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Article

Phase Formation and Magnetic Properties of (Y1−xSmx)Co5 Melt-Spun Ribbons

by
Xiang Liu
,
Siyue Yang
*,
Xingping Zheng
,
Feilong Dai
,
Qingrong Yao
and
Jiang Wang
*
Guangxi Key Laboratory of Information Materials, School of Materials Science and Engineering, Guilin University of Electronic Technology, Guilin 541004, China
*
Authors to whom correspondence should be addressed.
Metals 2024, 14(5), 562; https://doi.org/10.3390/met14050562
Submission received: 2 April 2024 / Revised: 30 April 2024 / Accepted: 7 May 2024 / Published: 10 May 2024
(This article belongs to the Section Metallic Functional Materials)
Browse Figures
Versions Notes

Abstract

:
Using X-ray diffraction (XRD) and a vibrating sample magnetometer (VSM), the effects of Sm substitution, wheel speed, and annealing temperature on the phase formation and magnetic properties of (Y1−xSmx)Co5 (x = 0.2, 0.3, 0.4, 0.5) melt-spun ribbons were investigated. The results indicate the following: (1) With the increase in Sm substitution, it was found that (Y1−xSmx)Co5 ribbons are entirely composed of the (Y-Sm)Co5 phase with a CaCu5-type structure. Additionally, the coercivity gradually increases, while the remanence and saturation magnetization gradually decrease. (2) As the wheel speed increases, the (Y1−xSmx)Co5 ribbons exhibit an increasing proportion of (Y-Sm)Co5 phase until reaching a speed of 40 m/s, where they are entirely composed of the (Y-Sm)Co5 phase. Magnetic measurements show that the coercivity (Hcj) and remanence (Br) of (Y0.5Sm0.5)Co5 ribbons increase gradually with increasing wheel speed, while saturation magnetization decreases. The variation in magnetic properties is mainly attributed to the formation of nucleation centers for reversed magnetic domain (2:7 and 2:17 phases); (3) (Y0.5Sm0.5)Co5 ribbons are composed of the (Y-Sm)Co5 phase and a small amount of the Sm2Co7 phase after annealing at 550 °C, 600 °C, and 650 °C. Temperature elevation promotes crystallization of the amorphous phase, resulting in a gradual decrease in coercivity, while the remanence and saturation magnetization exhibit an overall increasing trend. Through continuous optimization of the process, favorable magnetic properties were achieved under the conditions of a 0.5 Sm substitution level, a wheel speed of 40 m/s, and an annealing temperature of 550 °C, with a coercivity of 7.98 kOe, remanence of 444 kA/m, and saturation magnetization of 508 kA/m.

