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Fig. 7. (a) Hysteresis loops for Pd-Fe films with different compositions. (b) Magnetization (solid circles) and coercivity (solid squares) as a function of the iron content x in the Pd-Fe films. Dash line is a liner fit for the magnetization, the solid lines connect experimental point for the coercive field as a function of x. the second magnetic phase in the samples. for the magnetization, the solid lines connect experimental point for the coercive field as a function of x.

Figure 7 (a) Hysteresis loops for Pd-Fe films with different compositions. (b) Magnetization (solid circles) and coercivity (solid squares) as a function of the iron content x in the Pd-Fe films. Dash line is a liner fit for the magnetization, the solid lines connect experimental point for the coercive field as a function of x. the second magnetic phase in the samples. for the magnetization, the solid lines connect experimental point for the coercive field as a function of x.

Related Figures (6)

Fig. 1 X-ray diffraction patterns of Pd-Fe alloys deposited onto copper (a) and brass (b) substrate; the Fe percentage is indicated over the corresponding curve. The percentage content of iron is given as a measure of palladium substitution. different composition are presented. The films were deposited on top of copper and brass substrates.
Fig. 1 X-ray diffraction patterns of Pd-Fe alloys deposited onto copper (a) and brass (b) substrate; the Fe percentage is indicated over the corresponding curve. The percentage content of iron is given as a measure of palladium substitution. different composition are presented. The films were deposited on top of copper and brass substrates.
results are confirmed by the TEM investigations (see Fig. 2). The peaks corresponding to the deposited films are substantially broadened. The analysis of the yroadening shows that it takes place due to the small size of the crystallites. The film with 91% Fe s a bcc solid solution of Pd in Fe (here and below the percentage content of iron is given as a neasure of palladium substitution). The films with 24, 32 and 57% of Fe consist of a fcc solid olution. The considerable change in the intensity of the (111) and (200) lines of the Pd;_,Fe, alloy lemonstrate the presence of the (111) texture in the grains orientation relatively to the substrate surface. The XRD data show that the Pd- and Fe-related solid solution area for the Pd;_,Fe, films leposited at 50°C is considerably enlarged as compared to the bulk phase diagram. We consider his result as a size effect of crystallites formed in the films. It is shown that decrease of the grain ize can result in a drastic rise of the mutual solubility of the binary system components The X RD nciite am rnanfirmadn hiv tha TEM intrachnatnne (coo Gin 9) iron content (74%) the crystallites of irregular shape with a size of about 200 nm are observed.
results are confirmed by the TEM investigations (see Fig. 2). The peaks corresponding to the deposited films are substantially broadened. The analysis of the yroadening shows that it takes place due to the small size of the crystallites. The film with 91% Fe s a bcc solid solution of Pd in Fe (here and below the percentage content of iron is given as a neasure of palladium substitution). The films with 24, 32 and 57% of Fe consist of a fcc solid olution. The considerable change in the intensity of the (111) and (200) lines of the Pd;_,Fe, alloy lemonstrate the presence of the (111) texture in the grains orientation relatively to the substrate surface. The XRD data show that the Pd- and Fe-related solid solution area for the Pd;_,Fe, films leposited at 50°C is considerably enlarged as compared to the bulk phase diagram. We consider his result as a size effect of crystallites formed in the films. It is shown that decrease of the grain ize can result in a drastic rise of the mutual solubility of the binary system components The X RD nciite am rnanfirmadn hiv tha TEM intrachnatnne (coo Gin 9) iron content (74%) the crystallites of irregular shape with a size of about 200 nm are observed.
Fig. 3. SEM images of films surfaces with different compositions: (a) 14; (b) 52; and (c) 74% of Fe.
Fig. 3. SEM images of films surfaces with different compositions: (a) 14; (b) 52; and (c) 74% of Fe.
epitaxy on a single crystalline MgO substrate [4]. The ferromagnetic resonance (FMR) is a very accurate and sensitive technique which allows tc etermine the magnetic anisotropy fields of thin magnetic films [5]. Experimental FMR spectra fo: ne film containing 14% of iron, with a thickness of 100 nm, are given in Fig. 5; and in Fig. 6 the ngular dependence of the in-plane resonance field (Fig. 6a) and the temperature dependence of the hard axis’ field for resonance (Fig. 6b) are shown. The angular dependences show an anomalously igh uniaxial magnetic anisotropy and unconventional triple-line stricture of the FMR spectrum H1, H2, H3) in the film plane, measured at low temperatures (20K, see Figs. 5a and 6a). As the 2mperature increases towards room temperature (see Fig. 6b), the magnetic anisotropy dramatically ecreases, and two of the three components of the FMR signal (H2 and H3) merge. From the
epitaxy on a single crystalline MgO substrate [4]. The ferromagnetic resonance (FMR) is a very accurate and sensitive technique which allows tc etermine the magnetic anisotropy fields of thin magnetic films [5]. Experimental FMR spectra fo: ne film containing 14% of iron, with a thickness of 100 nm, are given in Fig. 5; and in Fig. 6 the ngular dependence of the in-plane resonance field (Fig. 6a) and the temperature dependence of the hard axis’ field for resonance (Fig. 6b) are shown. The angular dependences show an anomalously igh uniaxial magnetic anisotropy and unconventional triple-line stricture of the FMR spectrum H1, H2, H3) in the film plane, measured at low temperatures (20K, see Figs. 5a and 6a). As the 2mperature increases towards room temperature (see Fig. 6b), the magnetic anisotropy dramatically ecreases, and two of the three components of the FMR signal (H2 and H3) merge. From the
temperature dependences of the resonance field for the low-field component as opposed to the temperature dependence of the two high-field components of the FMR spectrum (see Fig. 6b) it is very probably that a phase with magnetization perpendicular to the film plane is present in the studied sample (see the magnetic hysteresis measurements below). The detailed analysis of the FMR measurements is under intensive development in the fashion of the works [6-8]. FMR measurements is under intensive development in the fashion of the works [6-8].
temperature dependences of the resonance field for the low-field component as opposed to the temperature dependence of the two high-field components of the FMR spectrum (see Fig. 6b) it is very probably that a phase with magnetization perpendicular to the film plane is present in the studied sample (see the magnetic hysteresis measurements below). The detailed analysis of the FMR measurements is under intensive development in the fashion of the works [6-8]. FMR measurements is under intensive development in the fashion of the works [6-8].
Fig. 6. (a) In-plane angular and (b) temperature dependences of the resonance field for the PdgsFe,, correlate the magnetic properties with the composition and structure (Figs. 1-4).
Fig. 6. (a) In-plane angular and (b) temperature dependences of the resonance field for the PdgsFe,, correlate the magnetic properties with the composition and structure (Figs. 1-4).
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