The Effect of Fe Doping on the Magnetic and Magnetocaloric Properties of Mn5-x Fex Ge3

Abstract

The magnetic and magnetocaloric properties of a series of minutely doped [subscript]Mn5-x[/subscript] [subscript]Fex[/subscript] [subscript]Ge3[/subscript] compounds that exhibit the D88-type hexagonal crystal structure at room temperature have been investigated. For all Fe concentrations, the alloys are ferromagnetic and undergo a second-order ferromagnetic-to-paramagnetic transition near room temperature. Although the small Fe doping had little effect on the ferromagnetic transition temperatures of the system, changes in the saturation magnetization and magnetic anisotropy were observed. For x<=0.15, all compounds exhibit nearly the same magnetic entropy change of ~7 J/kg K, for a field change of 50 kOe. However, the magnitude of the refrigerant capacities increased with Fe doping, with values up to 108.5 J/kg and 312 J/kg being observed for field changes of 20 kOe and 50 kOe, respectively. As second-order phase transition materials, the [subscript]Mn5-x[/subscript] [subscript]Fex[/subscript] [subscript]Ge3[/subscript] compounds are not subject to the various drawbacks associated with first-order phase transition materials yet exhibit favorable magnetocaloric effects.

Jeffrey Brock 1 and Nathanael Bell-Pactat 1 and Hong Cai 1 and Timothy Dennison 1 and Tucker Fox 1 and Brandon Free 1 and Rami Mahyub 1 and Austin Nar 1 and Michael Saaranen 1 and Tiago Schaeffer 1 and Mahmud Khan 1

Academic Editor:Jamal Berakdar

Department of Physics, Miami University, Oxford, OH 45056, USA

Received 18 January 2017; Revised 17 February 2017; Accepted 23 February 2017; 6 March 2017

This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.

1. Introduction

Motivated by the energy-inefficiency, environmental impacts, and poor durability of current gas-compression based refrigeration technologies, there has been a great deal of interest in the development of alternative technologies that are more energy efficient and environmentally friendly. One such solution that has spurred considerable interest is the magnetocaloric effect (MCE) [1, 2]. In brief, the MCE occurs when a magnetic material is adiabatically magnetized in a changing magnetic field. As the individual magnetic moments align themselves with the applied field, there is a decrease in the number of energy microstates available to the system, commensurate to an isothermal magnetic entropy change (Δ_SM ). This change in a thermodynamic state variable can lead to an adiabatic temperature change (Δ_TAd ). The Δ_TAd generated via the MCE can enable the transport of a significant amount of heat at greater efficiency than current technologies, attracting interest for solid-state cooling applications [3]. First observed in Ni by Weiss in 1917, research interest in MCE burgeoned after Pecharsky and Gschneidner Jr. published their seminal report regarding so-called giant MCE in Gd₅ (Si₂ Ge₂ ), attainable using magnetic field changes within the reach of permanent magnets [4].

Generally, large MCE is associated with materials that undergo a coupled first-order magnetostructural phase transition (FOMPT), as the simultaneous change in both the magnetic and structural phase is conducive to larger Δ_SM values and potentially larger Δ_TAd values [5-7]. Strong MCE has been observed in many Mn-based FOMPT materials, including MnFe(P, As) [3, 8-10], Mn(As, Sb) [5], and MnFe(P,As,Ge) [11] compounds. Unfortunately, the heightened MCE of these materials is offset by the downfalls that all FOMPT materials are susceptible to, including thermal and magnetic hysteresis losses and irreproducibility due to mechanical fatigue [12]. Moving towards the realization of robust magnetic refrigeration technologies, it is clear that these FOMPT pitfalls should be addressed in FOMPT materials, or that FOMPT-comparable MCE should be sourced from materials exhibiting second-order phase transitions.