1. Introduction

Nd-Fe-B permanent magnets are widely recognized for their exceptional magnetic properties at room temperature, making them indispensable in various modern industrial applications such as wind power generation and electric vehicles [1,2,3,4]. However, their utility is limited for high temperature applications due to their relatively low Curie temperature [5,6,7,8]. In contrast, SmCo5 permanent magnets, as one of the most representative types among RECo5 (where RE represents rare-earth elements) magnets, exhibit high thermal stability, meeting the stringent requirements of industrial applications. With a maximum operating temperature reaching up to 250 °C [9,10,11,12], SmCo5 magnets ensure reliable performance even under elevated temperature conditions. Presently, various methods such as mechanical alloying, magnetron sputtering, and melt spinning are commonly employed for the preparation of SmCo5-based alloys [13,14,15]. For instance, Li et al. [13] utilized the melt spinning technique to successfully fabricate anisotropic nanocrystalline SmCo4.8Cr0.14C0.08. They observed a transition in grain structure from randomly oriented equiaxed grains to dendritic morphology with increasing quenching speed. Remarkably, at a quenching speed of 50 m/s, the coercivity of the alloy reached 40.3 kOe, exhibiting excellent magnetic properties. In other research, Su et al. [14] employed high-energy ball milling to prepare SmCo5/α-Fe nanocomposite permanent magnetic materials. By subjecting the materials to heat treatment below 700 °C in a magnetic field, they successfully obtained nanocomposite magnets exhibiting strong soft–hard phase interactions, characterized by a single-phase hysteresis loop. Such distinctive microstructure and performance characteristics offer new insights and possibilities for the design and application of permanent magnetic materials. Recently, Gabay et al. [15] used another method to produce high-coercivity YCo5 and SmCo5 powders by employing a mechanosynthesis approach based on conventional powder grinding. They employed mechanical activation using a mixture of rare earth oxides with Co, Ga, and CaO, followed by short-term annealing and washing/separation processes to produce high-coercivity YCo5 and SmCo5 powders. They found out that the hard magnetic properties of YCo5 powders synthesized via mechanosynthesis are comparable to those of conventionally prepared SmCo5 powders, offering a novel avenue for the controllable synthesis of permanent magnetic materials.
The elements lanthanum (La), cerium (Ce), and yttrium (Y), which are found abundantly in rare-earth resources, are capable of forming a 1:5 phase with the transition metal cobalt (Co). Compounds such as LaCo5, CeCo5, and YCo5, as well as SmCo5, all crystallize into the hexagonal CaCu5-type crystal structure, characterized by a space group of P6/mmm. However, it is noteworthy that only YCo5 exhibits intrinsic magnetic properties that are on par with or even surpass those of SmCo5 [16,17,18,19]. Specifically, both SmCo5 and YCo5 exhibit high magnetic anisotropy, owing to the interaction between the 4f electrons of samarium (Sm) atoms and the hexagonal crystal field, as well as the spin–orbit coupling of the 3d electrons of cobalt (Co) atoms [20]. This interplay of electronic configurations contributes significantly to the magnetocrystalline anisotropy observed in these materials. Considering Y as a high-abundance rare-earth element, it is believed that adding the element Y is a promising and cost-effective way to enhance the magnetic properties of 1:5-type permanent magnets [21,22,23].
Research on SmCo5 and YCo5 in the past has mainly focused on investigating the incorporation of various elements into their structures. These elements are the transition metals, like Fe, Cu, Ti, Zr, Ni, and Mn [24,25,26,27,28,29,30], non-metallic elements, such as C, H, and Si [31,32,33], and rare-earth elements, like La, Ce, Pr, Nd, Dy, and Tm [34,35,36,37,38]. The aim has been to fine-tune the phase composition and magnetic characteristics of permanent magnets. For instance, Larson et al. [25] investigated the impact of Fe doping on the magnetic anisotropy of SmCo5 and YCo5, employing both experimental and computational techniques. They observed that when the doping level of Fe was approximately 3–4% in SmCo5−xFex and 6–7% in YCo5−xFex, the magneto-crystalline anisotropy energy (MAE) increased by about 1 meV/f.u. However, with further increases in Fe doping, the magnetic anisotropy rapidly declined. This phenomenon was also observed in other RECo5−xFex magnets. Chen et al. [34], on the other hand, systematically investigated the phase structures and magnetic properties of Sm1−xLaxCo5 and Sm1−xCexCo5 alloys tuning La and Ce doping levels and annealing conditions. Their findings indicated a superior magnetic performance in La-doped SmCo5 compared to Ce-doped counterparts. Additionally, Banerjee et al. [37] investigated the structural and magnetization characteristics of Dy1−xYxCo5 compounds, finding an enhancement in the axial magneto-crystalline anisotropy energy (MAE) with increasing Y content. Despite these efforts, research on the phase evolution, microstructural intricacies, and magnetic behaviors of (Y1−xSmx)Co5 alloys still needs research. Passos et al. [20] conducted an investigation on the effect of substituting Y with Sm on the magnetic properties of (Y1−xSmx)Co5 (x = 0.0, 0.1, 0.2, 0.3, and 0.4) alloys. Furthermore, Gonzalez et al. [39] reported a coercivity of 12 kOe for Y0.5Sm0.5Co5 melt-spun ribbon at a wheel speed of 40 m/s. In order to deeply study the relationship between the composition, phase formation, preparation conditions, and magnetic properties of rare-earth element Sm and YCo5 alloys, (Y1−xSmx)Co5 alloys were prepared using melt spinning technology. The phase formation and magnetic properties of these alloys were analyzed. The effects of Sm substitution, wheel speeds, and annealing temperatures under different conditions on the magnetic properties of (Y1−xSmx)Co5 ribbons were investigated.

