1. Introduction

In recent years, magnetic nanomaterials based on rare-earth elements (R) and transition metals (T) have been widely investigated due to their extremely diverse potential applications in industrial fields ^{[1][2][3][4][5][6][7][8]}. These properties are often used to produce soft, hard, or semi-hard magnetic materials ^{[9][10][11][12][13][14][15][16][17][18][19][20][21][22][23]}. The origin of these exceptional magnetic properties is particularly due to the coexistence of of two complementary kinds of magnetism: the localized magnetism characteristic of rare-earth (R) electrons and the itinerant magnetism of the $3d$ electrons of transition metals (T), such as cobalt (Co) and iron (Fe) ^{[24][25][26][27][28][29][30][31][32][33]}. The R elements thus provide their strong magnetocrystalline anisotropy (H ${}_a$ ) due to the interactions between their orbital moment and the crystal field. The $3d$ metals provide their strong magnetization and a high Curie temperature (T ${}_C$ ) due to the important exchange interactions between the $3d$ elements ^{[34][35][36][37][38][39][40][41][42][43][44][45][46][47][48][49][50][51]}. Permanent magnets are the idea of an ever-increasing number of recent devices. Alloys and intermetallic compounds obtained by combining (R) elements with metals (T) form a crucial class of materials for which applications have been found in permanent magnets ^[44]. Among the intermetallic systems, the noncrystalline Pr₂Co₇ compound is currently one of the most promising ^{[34][52][53][54]}. The interest in these systems is due to the combination of the complementary characteristics of the $3d$ -itinerant and $4f$ -localized magnetism of Co and Pr atoms, respectively ^[54][55]. In order to strengthen these interactions, it is necessary to partially substitute the Co atoms in the noncrystalline Pr₂Co₇ compounds with an appropriate element, such as iron (Fe), or through the insertion of a light element, such as carbon (C) or hydrogen (H), which can increase interatomic distances and strengthen the magnetic moment.

2. Synthesis Methods of Pr₂Co_7, Pr₂Co₇−_xFe_x, Pr₂Co_xC_x, and Pr₂Co_xH_x Samples

To prepare the nanocrystalline Pr₂Co₇ and Pr₂Co₇−_xFe_x (x = 0.25, 0.5, 0.75, and 1) samples, high-energy ball milling was carried out on previously prepared ingots ^[56]. The pre-alloy obtained by fusion was broken inside a glove box with a mortar and then introduced with five beads into a hermetically sealed jar. A Fritsch P7 planetary mill with a bead/powder ratio of 15:1 was used to get finer particles. The ground powder was then wrapped in tantalum foil (Ta) and then sealed in quartz ampoules under secondary vacuum (10^-6 bar) at different annealing temperatures: T ${}_a$ = 700 K and 1350 K. The tantalum foil (Ta) was used to avoid contamination due to contact with silica; these samples were first degassed under secondary vacuum to ensure that no impurities came to pollute the synthesis products. The sample was cooled after leaving the oven by quenching in water. To insert carbon atoms (C) into the Pr₂Co₇ elemental cell, scholars used a carbonation technique that involved a solid–solid-type reaction according to the following reaction ^[57]:

$$7\mathrm{Pr}{}_2\mathrm{Co}{}_7+\frac{1}{2}\mathrm{C}{}_{14}\mathrm{H}{}_{10}+\frac{5}{2}\mathrm{Mg}⟶7\mathrm{Pr}{}_2\mathrm{Co}{}_7\mathrm{C}+\frac{5}{2}\mathrm{MgH}{}_2$$

Hydrogen atoms (H) were inserted into the Pr₂Co₇ compound with a solid–gas reaction between the sample and 99.99% pure dihydrogen (H₂) ^[58]. The method used was that of Sievert ^[59][60]. The amount of absorbed hydrogen was determined with a volumetric method ^[61][62].