The Mn₅ Ge₃ compound has attracted significant research interest because it exhibits a second-order ferromagnetic phase transition with a Curie temperature (_TC ) near room temperature (296 K) in addition to a moderately large Δ_SM (9.2 J/kg K for a field change of 50 kOe) [13, 14]; both of these quantities are characteristics that should be sought from candidate MCE materials. Given that the magnetic properties of transition metal-based systems are heavily sensitive to the interatomic distances that governs the magnetic exchange mechanisms [15, 16], attempts have been made to incorporate other transition metals within basic systems in order to modify the lattice parameters and exchange interactions and thus optimize the magnetic and MCE properties of the Mn₅ Ge₃ parent compound [15]. One such system is the _Mn5-xFexGe3 series previously investigated by Zhang et al. [17]. In their report, they employed substitutions with x ranging from 0 to 1, in steps of 0.25, and found that larger refrigerant capacities were observed in samples with smaller x (less Fe). This system is worth reexamination using smaller substitutions, given that the previously reported replacements displaced _TC from 300 K in the x=0 compound to 330 K in the x=1 compound, as well as the aforementioned findings regarding the refrigerant capacity.

Keeping this in mind, we have performed an experimental study of the _Mn5-xFexGe3 (0<=x<=0.15) system, exploring the effect of smaller Fe substitutions on the structural, magnetic, and magnetocaloric properties of the compounds. In limiting investigation to small substitutions of Fe, our goals were to observe whether a changing nature of the magnetic interactions was apparent across the series and to assess the MCE potential of the compounds by means of Δ_SM and refrigerant capacity calculations.

2. Experimental Details

Polycrystalline buttons of _Mn5-xFexGe3 (0<=x<=0.15) weighing approximately 2 g each were fabricated in Ar atmosphere using the vacuum arc melting technique. The virgin metals used in fabrication were of at least 3 N purity, and an additional 2 wt.% of Mn was incorporated to account for Mn loss during the melting process. The samples were flipped and remelted several times in order to ensure homogeneity. Next, the as-casted buttons were wrapped in Ta foil, sealed in partially evacuated (Ar partial pressure) vycor tubes, and annealed at 750°C for four days in an electric furnace to promote further homogenization. After annealing, the samples were immediately quenched in cold water.

In order to explore the structure and phase purity of the alloys, powder X-ray diffraction (XRD) measurements were performed using a Scintag PAD X, a device which employs a monochromatic Cu-Kα₁ radiation source and a theta-theta geometry. The powder patterns were indexed using PowderCell [18]. Compositional properties were examined using a Zeiss Supra 35 FEG SEM, equipped with energy-dispersive X-ray spectroscopic (EDS) capabilities. Magnetization as a function of temperature and applied magnetic field (M(T) and M(H), resp.) were measured using a Physical Property Measurement System (PPMS), manufactured by Quantum Design, Inc. M(T) and M(H) measurements were performed in temperatures ranging from 5 to 400 K and in applied magnetic fields up to 50 kOe. M(T) data was collected under both the zero-field-cooled and field-cooled protocols (ZFC and FC, resp.), and each sample's _TC was determined by inspecting the derivative of the M(T) curves for the minima. From M(H) measurements collected isothermally at temperatures near the samples' _TC , Δ_SM was determined using the well-known Maxwell relation [19]: [figure omitted; refer to PDF] Furthermore, as Δ_SM may not necessarily be the best metric by which to judge the appropriateness of a material for MCE applications, we have calculated the refrigerant capacity (RC) of our compounds using the _RCA expression of Gschneidner and Pecharsky, given as follows [20]: [figure omitted; refer to PDF] where _THot and _TCold are defined as the temperature bounds forming the full-width at half-maximum of each sample's Δ_SM curve, for a given field change (ΔH ).

3. Results and Discussion

The room temperature XRD patterns of the four fabricated _Mn5-xFexGe3 compounds are shown in Figure 1. In agreement with previous literature on the _Mn5-xFexGe3 system, the compounds were found to crystallize in the hexagonal D8₈ -type crystalline structure (CSG: P63/mcm ). The lattice parameters of the x=0 sample and all samples' c/a ratios match the literature as well. Rietveld refinement of the powder patterns corroborates past neutron diffraction studies of the Mn₅ Ge₃ compound, suggesting that Mn occupies the 4d and 6g crystallographic sites while Ge is localized to the 6f sites [24]. The lattice parameters decrease minutely with x, from a=b=7.2058 Å and c=5.0398 Å in the x=0 sample to a=b=7.2023 Å and c=5.0375 Å in the x=0.15 sample. The static c/a ratio across the system indicates a uniform cell contraction, suggesting that the substitutional Fe assumes the 4d site in _Mn5-xFexGe3 . SEM backscatter micrographs of the compounds are shown in Figure 2. The lack of contrast in the micrographs demonstrates that a single compositional phase is formed in the _Mn5-xFexGe3 compounds, suggesting that a nearly ideal solid-state solution is formed. EDS analysis (not shown) showed that the fabricated alloys suitably matched their respective targeted compositions.