2. Experiment

The (Y1−xSmx)Co5 (x = 0.2, 0.3, 0.4, 0.5) alloys were synthesized with the arc-melting method, using high-purity bulk metals Y, Sm, and Co (99.99% purity) as raw materials. Due to the high volatility of the rare-earth elements Y and Sm at high temperatures, an additional 5% of Y and Sm was added during weighing to compensate for evaporation. To ensure compositional homogeneity, the alloys underwent four re-melting cycles during the arc-melting process. Subsequently, the alloys were crushed into small pieces (approximately 2.5 g) and loaded into a quartz tube with an orifice (diameter approximately 0.9 mm). They were then spun onto a copper wheel in an argon atmosphere at various wheel speeds (20–40 m/s) to produce melt-spun ribbons. Subsequently, the melt-spun ribbons were placed in quartz tubes filled with argon, annealed at different temperatures (500–650 °C) for 30 min, and then quenched in ice water. The width of the melt-spun ribbons ranged from about 8 to 13 mm, and the thickness was approximately 2 to 3 mm.
The (Y1−xSmx)Co5 melt-spun ribbons (about 0.5 g) were placed in an agate mortar filled with anhydrous ethanol to prevent oxidation and then were manually grinded into powders, which was sieved to achieve a particle size of 250 mesh. XRD measurements of powders were performed on a PLXcel 3D X-ray diffractometer (Tokyo, Japan) in the range 20–70° at 45 kV and 25 mA using a Co K radiation source. The crystal structure of the (Y1−xSmx)Co5 ribbons was determined by analyzing XRD patterns. The magnetic properties of the melt-spun ribbons were measured at room temperature using a vibrating sample magnetometer (VSM, Lakeshore Model 7400 740H, Carson, CA, USA). The demagnetization correction of the melt-spun ribbons was neglected because the applied external field is parallel to the plane of the ribbons during the magnetic measurements.

3. Results and Discussion

3.1. Structure and Magnetic Properties of (Y1−xSmx)Co5 Ribbons

Figure 1 shows the XRD spectra of the (Y1−xSmx)Co5 (x = 0.2, 0.3, 0.4, 0.5) melt-spun ribbons at a wheel speed of 40 m/s. In Figure 1a, it is observed that the (Y1−xSmx)Co5 ribbons contain a continuous solid solution phase (Y-Sm)Co₅, exhibiting a CaCu5-type structure with a space group of P63/mmc, as identified by comparison with standard PDF cards. Figure 1b presents the local XRD spectra of these ribbons in the 40° to 45° range, revealing a leftward shift of the diffraction peaks of the (Y-Sm)Co5 phase with increasing Sm atomic substitution. This shift is attributed to the larger atomic radius of Sm compared to Y, leading to a decrease in diffraction angle according to the Bragg equation. Figure 2 displays the variations in lattice parameters and unit cell volumes of the (Y-Sm)Co5 phase as the Sm atomic substitution increases. Specific numerical values are provided in Table 1. It is observed from Figure 2 that the lattice parameter ‘a’ and cell volume of the (Y-Sm)Co5 phase slightly increase with increasing Sm substitution, while the lattice parameter ‘c’ gradually decreases. This trend may be attributed to the lattice constants of SmCo5 phase, where ‘a’ = 4.998 (Å) is greater than that of YCo5 phase with ‘a’ = 4.928 (Å), while ‘c’ = 3.976 (Å) for SmCo5 is smaller than ‘c’ = 3.992 (Å) for YCo5 [40,41].
