Investigation into the Effect of Thermal Treatment on the Obtaining of Magnetic Phases: Fe5Y, Fe23B6, Y2Fe14B and αFe within the Amorphous Matrix of Rapidly-Quenched Fe61+xCo10−xW1Y8B20 Alloys (Where x = 0, 1 or 2)

Vizureanu, Petrică; Nabiałek, M.; Sandu, Andrei Victor; Jeż, B.

doi:10.3390/ma13040835

Cited by 8 publications

(5 citation statements)

References 41 publications

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“…This means that privileged system clusters are much easier to form in four-component systems. In numerous studies [28] of alloys with the addition of Y (FeCoYB), it has been demonstrated that one of the most frequently formed crystalline phases is magnetically soft phase αFe, magnetically semi-hard phase Fe 5 Y, and magnetically hard phase Y 2 Fe 14 B. In the case of the FeNbYB alloy, an axial shape of the hysteresis loop was observed, indicating the appearance of a magnetic phase in the alloys with hard or semi hard magnetic properties.…”

Section: Discussionmentioning

confidence: 99%

The Process of Magnetizing FeNbYHfB Bulk Amorphous Alloys in Strong Magnetic Fields

et al. 2020

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The structure of amorphous alloys still has not been described satisfactorily due to the lack of direct methods for observing structural defects. The magnetizing process of amorphous alloys is closely related to its disordered structure. The sensitivity of the magnetization vector to any heterogeneity allows indirect assessment of the structure of amorphous ferromagnetic alloys. In strong magnetic fields, the magnetization process involves the rotation of a magnetization vector around point and line defects. Based on analysis of primary magnetization curves, it is possible to identify the type of these defects. This paper presents the results of research into the magnetization process of amorphous alloys that are based on iron, in the areas called the approach to ferromagnetic saturation and the Holstein-Primakoff para-process. The structure of a range of specially produced materials was examined using X-ray diffraction. Primary magnetization curves were measured over the range of 0 to 2 T. The process of magnetizing all of the tested alloys was associated with the presence of linear defects, satisfying the relationship D di p < 1 H . It was found that the addition of yttrium, at the expense of hafnium, impedes the magnetization process. The alloy with an atomic content of Y = 10% was characterized by the highest saturation magnetization value and the lowest value of the D spf parameter, which may indicate the occurrence of antiferromagnetic ordering in certain regions of this alloy sample.produced in the form of thin ribbons, using the melt-spinning method [4], present particularly good properties. Materials of this type are characterized by a high value of saturation magnetization (above 1.5 T) and a low value of coercive field (approximately 1 A/m) [5][6][7][8][9]. These material samples are extremely easy to magnetize, partly due to their dimensions. Amorphous ribbons have thicknesses of up to several tens of µm. Unfortunately, these dimensions significantly limit the applications of these materials. The so-called bulk amorphous alloys comprise a relatively new group of promising materials. These materials are produced by a rapid-quenching process in copper molds. The most well-known production methods are the injection-and suction-casting methods [10,11]. In this way, at a cooling rate of 10 −1 -10 3 K/s, iron-based alloys with dimensions exceeding 10 mm can be produced [12][13][14]. However, due to their high proportions of non-magnetic component elements, such as: B, C, Zr, Y, Mo, Nb, Hf, or Cr, these alloys do not exhibit the best magnetic properties. A compromise that combines relatively good magnetic properties (saturation magnetization greater than1T, coercive field less than 50 A/m) with favorable alloy geometry (diameter up to 3 mm) exists in the form of alloys with a content of approximately 65%-75% magnetic elements [15][16][17][18].The process of magnetizing amorphous alloys does not differ significantly from their crystalline counterparts. Figure 1 shows a diagram of the primary magnetization cur...