Figure 1: Room temperature XRD patterns for the _Mn5-xFexGe3 system.

[figure omitted; refer to PDF]

Figure 2: Backscatter SEM micrographs of the _Mn5-xFexGe3 compounds, collected using a 30 keV primary beam.

[figure omitted; refer to PDF]

The M(T) data for the _Mn5-xFexGe3 compounds is shown in Figure 3. The M(T) curves were collected in a 1 kOe magnetic field. For each sample, the only anomalous behavior observed is the sudden drop in magnetization corresponding to the ferromagnetic-to-paramagnetic phase transition at _TC . The lack of thermal hysteresis at the phase transition between the ZFC and FC curves indicates that it is a second-order transition. Interestingly, _TC is nearly constant across the series (~296 K). It was previously argued that Fe and Mn randomly occupy the 4d sites in _Mn5-xFexGe3 compounds [17]. It is possible that the maximum concentration of Fe (x<=0.15, where 0.15 implies only 3 at. %) in our compounds is not large enough to cause any change in the exchange interactions, as far as _TC is concerned.

Figure 3: Temperature dependence of magnetization, M(T), for the _Mn5-xFexGe3 system. The data was collected in an applied magnetic field of 1 kOe.

[figure omitted; refer to PDF]

To further explore the magnetic properties of the _Mn5-xFexGe3 compounds, M(H) curves were collected at T=10 K and the results are shown in Figure 4. As shown in the figure, all samples exhibit typical ferromagnetic behavior and attain magnetic saturation (_MS ) well below 50 kOe. As shown in the inset of Figure 4, _MS initially increases with x until x=0.05 and decreases with further increase of x. The initial increase in _MS may be attributed to the occupancy considerations discussed above as well as the comparatively larger magnetic moment of the Fe atoms versus the 4d Mn atoms (2.6 _μB to 1.85 _μB , resp.) [25]. The decreased _MS in the higher-Fe samples may be explained by an appeal to the XRD findings, which demonstrated a uniform unit cell contraction with Fe content. As the lattice parameters decrease, it is possible that the ferrimagnetic ordering of the Fe₅ Ge₃ phase may become more dominant in determining the bulk magnetic properties of the _Mn5-xFexGe3 compounds [17]. Additionally, it is noted that the M(H) curves for samples with x<=0.1 exhibit relatively "harder" magnetic behavior, whereas the samples with x>0.1 exhibit "softer" magnetic behavior [26]. This indicates that a greater degree of magnetic anisotropy exists in the higher-Fe samples and further confirms a change in magnetic properties across the relatively small compositional span of the _Mn5-xFexGe3 (0<=x<=0.15) system.

Figure 4: Magnetization as a function of applied magnetic field, M(H), for the _Mn5-xFexGe3 system, measured at a temperature of 10 K. The inset shows the saturation magnetization, _MS , as a function of Fe concentration.

[figure omitted; refer to PDF]

In order to assess the magnetic entropy changes (Δ_SM ) in the _Mn5-xFexGe3 compounds, isothermal M(H) data was collected at multiple temperatures in the vicinity of the samples' _TC . As an illustration, isothermal M(H) data for the x=0.05 compound is shown in Figure 5. It is clear that the sample with x=0.05 exhibits typical ferromagnetic behavior (i.e., paramagnetic for isotherms above _TC , ferromagnetic below _TC [27]). From each sample's isothermal M(H) curves, the respective Δ_SM (T) curve was determined by applying (1) to each of the five field changes, and the results are shown in Figure 6. It is evident that Δ_SM (T) initially increases with temperature until each sample's respective _TC , at which point it begins to decay. The largest peak Δ_SM values are observed in the sample with x = 0-7.0 J/kg K and 3.65 J/kg K for field changes of 50 kOe and 20 kOe, respectively.