Figure 3 depicts the initial magnetization curves and hysteresis loops (M-H curves) of the (Y1−xSmx)Co5 (x = 0.2, 0.3, 0.4, 0.5) melt-spun ribbons prepared at a wheel speed of 40 m/s. Figure 4 illustrates the variations in remanence (Br), coercivity (Hcj), and saturation magnetization (Ms) of the (Y1−xSmx)Co5 (x = 0.2, 0.3, 0.4, 0.5) melt-spun ribbons with the substitution of Sm. The corresponding magnetic parameters are listed in Table 1. From Figure 3a, it can be observed that the initial magnetization curve of the (Y1−xSmx)Co5 melt-spun ribbons shows a rapid increase in magnetization intensity at low magnetic fields. As the magnetic field intensity increases, the magnetization intensity tends to saturate, indicating that the magnetization mechanism is regulated by the nucleation field [42]. From Table 1 and Figure 4, it is evident that the saturation magnetization of the (Y1−xSmx)Co5 melt-spun ribbons decreases from 726 kA/m to 488 kA/m with increasing Sm substitution. Due to the higher saturation magnetization of YCo5 compared to SmCo5, the increase in Sm content promotes the formation of SmCo5 in the continuous solid solution phase (Y-Sm)Co5, reducing the YCo5 content and consequently leading to a decrease in the saturation magnetization of the ribbon [43,44]. Figure 3b shows the hysteresis loops of the (Y1−xSmx)Co5 melt-spun ribbons, indicating that the coercivity increases from 0.79 to 7.98 kOe with the increasing substitution of Sm. This significant enhancement is attributed to the introduction of Sm, which also leads to an increase in the proportion of SmCo5 in the continuous solid solution phase (Y-Sm)Co5. Compared to YCo5, SmCo5 exhibits higher coercivity, thus the coercivity of the ribbon increases with increasing Sm content. Meanwhile, the remanence decreases from 479 kA/m to 406 kA/m, exhibiting a trend similar to the decrease in saturation magnetization, both attributed to the increase in the volume fraction of SmCo5 in the continuous solid solution phase (Y-Sm)Co5.
In this section, an investigation was conducted into the phase structure, phase composition, and magnetic properties of (Y1−xSmx)Co5 (x = 0.2, 0.3, 0.4, 0.5) melt-spun ribbons at a wheel speed of 40 m/s. It was confirmed that the (Y1−xSmx)Co5 ribbons exhibit a CaCu5-type structure, with the XRD diffraction peaks shifting to the left as the substitution amount of Sm increases. The lattice parameter ‘a’ and the unit cell volume of the (Y-Sm)Co5 phase showed a slight increase, while the lattice parameter ‘c’ gradually decreased. Magnetic measurement results indicated that the magnetization mechanism is regulated by the nucleation field. With an increase in the substitution amount of Sm, the saturation magnetization of the (Y1−xSmx)Co5 ribbons decreased from 726 kA/m to 488 kA/m, coercivity increased from 0.79 kOe to 7.98 kOe, and remanence decreased from 479 kA/m to 406 kA/m. These changes were attributed to the increase in the proportion of SmCo5 in the continuous solid solution phase (Y-Sm)Co5.