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Section: Discussionmentioning

confidence: 99%

The Process of Magnetizing FeNbYHfB Bulk Amorphous Alloys in Strong Magnetic Fields

et al. 2020

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“…Depending on the cooling rate and chemical composition, it is possible to produce alloys with an amorphous or nanocrystalline structure in a one-stage process [1]. The type of phases formed during solidification determines the properties of these materials -rapid quenched alloys may have hard magnetic properties (for example, with the Y 2 Fe 14 B phase [2]), semi-hard magnetic properties (with the Fe 5 Y phase [3]), or soft magnetic properties (with the α-Fe, Fe 2 B, Fe 23 B 6 , Fe 3 B [4][5][6]). The properties of these alloys are related, among other things, to the distances between magnetic atoms [7] and the size of crystal grains [8].…”

Section: Introductionmentioning

confidence: 99%

Influence of a Small Addition of Cu on the Magnetization Process of Rapid Quenched Alloys in Strong Magnetic Fields

Jeż,

Postawa,

Kalwik

et al. 2023

Acta Phys. Pol. A

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The magnetization process is based on bringing about a unified arrangement of the magnetic domains. During this process, there are shifts and then the rotations of the domain walls. At a later stage, domains with a direction of magnetization that do not correlate with the applied magnetic field disappear. The turnover depends on the size of the domains. For an amorphous structure, the key factors determining the size of the magnetic domains are the distance between the magnetic atoms and the possible presence of crystalline grains. The paper presents the results of research on the influence of Cu addition on the distances between magnetic atoms and the magnetization process in high magnetic fields. The structure of the alloys was studied using X-ray diffraction. The mean grain size was estimated using the Scherrer method. The magnetic properties were determined on the basis of measurements with a vibrating magnetometer. A numerical analysis of the primary magnetization curves was performed. Despite the significant reorganization of the structure, no changes in the distance between the magnetic atoms were observed, as indicated by slight changes in the D spf parameter. It was found that a small addition of Cu positively influences the improvement of the magnetic properties, in particular the reduction of the value of the coercive field.

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“…There are mainly four types of intermetallic compounds in M-B systems (M = Fe, Co, Ni): MB, M 2 B, M 3 B, and M 23 B 6 , whose formations are dependent on the solidification routes [13,14], which are affected by the composition and technology parameters, such as the cooling rate, the undercooling, the holding time, etc., and which show different magnetic properties because of the different contents of boron. It is worth noting that the Co 23 B 6 metastable phase is usually regarded as a good candidate for enhancing the soft properties [15], and, in addition, the Co 2 B phase with the higher boron content has an intrinsic hardness of about 816 HV, which is comparable to the hard chromium (860 HV). Its high hardness makes it a potential wear-resisting protective coating [16].…”

Section: Introductionmentioning

confidence: 99%

Re-Examination of the Microstructural Evolution in Undercooled Co-18.5at.%B Eutectic Alloy

et al. 2022

Materials

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The undercooling (∆T) dependencies of the solidification pathways, microstructural evolution, and recalescence behaviors of undercooled Co-18.5at.%B eutectic alloys were systematically explored. Up to four possible solidification pathways were identified: (1) A lamellar eutectic structure consisting of the FCC–Co and Co3B phase forms, with extremely low ΔT; (2) The FCC–Co phase primarily forms, followed by the eutectic growth of the FCC–Co and Co2B phases when ΔT < 100 K; (3) As the ΔT increases further, the FCC–Co phase primarily forms, followed by the metastable Co23B6 phase with the trace of an FCC–Co and Co23B6 eutectic; (4) When the ΔT increases to 277 K, the FCC–Co phase primarily forms, followed by an FCC–Co and Co3B eutectic, which is similar in composition to the microstructure formed with low ΔT. The mechanisms of the microstructural evolution and the phase selection are interpreted on the basis of the composition segregation, the skewed coupled zone, the strain-induced transformation, and the solute trapping. Moreover, the prenucleation of the primary FCC–Co phase was also detected from an analysis of the different recalescence behaviors. The present work not only enriches our knowledge about the phase selection behavior in the undercooled Co–B system, but also provides us with guidance for controlling the microstructures and properties practically.

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Investigation into the Effect of Thermal Treatment on the Obtaining of Magnetic Phases: Fe5Y, Fe23B6, Y2Fe14B and αFe within the Amorphous Matrix of Rapidly-Quenched Fe61+xCo10−xW1Y8B20 Alloys (Where x = 0, 1 or 2)

Cited by 8 publications

References 41 publications

The Process of Magnetizing FeNbYHfB Bulk Amorphous Alloys in Strong Magnetic Fields

The Process of Magnetizing FeNbYHfB Bulk Amorphous Alloys in Strong Magnetic Fields

Influence of a Small Addition of Cu on the Magnetization Process of Rapid Quenched Alloys in Strong Magnetic Fields

Re-Examination of the Microstructural Evolution in Undercooled Co-18.5at.%B Eutectic Alloy

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