Figure 5: Isothermal magnetization as a function of applied magnetic field of the _Mn5-xFexGe3 (x=0.05) sample measured at isotherms in the vicinity of the sample's Curie temperature.

[figure omitted; refer to PDF]

Figure 6: The magnetic entropy change as a function of temperature of the _Mn5-xFexGe3 compounds, for magnetic field changes of 10 kOe (1 T) to 50 kOe (5 T).

(a) [figure omitted; refer to PDF]

(b) [figure omitted; refer to PDF]

(c) [figure omitted; refer to PDF]

(d) [figure omitted; refer to PDF]

As mentioned earlier, the peak Δ_SM values are not the only or most appropriate quantity by which to judge the MCE potential of a material. Using the well-established protocol enumerated in (2), we calculated each sample's _RCA for the explored field changes, and the results are shown in Table 1. A visual representation of this integration for a field change of 20 kOe is provided in Figure 6(c) for the x=0.1 sample. From Table 1, it is apparent that the x=0.15 sample exhibits the largest _RCA values--108.5 J/kg and 312 J/kg for field changes of 20 kOe and 50 kOe, respectively. The heightened MCE properties of the x=0.15 sample may be explained by the broadness of its Δ_SM full-width at half-maximum. While the RC values reported in [17] were calculated using the Wood/Potter technique, recent literature overwhelmingly utilizes _RCA as the MCE assessment parameter; thus, we have chosen to use this metric as it is more suitable for comparison. The _RCA values calculated for the _Mn5-xFexGe3 (0<=x<=0.15) system favorably compare to a variety of recently reported second-order phase transition compounds, including _{Mn5Ge2.7Ga0.3} [21], _{Mn5Ge2.8Sb0.2} [13], Gd(_Co0.35Mn0.65 )₂ [22], and Ni₂ Mn_0.95 Cr_0.05 In [23], as demonstrated in Table 1. The large RC values of the _Mn5-xFexGe3 system suggest that it is worthy of further MCE explorations, including Δ_TAd measurements.

Table 1: The magnetocaloric properties of the _Mn5-xFexGe3 compounds compared to several other second-order phase transition compounds.

Compound	Peak ΔSM (J/kg K)	R C A (J/kg)	Reference
20 kOe	50 kOe	20 kOe	50 kOe
Mn5 Ge3	3.65	7.0	97	298	This work
Mn4.95 Fe0.05 Ge3	3.58	6.9	95	294	This work
Mn4.9 Fe0.1 Ge3	3.50	6.96	104.5	305	This work
Mn4.85 Fe0.15 Ge3	3.63	6.9	108.50	312	This work
Mn5 Ge2.7 Ga0.3	3.2	6.1	84	256.2	[21]
Mn5 Ge2.8 Sb0.2	--	6.2	--	320	[13]
Gd(Co0.35Mn0.65 )2	--	3.4	--	289	[22]
Ni2 Mn0.95 Cr0.05 In	1.69	3.37	59.79	167.5	[23]

4. Conclusion

In brief, we have performed an experimental study of the structural, magnetic, and magnetocaloric properties of the _Mn5-xFexGe3 (0<=x<=0.15) system. All samples were found to crystallize in the D8₈ -type hexagonal structure at room temperature and in a single compositional phase. Increasing Fe content has little effect on the Curie temperatures but has a noticeable effect on the saturation magnetization and magnetic anisotropy of the samples, indicating a change in the magnetic properties. For all Fe concentrations, large refrigerant capacities are observed in the vicinity of room temperature; maximal refrigerant capacities are observed in the sample with the highest Fe co(TM)ntent, which has the magnetic anisotropy. The experimental findings suggest that additional magnetocaloric investigations of the _Mn5-xFexGe3 system may be warranted.

Acknowledgments

The XRD measurements were performed by Professor Shane Stadler's group at the Louisiana State University. The SEM micrographs and related EDS data were collected at the Miami University Center for Advanced Microscopy (CAMI), Oxford, OH 45056, USA.

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