3.2. Structural and Magnetic Properties of (Y0.5Sm0.5)Co5 Ribbons at Different Wheel Speeds

In the previous section, an investigation on the structure and magnetic properties of (Y1−xSmx)Co5 (x = 0.2, 0.3, 0.4, 0.5) melt-spun ribbons prepared at a wheel speed of 40 m/s revealed that at a Sm substitution level of 0.5, i.e., x = 0.5, the ribbons exhibited a higher coercivity of 7.98 kOe. In order to further investigate the structural and magnetic property variations in (Y1−xSmx)Co5 melt-spun ribbons under different conditions, we kept x = 0.5 constant and varied the wheel speed. (Y0.5Sm0.5)Co5 melt-spun ribbons were prepared at different wheel speeds (20 m/s, 30 m/s, 40 m/s) to examine their structural and magnetic property changes.
Figure 5 shows the X-ray diffraction (XRD) patterns of the (Y0.5Sm0.5)Co5 melt-spun ribbons prepared at different wheel speeds (20 m/s, 30 m/s, 40 m/s). It can be observed from Figure 5 that at a wheel speed of 20 m/s, the melt-spun ribbon consists entirely of the (Y-Sm)2Co17 phase; at 30 m/s, the ribbon comprises small amounts of the Sm2Co7 and (Y-Sm)Co5 phases, while at 40 m/s, the ribbon consists entirely of the (Y-Sm)Co5 phase. During the preparation of the melt-spun ribbons, slower wheel speeds lead to the accumulation of molten metal on the surface of the copper roller, resulting in thicker ribbon layers and slower cooling rates. According to the Y-Co [45] and Sm-Co [46] binary phase diagrams, the 1:5 phase decomposes into 2:7 and 2:17 phases at low temperatures. Thus, at a wheel speed of 20 m/s, the decomposition of (Y-Sm)Co5 phase forms the (Y-Sm)2Co17 phase, while at 30 m/s, partial decomposition of (Y-Sm)Co5 phase forms Sm2Co7 phase. However, at a wheel speed of 40 m/s, the resulting ribbon has a thinner layer and faster cooling rate, preventing the (Y-Sm)Co5 phase from undergoing a phase transformation. When the speed is 40 m/s, there is an unclear diffraction peak between 20° and 25° in the diffraction pattern, indicating the presence of an amorphous phase in the (Y0.5Sm0.5)Co5 melt-spun ribbon at this speed. To further confirm the existence of the amorphous phase, we calculated the crystallinities at wheel speeds of 20 m/s, 30 m/s, and 40 m/s, which were found to be 60.4%, 53.2%, and 45.7%, respectively. The formation of the amorphous phase is attributed to the higher wheel speed accelerating the cooling rate, resulting in partial solidification of the alloy melt before crystallization.
Figure 6 depicts the initial magnetization curves and hysteresis loops (M-H curves) of (Y0.5Sm0.5)Co5 melt-spun ribbons at different wheel speeds. Figure 7 shows the variations in remanence (Br), coercivity (Hcj), and saturation magnetization (Ms) with Sm substitution for the (Y0.5Sm0.5)Co5 melt-spun ribbons, with corresponding magnetic parameters presented in Table 2. In Figure 6a, it can be observed that the initial magnetization intensity of the (Y0.5Sm0.5)Co5 melt-spun ribbon increases with the increasing applied magnetic field, gradually approaching saturation, with the magnetization mechanism being regulated by the nucleation field. From Table 2 and Figure 7, it can be seen that with increasing wheel speed, the saturation magnetization of the (Y0.5Sm0.5)Co5 melt-spun ribbon decreases from 870 kA/m to 488 kA/m. Consistent with previous research findings, the reduction in saturation magnetization intensity is attributed to the gradual decrease in crystallinity as the wheel speed increases in the (Y0.5Sm0.5)Co5 melt-spun ribbon, indicating an increasing proportion of the amorphous phase. Materials with non-crystalline structure exhibit higher magnetic hysteresis losses, resulting in increased energy dissipation during magnetization and consequently lowering the saturation magnetization. Additionally, amorphous structures typically lack distinct magnetic domain structures, resulting in higher domain wall energies, thus increasing the energy cost for magnetic moment reversal and decreasing the magnetization intensity. Figure 6b presents the hysteresis loop of the (Y0.5Sm0.5)Co5 melt-spun ribbons. From Figure 6b and Figure 7, it can be seen that with increasing wheel speed, the coercivity of the (Y1−xSmx)Co5 melt-spun ribbon increases from 0.4 to 7.98 kOe. This is attributed to the gradual increase in the proportion of the 1:5 phase with high coercivity as the speed increases. Additionally, when the wheel speed is 20 m/s, the ribbon is composed entirely of the (Y-Sm)2Co17 phase, which is a soft magnetic phase with lower coercivity. However, as the wheel speed increases to 30 m/s, the ribbon consists of Sm2Co7 and (Y-Sm)Co5, with the 2:7 phase becoming the nucleation center for demagnetization within the ribbon, resulting in lower coercivity compared to when the speed is 40 m/s. At a wheel speed of 40 m/s, both coercivity and remanence significantly increase, indicating a notable enhancement in remanence effect, primarily attributed to the reduction in the 2:7 and 2:17 phases, which reduces the nucleation centers for demagnetization.
In this section, we investigated the phase structure, phase composition, and magnetic properties of (Y0.5Sm0.5)Co5 melt-spun ribbons prepared at different wheel speeds (20 m/s, 30 m/s, 40 m/s). It was found that at a wheel speed of 20 m/s, the ribbons were composed of the (Y-Sm)2Co17 phase; at 30 m/s, they contained small amounts of Sm2Co7 and (Y-Sm)Co5, while at 40 m/s, the ribbons were entirely composed of the (Y-Sm)Co5 phase. Magnetic measurement results revealed that with increasing wheel speed, the saturation magnetization of the (Y0.5Sm0.5)Co5 melt-spun ribbons decreased from 870 kA/m to 488 kA/m. This decrease in saturation magnetization was attributed to the increase in the amorphous phase. Meanwhile, the remanence and coercivity increased with increasing speed, primarily due to the reduction in the 2:7 and 2:17 phases, thereby lowering the demagnetization nucleation centers.