3. Structural, Microstructural, and Magnetic Characterizations of the Samples

The microstructural characterizations of the Pr₂Co₇, Pr₂Co₇−_xFe_x, Pr₂Co_xH_X, and Pr₂Co_xH_X samples were investigated by using X-ray diffraction (XRD; Bruker D8 Advance) with CuK ${}_{\alpha }$ radiation of wavelength $\lambda$ = 0.154056 nm. The refinement of the patterns was done by using the FULLPROF computing code based on the Rietveld method ^[63][64] with the assumption of the Thompson–Cox–Hastings line profile. The goodness-of-fit indicators ${\chi }^2$  and R ${}_B$ were calculated as previously described in ^[57]. Extended X-ray absorption fine-structure (EXAFS) measurements were performed on a 2.75 GeV SAMBA beamline, Synchrotron SOLEIL, France. EXAFS experiments were carried out at 293 K in the fluorescence mode using a 4-element Si(111) drift detector. The EXAFS spectra were extrapolated using the MAXeCherokee code ^[65][66], while the fitting process and comparison between theoretical and experimental EXAFS curves were carried out with the MAX-Roundmidnight package ^[65]. The theoretical phases and amplitudes used in the EXAFS models were determined with the FEFF8 code ^[67] by using the crystal structure results of the Rietveld refinements at each Fe site with the use of the MAX-CRYSTALFFREV code ^[65] for the Crystal Structure–EXAFS Modeling interface.

The morphology, the chemical compositions, and the images were considered using a JEOL 2010 FEG transmission electron microscope equipped with an energy-dispersive spectrometer (EDS). For the TEM measurements, specimens were thinned using a focused-ion-beam-type FEI Helios 600 Nanolab dual-beam instrument. The Curie temperature T ${}_C$ was measured on a MANICS differential sample magnetometer (DSM-871 Magneto/susceptometer) in a field of 1 kOe with a sample of around 5–10 × 10 ${}^{-3}$ g. T ${}_C$ was obtained from the M(T) curve by extracting the linear part of the M(T) curve and determining the temperature value of the intersection with the expanded baseline. Magnetic hysteresis M(H) loops were determined using a Physical Properties Measurement System (PPMS9) Quantum Design microscope.

4. Structural Properties

4.1. Nanocrystalline Pr₂Co₇ Compound

The nanocrystalline Pr₂Co₇ compound can crystallize into two polymorphic structures ^[54] as a function of the annealing temperature T ${}_a$ ; the first is a hexagonal (2:7 H) structure of the Ce₂Ni₇ type ( $P{6}_3/mmc$ space group) that is stable at T ${}_a$ ≤ 1023 K with the lattice parameters $a=b=5.068$ Å and $c=24.463$ Å. The second is a rhombohedral (2:7 R) structure of the Gd₂Co₇ type ( $R\overline{3}m$ space group) that is stable at Ta ${}_a$ ≥ 1223 K. The lattice parameters are $a=b=5.068$ Å and c = 36.549 ÅṪhe Pr₂Co₇ cells can be defined by stacking the hexagonal structural blocks for PrCo₅ (CaCu₅-type structure) and the cubic PrCo₂ blocks (MgCu₂- and MgZn₂-type structures) along the common hexagonal (trigonal for PrCo₂) axis ^[54]. The lattice parameters of the two structures are distinguished by the c parameter, which is higher for the 2:7 R structure due to the difference in stacking ([2H] = [BBA ${}_1$ BBA ${}_2$ ], [3R ${}_h$ ] = 3[BBA ${}_1$ ]) ^[68][69][70].

