some of the high Vickers microhardness values measured in the amorphous state.

アモルファス合金薄帯積層型複合材の確率疲労特性に関する研究

Amorphous alloy ribbons have no crystalline structure and they have superiority in the electomagnetic and mechanical properties. Due to their useful electomagnetic property, the amorphous ribbons are widely used, nowadays, in the various products such as core of current transformers and electric motors. But we have a difficulty that the thickness of the amorphous ribbon is restricted within a certain value in order to realize the rapid quenching. Thus amorphous ribbons must be put together to some extent in order to use as mechanical components. In this study, a number of thin ribbons of Fe78B13Si9 amorphous alloy are piled up and bonded by an adhesive. Statistical fatigue properties of such multilayer composites are examined by performing fatigue tests and fatigue mechanisms are discussed.

Core Losses and Soft Magnetic Properties of Nanocrystalline Fe-Zr-Nb-B Alloys with Zero-Magnetostriction

AbstractThe structure, the soft magnetic properties and the core losses for Fe-Zr-Nb-B(-Cu) nanocrystalline alloys were investigated. It has been already reported that the typical ternary nanocrystalline Fe90Zr7B3 and Fe84Nb7B9 alloys exhibit good soft magnetic properties and a small negative and a small positive magnetostriction (λs), respectively. The soft magnetic properties of the nanocrystalline Fe84–90(Zr, Nb)7B3–9 quaternary alloys with mixed compositions of Fe90Zr7B3 and Fe84Nb7B9 cannot be improved whereas very small magnetostrictions are obtained. The quaternary alloys with 7 at% (Zr + Nb) have structures of an amorphous with α-Fe phases on the free and roll-contacted surfaces at an as-quenched state. The crystalline surface layers deteriorate the soft magnetic properties at a crystallized state. The high saturation magnetic induction of 1.64 T, the high permeability of 60,000 at 1 kHz and the very low core loss of 0.9 W/kg at 1.4 T and 50 Hz are obtained for the Fe85.5(Zr1/3Nb2/3)6B8.5 alloy containing 6 at% of (Zr + Nb) content with nearly zero-λs produced by crystallizing the single amorphous phase without the crystalline surface layers. The thermal stability of the core loss of the quaternary alloy is significantly higher than that of the Fe78Si9B13 amorphous alloy. The crystalline surface layers of the Fe84–90(Zr, Nb)7B3–9 quaternary alloys disappear by 1 at% Cu addition, which results in significant improvement of the soft magnetic properties at a crystallized state.

Low core losses and soft magnetic properties of Fe–Al–Ga–P–C–B–Si glassy alloy ribbons with large thicknesses

The structure, soft magnetic properties, and core losses were investigated for a Fe77Al2.14Ga0.86P8.4C5B4Si2.6 glassy alloy with a sheet thickness in a wide range from 30 to 240 μm prepared by the melt-spinning technique. The maximum thickness (tmax) for glass formation and the thermal stability (ΔTx) of the supercooled liquid region defined by the difference between the crystallization temperature (Tx) and the glass transition temperature (Tg) are about 220 μm and 35 K, respectively. The saturation magnetization (σs) of this glassy alloy is about 1.5 T. The effective permeability at 1 kHz is as high as 12 000 in a thickness of 30 μm and it maintains high values above 4400 up to a thickness of tmax. The coercive force is kept at a low level, under 3 A/m up to tmax. This glassy alloy also shows low core loss values of 0.1–0.3 W/kg at f=50 Hz and Bm=1.0 T in the thickness from 30 to 220 μm. On the other hand, a Fe78Si9B13 amorphous alloy shows almost the same low core losses as that of the glassy alloy only in a thickness of less than 70 μm. The difference between the dependence of the soft magnetic properties and the core loss on the thickness of these alloys should arise from their difference in ability of glass forming. The Fe–Al–Ga–P–C–B–Si glassy alloys should be very useful for inductive applications because of their thick ribbon shape and good soft magnetic properties in addition to low core loss.

高飽和磁化を有するＦｅ基金属ガラスの軟磁気特性

The compositional dependence of the glass-forming ability and magnetic properties of Fe-Al-Ga-P-C-B- (Si) glassy alloys was investigated. The saturation magnetization (σs) increase with increasing Fe content. While the maximum thickness for glass formation (tmax) decreases when the (P, C, B) is replaced by Fe, it hardly does so when the (Al, Ga) is replaced by Fe. When P is replaced by Si, tmax increases. As a result, a high σs of 207 × 10-6 Wbm kg-1 and a large tmax of 220 μm were simultaneously obtained in a Fe77Al2.14Ga0.86P8.4C5B4Si2.6 glassy alloy. The core loss of this glassy alloy with a smaple thickness of 100μm at f=50 Hz and Bm = 1.0 T was 0.22 Wkg, which is lower than those of 6.5%Si-Fe alloy and amorphous Fe78Si9B13 alloy with the same sample thickness. Therefore, it can be said that the Fe-Al-Ga-P-C-B-Si glassy alloys are useful for inductive applications.

Low core losses of nanocrystalline Fe–M–B (M=Zr, Hf, or Nb) alloys

Magnetic core properties, core loss, permeability, and saturation magnetic induction of bcc-nanocrystalline Fe–M–B (M=Zr, Hf, and Nb) alloys produced by annealing a melt-spun amorphous phase were investigated in a ring-shaped form with the aim of clarifying the application potential as a core material. The bcc alloys exhibit high saturation induction (Bs) from 1.49 to 1.63 T combined with high permeability (μe) from 22 000 to 32 000 at 1 kHz and 0.4 A/m. The bcc Fe–M–B (M=Zr, Hf, or Nb) alloys also show low core losses (W) from 1.4×10−1 to 2.1×10−1 W/kg at 50 Hz and 1.4 T and from 1.70 to 2.50 W/kg at 1 kHz and 1.0 T. The W values attained for the bcc Fe–M–B (M=Zr, Hf, and Nb) alloys are smaller by 60%– 90% at 50 Hz and 1.4 T and 50%–70% at 1 kHz and 1.0 T, as compared with those for an amorphous Fe78Si9B13 alloy in practical use as a transformer core material. The low W values for the bcc-nanocrystalline alloys are presumably due to the small anomaly factor comparable to a Co-based amorphous alloy. The comparison of the present data with those for the amorphous Fe78Si9B13 alloy indicates that the bcc-nanocrystalline Fe–M–B (M=Zr, Hf, and Nb) alloys are promising for practical use as core materials.

Investigation of Effect of Annealing the Fe78Si9B13Amorphous Alloy Using the EELS Method and the Hall Effect

Investigation of Effect of Annealing the Fe₇₈Si₉B₁₃Amorphous Alloy Using the EELS Method and the Hall Effect