3.3. Structure and Magnetic Properties of (Y0.5Sm0.5)Co5 Ribbons Annealed at Different Temperatures

In the previous sections, investigations were carried out on the structure and magnetic properties of (Y1−xSmx)Co5 (x = 0.2, 0.3, 0.4, 0.5) melt-spun ribbons prepared with different Sm substitutions and wheel speeds. It was found that when the Sm substitution is 0.5 and the wheel speed is 40 m/s, the melt-spun ribbon exhibits optimal magnetic properties. In order to further explore the structural and magnetic property changes of the (Y0.5Sm0.5)Co5 melt-spun ribbons under different conditions, in this section, ribbons prepared at a wheel speed of 40 m/s will be subjected to heat treatment at different temperatures (550 °C, 600 °C, and 650 °C). This aims to further investigate the variations in structure and magnetic properties.
Figure 8 displays the X-ray diffraction (XRD) patterns of (Y0.5Sm0.5)Co5 ribbons annealed at various temperatures for 30 min, prepared with a wheel speed of 40 m/s. It can be observed from Figure 8 that the (Y0.5Sm0.5)Co5 ribbon is predominantly composed of (Y-Sm)Co5 with a minor amount of Sm2Co7. The presence of the minor 2:7 phase could be attributed to the segregation of the 1:5 phase during the annealing process. As the annealing temperature increases, the main diffraction peaks gradually sharpen. According to the previous discussion, when the wheel speed is 40 m/s, the ribbon exhibits partial amorphous phase. According to the calculations, after heat treatment at 550 °C, 600 °C, and 650 °C, the crystallinity of the ribbon is 59.1%, 67.8%, and 76.5%, respectively. This indicates that with increasing temperature, the amorphous phase gradually transforms into a crystalline phase.
Figure 9 shows the initial magnetization curves and hysteresis loops (M-H curves) of (Y0.5Sm0.5)Co5 melt-spun ribbons annealed at different temperatures for 30 min, prepared with a wheel speed of 40 m/s. Figure 10 illustrates the variations in remanence (Br), coercivity (Hcj), and saturation magnetization (Ms) of the annealed (Y0.5Sm0.5)Co5 ribbons with annealing temperature. Corresponding magnetic parameters are provided in Table 2. From Figure 9a, it can be observed that the initial magnetization curve of the (Y0.5Sm0.5)Co5 melt-spun ribbon exhibits distinct ferromagnetic characteristics. The initial magnetization intensity of the ribbon rapidly increases with the applied magnetic field, reaching saturation, with the magnetization mechanism regulated by nucleation field. Figure 9b presents the hysteresis loop of the annealed (Y0.5Sm0.5)Co5 melt-spun ribbon. In the second quadrant, the demagnetization curve of the ribbon exhibits a relatively smooth profile, indicative of typical single-phase hard magnetic behavior. This observation suggests well-crystallized microstructure within the ribbon. However, there are evident twists in the demagnetization curve, indicating the possible formation of soft magnetic phases (such as Sm2Co7) during annealing. The exchange coupling effect between the (Y-Sm)Co5 hard magnetic phase and soft magnetic phase leads to the twists in the demagnetization curve of the ribbon. From Figure 10 and Table 2, it is revealed that after annealing at 550 °C, both saturation magnetization and remanence of the ribbon increase, showing a certain remanence enhancement effect. The crystallization of the amorphous phase in the ribbon after annealing is the main reason for the improvement in magnetic properties. With increasing annealing temperature, coercivity decreases from 7.98 kOe at 550 °C to 5.17 kOe at 650 °C. This decrease may be attributed to the growth of grain size in the ribbon with increasing annealing temperature, reducing the interaction between grains in the ribbon. Additionally, the increase in annealing temperature promotes the decomposition of the 1:5 phase into 2:7 and 2:17 phases, and the formation of these secondary phases can easily become nucleation centers for antiferromagnetic domains within the 1:5 ribbon, leading to a decrease in coercivity.
In this section, we investigated the phase structure, phase composition, and magnetic properties of (Y0.5Sm0.5)Co5 melt-spun ribbons annealed at different temperatures (550 °C, 600 °C, 650 °C) for 30 min. The results reveal that all ribbons were predominantly composed of (Y-Sm)Co5 with small amounts of Sm2Co7. Magnetic measurement results indicated a trend of increasing saturation magnetization and remanence with rising temperature, primarily attributed to the crystallization of the amorphous phase post-annealing. However, the coercivity decreases from 7.98 kOe to 5.17 kOe, attributed to the increase in grain size in the ribbon as annealing temperature rises, reducing the interaction between grains. Additionally, the elevated annealing temperature promotes the decomposition of the 1:5 phase into the 2:7 phase, with the formation of the 2:7 phase serving as easy nucleation sites for antiferromagnetic domains within the 1:5 phase, consequently leading to a decrease in coercivity.