4.2. Nanocrystalline Pr₂Co₇-_xFe_x (x = 0, 0.25, 0.5, 0.75, and 1) Compounds

Figure 1 presents bright-field micrographs of the Pr₂Co₇-_xFe_0.75 (Figure 1a) compound. By performing statistical calculations on the grain size, the grain size distributions are shown in Figure 1b. The grain size ${\mathsf{\Phi }}_{TEM}$ was estimated to be 90 nm. The values found are in good agreement with the average grain sizes found using Scherrer’s expression. The HRTEM images shown in Figure 2a,b reveal the fully crystallized structure of the Pr₂Co_6.25Fe_0.75 and Pr₂Co₆Fe₁ compounds. The composition distribution was investigated by STEM–EDX mapping (Figure 2c–e. The stoichiometric proportions of Pr₂Co_7-xFe_x were maintained. The Pr, Co, and Fe compositions ranged from 20.8 to 23.5%, 78.9 to 75.5%, and 1.4 to 2.6%, respectively. The diffraction spots were distributed over the rings corresponding to the d ${}_{107}$ (0.795 nm), d ${}_{110}$ (0.635 nm), d ${}_{201}$ (0.508 nm), d ${}_{116}$ (0.458 nm), d ${}_{0012}$ (0.291 nm), d ${}_{1110}$ (0.258 nm), and d ${}_{217}$ (0.158 nm) distances for the (2:7 H) structure ^[66]

Figure 1. Bright-field micrography of the Pr₂Co_6.25Fe_0.75 compound (a). The grain size distribution is shown in the inset (b). 

Figure 2. HRTEM images (the selected area of electron diffraction is shown in the inset): (a) Pr₂Co_6.25Fe_0.75 and (b) Pr₂Co₆Fe₁ compounds annealed at 1023 K. Elemental mapping of  Pr₂Co_6.25Fe_0.75: (c) Pr, (d) Co and (e) Fe. 

4.3. Structural Analysis of Nanocrystalline Pr₂Co₇-_xFe_x  Compounds with EXAFS

Figure 3 displays the extended X-ray absorption fine structure (EXAFS) found for the Pr₂Co₇-_xFe_x compounds (x = 0.5, 0.75, and 1). The Fe–K edge is near 7120 eV, with a maximum absorbance located at 7126 eV. The apparent features of the three spectra are similar, revealing that the local structure around the Fe atoms does not change significantly with Fe content. The Fourier transforms (FTs) of the EXAFS data (Figure 3) were calculated between k ${}_{\min }$ 2 Å ${}^{-1}$ and k ${}_{\max }$ = 10.5 Å − 1 in order to to avoid disturbance and noise. The resolution is $\pi$ /(2 $\Delta$ k) = 0.18 Å. The main FT peak observed between 1.3 and 3.4 Å is due to the second atom shell (Pr and Fe) at ≈3.0 Å and the single Fe–Co scattering at ≈2.50 Å.

Figure 3. Experimental EXAFS spectra in k space of the imaginary part of the Fourier transforms of the Pr₂Co_6.5C_0.5 compound, adjusted using Models 1 and 4. Black and red lines show the experimental signal and theoretical curves, respectively.

4.4. Nanocrystalline Pr₂Co₇C_x (x = 0–1) Compounds

Pr₂Co₇C_x compounds have a predominantly hexagonal Ce₂Ni₇ structure with a P63/mmc space group. The a and c parameters and the unit cell volume V are increased during C insertion ( $\Delta$ a/a = 0.23%, $\Delta$ c/c = 10.5% and $\Delta$ V/V = 10%). Figure 4a shows a bright-field micrograph of the Pr₂Co₇C_0.75 compound. The average grain size ${\mathsf{\Phi }}_{TEM}$ is around 150 nm (Figure 4b). The HRTEM images of the nanocrystalline Pr₂Co₇C_0.75 and Pr₂Co₇C_0.75 indicate a fully crystallized structure. The compositions of Pr, Co, and C are around 23.2, 74.8, and 2 atomic percent (at.%), respectively.

Figure 4. Bright-field micrographs of Pr 2 Co 7 C 0.75 (a). The grain size distribution is shown in the inset (b). 