4. Conclusions

This experimental investigation focused on the effects of Sm substitution, wheel speed, and annealing temperature on the phase structure and magnetic properties of (Y1−xSmx)Co5 melt-spun ribbons, yielding the following conclusions:
(1) With increasing Sm substitution, X-ray diffraction (XRD) analysis reveals that (Y1−xSmx)Co5 (x = 0.2, 0.3, 0.4, 0.5) ribbons are composed of (Y-Sm)Co5 with a CaCu5-type structure and space group P63/mmc. Magnetic measurements indicate that the magnetization mechanism is regulated by the nucleation field. As the Sm substitution increases, the proportion of tSmCo5 increases, leading to a decrease in saturation magnetization from 726 kA/m to 488 kA/m and remanence from 479 kA/m to 406 kA/m, while coercivity increased from 0.79 to 7.98 kOe.
(2) Based on the XRD results, the (Y0.5Sm0.5)Co5 ribbon prepared at wheel speeds of 20 m/s and 40 m/s are composed of (Y-Sm)2Co17, while the ribbon at a wheel speed of 30 m/s is composed of (Y-Sm)Co5 and Sm2Co7. The magnetic measurements show that the coercivity (Hcj), the remanence (Br), and the saturation magnetization (Ms) of the (Y0.5Sm0.5)Co5 ribbon increase gradually with the increase in wheel speed. The variation in magnetic properties is primarily attributed to the formation of nucleation centers for reversed magnetic domain (2:7 and 2:17 phases). At a wheel speed of 40 m/s, the ribbon is primarily composed of a single-phase (Y-Sm)Co5, exhibiting excellent magnetic properties under optimal conditions (coercivity of 7.98 kOe, remanence of 406 kA/m, saturation magnetization of 488 kA/m).
(3) The (Y0.5Sm0.5)Co5 ribbon prepared at a wheel speed of 40 m/s consists of (Y-Sm)Co5 and a small amount of Sm2Co7 according to the XRD results after annealing at 550 °C, 600 °C, and 650 °C for 30 min. The optimization of the annealing process promotes the crystallization of the amorphous phase. The best magnetic performance was achieved at an annealing temperature of 550 °C, resulting in a coercivity of 7.98 kOe, remanence of 444 kA/m, and saturation magnetization intensity of 508 kA/m.

Author Contributions

Conceptualization, X.L., S.Y., Q.Y. and J.W.; methodology, X.L., X.Z., F.D. and J.W.; software, X.Z. and F.D.; validation, X.L., X.Z. and F.D.; formal analysis, X.L., Q.Y. and J.W.; investigation, J.W. and Q.Y.; resources, Q.Y. and J.W.; data curation, X.L., X.Z. and S.Y.; writing—original draft preparation, X.L., S.Y., Q.Y. and J.W.; writing—review and editing, X.L., S.Y., Q.Y. and J.W.; visualization, X.Z.; supervision, Q.Y. and J.W.; project administration, J.W. and Q.Y.; funding acquisition, Q.Y. and J.W. All authors have read and agreed to the published version of the manuscript.

Funding

This work was supported financially by Guangxi Natural Science Foundation (2020GXNSFFA297004), the National Natural Science Foundation of China (51971069), and the Engineering Research Center of Electronic Information Materials and Devices (EIMD-AA202004), Guilin University of Electronic Technology, China.

Data Availability Statement

The original contributions presented in the study are included in the article, further inquiries can be directed to the corresponding author.

Conflicts of Interest

The authors declare no conflicts of interest.

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Figure 1. XRD patterns (a) and local XRD patterns (b) of (Y1−xSmx)Co5 (x = 0.2, 0.3, 0.4, 0.5) melt-spun ribbons prepared at a wheel speed of 40 m/s. The arrows in panel (b) indicate the direction of diffraction peak shifts.
Figure 1. XRD patterns (a) and local XRD patterns (b) of (Y1−xSmx)Co5 (x = 0.2, 0.3, 0.4, 0.5) melt-spun ribbons prepared at a wheel speed of 40 m/s. The arrows in panel (b) indicate the direction of diffraction peak shifts.
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Figure 2. Lattice parameters and cell volumes of (Y-Sm)Co5 phase in (Y1−xSmx)Co5 (x = 0.2, 0.3, 0.4, 0.5) melt-spun ribbons.
Figure 2. Lattice parameters and cell volumes of (Y-Sm)Co5 phase in (Y1−xSmx)Co5 (x = 0.2, 0.3, 0.4, 0.5) melt-spun ribbons.
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Figure 3. Initial magnetization curves (a) and hysteresis loops (b) of (Y1−xSmx)Co5 (x = 0.2, 0.3, 0.4, 0.5) melt-spun ribbons.
Figure 3. Initial magnetization curves (a) and hysteresis loops (b) of (Y1−xSmx)Co5 (x = 0.2, 0.3, 0.4, 0.5) melt-spun ribbons.
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Figure 4. Magnetic properties (Hcj, Br and Ms) of (Y1−xSmx)Co5 (x = 0.2, 0.3, 0.4, 0.5) melt-spun ribbons as a function of Sm substitution.
Figure 4. Magnetic properties (Hcj, Br and Ms) of (Y1−xSmx)Co5 (x = 0.2, 0.3, 0.4, 0.5) melt-spun ribbons as a function of Sm substitution.
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Figure 5. XRD patterns of (Y0.5Sm0.5)Co5 as-cast ribbons prepared at wheel speeds of 20 m/s, 30 m/s and 40 m/s.
Figure 5. XRD patterns of (Y0.5Sm0.5)Co5 as-cast ribbons prepared at wheel speeds of 20 m/s, 30 m/s and 40 m/s.
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Figure 6. Initial magnetization curves (a) and hysteresis loops (b) of (Y0.5Sm0.5)Co5 ribbon prepared at different wheel speeds.
Figure 6. Initial magnetization curves (a) and hysteresis loops (b) of (Y0.5Sm0.5)Co5 ribbon prepared at different wheel speeds.
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Figure 7. Magnetic properties (Hcj, Br, and Ms) of (Y0.5Sm0.5)Co5 melt-spun ribbons as a function of wheel speeds.
Figure 7. Magnetic properties (Hcj, Br, and Ms) of (Y0.5Sm0.5)Co5 melt-spun ribbons as a function of wheel speeds.
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Figure 8. XRD patterns of (Y0.5Sm0.5)Co5 ribbon prepared at a wheel speed of 40 m/s after annealed at different temperatures for 30 min.
Figure 8. XRD patterns of (Y0.5Sm0.5)Co5 ribbon prepared at a wheel speed of 40 m/s after annealed at different temperatures for 30 min.
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Figure 9. Initial magnetization curves (a) and hysteresis loops (b) of (Y0.5Sm0.5)Co5 ribbon annealed at different temperatures.
Figure 9. Initial magnetization curves (a) and hysteresis loops (b) of (Y0.5Sm0.5)Co5 ribbon annealed at different temperatures.
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Figure 10. Magnetic properties (Hcj, Br, and Ms) of (Y0.5Sm0.5)Co5 ribbon annealed at different temperatures.
Figure 10. Magnetic properties (Hcj, Br, and Ms) of (Y0.5Sm0.5)Co5 ribbon annealed at different temperatures.
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Table 1. Lattice parameters and cell volumes of (Y-Sm)Co5 phase and magnetic properties in (Y1−xSmx)Co5 melt-spun ribbons.
Table 1. Lattice parameters and cell volumes of (Y-Sm)Co5 phase and magnetic properties in (Y1−xSmx)Co5 melt-spun ribbons.
(Y1−xSmx)Co5 RibbonsLattice ParametersCell Volumes (Å3)Magnetic Properties
a (Å)c (Å)c/aHcj (kOe)Br (kA/m)Ms (kA/m)
x = 0.24.9361(1)3.9924(6)0.808884.24(5)0.79 ± 0.04479 ± 3726 ± 4
x = 0.34.9457(1)3.9922(6)0.807284.57(6)2.98 ± 0.02431 ± 4524 ± 2
x = 0.44.9578(1)3.9866(6)0.804184.70(6)4.28 ± 0.06422 ± 5518 ± 7
x = 0.54.9650(1)3.9790(6)0.801485.11(7)7.98 ± 0.02406 ± 2488 ± 4
Table 2. Magnetic properties of (Y0.5Sm0.5)Co5 ribbons prepared at different wheel speeds and annealed at different temperatures for 30 min.
Table 2. Magnetic properties of (Y0.5Sm0.5)Co5 ribbons prepared at different wheel speeds and annealed at different temperatures for 30 min.
Wheel Speed
(m/s)		Annealed Temperature (°C)Hcj (kOe)Br (kA/m)Ms (kA/m)
20no annealed0.40 ± 0.03282 ± 5870 ± 4
304.61 ± 0.05398 ± 7525 ± 4
407.98 ± 0.02406 ± 4488 ± 2
405507.98 ± 0.05444 ± 3502 ± 3
6006.96 ± 0.07376 ± 3479 ± 6
6505.17 ± 0.02463 ± 5548 ± 5
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Liu, X.; Yang, S.; Zheng, X.; Dai, F.; Yao, Q.; Wang, J. Phase Formation and Magnetic Properties of (Y1−xSmx)Co5 Melt-Spun Ribbons. Metals 2024, 14, 562. https://doi.org/10.3390/met14050562

AMA Style

Liu X, Yang S, Zheng X, Dai F, Yao Q, Wang J. Phase Formation and Magnetic Properties of (Y1−xSmx)Co5 Melt-Spun Ribbons. Metals. 2024; 14(5):562. https://doi.org/10.3390/met14050562

Chicago/Turabian Style

Liu, Xiang, Siyue Yang, Xingping Zheng, Feilong Dai, Qingrong Yao, and Jiang Wang. 2024. "Phase Formation and Magnetic Properties of (Y1−xSmx)Co5 Melt-Spun Ribbons" Metals 14, no. 5: 562. https://doi.org/10.3390/met14050562

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