5. Intrinsic Magnetic Properties

5.1. Nanocrystalline Pr₂Co₇−_xFe_x (x = 0, 0.25, 0.5, 0.75, and 1) Compounds

To know the effects of Co substitution by Fe on the intrinsic magnetic properties of the alloy samples, the Curie temperature T ${}_C$ for the nanocrystalline Pr₂Co₇−_xFe_x phase was measured for each Fe content x. The nanocrystalline Pr₂Co₇−_xFe_x compounds were ferromagnetic. The T C value increased from 600 K for the nanocrystalline Pr₂Co₇−_x compound, attaining a maximum of 760 K at x = 0.5, and then decreased for x = 0.75 and x = 1. The T C values were around 695 and 667 K, respectively. The T C value was the result of two effects: the electronic effect related to the filling of the $3d$ band of Fe atoms and the magnetovolume effect related to the Co-Co distances ^[68]. The M(H) curves of the nanocrystalline Pr₂Co₇−_xFe_x compounds were measured at 293 K. The determination of $M_S$ was performed using the law of approach to saturation ^[71]:

$$\begin{array}{c}\hfill M\left(H\right)=M_S+a/H^2\end{array}$$

The M S values were converted into the magnetic moment per formula unit ${\mu }_s$ .The μ s increased linearly with increasing the Fe content x. The theoretical equation of μ s as a function of x was defined by the formula: $\mu (x=0)$ + 7x (0 ≤ x ≤ 1), where $\mu (x=0)$ is the saturation moment of the Pr 2 Co 7 − x compound (in ${\mu }_B$ /f.u). The experimental data corresponded well to the theoretical forecast. The evolution of μ s with x could be justified by the reduction in the average number of 3d electrons when replacing the Co atoms with Fe, which led to a progressive strengthening of the Co(3d)-Co(3d) exchange interactions and, thus, to an enhanced magnetic moment with the 3d ^[68]. Scholars realized the XRD patterns of Pr 2 Co 7 − x Fe x powders that were magnetically aligned at T = 293 K in a field of 0.5 T. For samples with x < 0.5, the (00l) reflections were heavily enhanced, indicating EMD along the c axis. For x > 0.5, the diagram shows a lower intensity of the (00l) peaks, while the reflections (h0l) are reinforced, implying that the EMD of the Pr 2 Co 7 − x Fe x sample deviates from the c axis.

5.2. Nanocrystalline Pr₂Co₇C_x (x = 0–1) Compounds

The Curie temperature T C of the Pr 2 Co ${}_7$ compounds was determined according to the Co-Co, Pr-Co, and Pr-Pr interactions. In general, the Co-Co interaction was dominant, and the Pr-Co and Pr-Pr interactions were negligible. From the obtained structural data, the C insertion led to a change in the a, c parameters of the Pr 2 Co 7 compound and thus to an increase in the unit cell volume V of 2.5%. The a, c parameters varied from $a=5.068$ Å and $c=24.457$ Å for Pr 2 Co 7 to $a=5.080$ Å and $c=26.980$ Å for Pr 2 Co 7 − x C. Consequently, the Co( $12k$ )-Co( 12 k ), Co( 12 k )-Co( $4f$ ), and Co( 4 f )-Co( 4 f ) distances increased the related $J_{12k-12k},J_{12k-4f}$ , and $J_{4f-4f}$ exchange interactions. As a result, the T C increased due to the magnetovolume effect.

5.3. Nanocrystalline Pr₂Co₇H_x (x = 0–10.8) Hydrides

The H absorption resulted in a variation of the lattice parameters of the Pr 2 Co 7 compound and, therefore, an increase in the cell volume V. The nearest-neighbor number of each Co atom and the Co-Co distances were then determined depending on the H content. The Co-Co distances most influenced by H absorption were those involving the Co ${}_3$ and Co ${}_5$ atoms, respectively, in the 4f and 12k sites. Therefore, the increase in the Co 5 -Co 5 , Co 3 -Co 5 ,Co 3 -Co 3 , distances led to a modification of the exchange interactions J ${}_{ij}$ ,which had some impact on the increase in T C . T C increased as a function of H content from 600 K at x = 0 to 691 K at x = 3.75, then decreased for x > 3.75. The Pr 2 Co 7 H x hydrides presented a ferromagnetic comportment for all H contents. The XRD patterns of the magnetically aligned Pr 2 Co 7 H x hydride powder samples showed only (0 0 l)-type peaks, implying that the EMDs of Pr 2 Co 7 H x hydrides were along the c axis.

5.4. Mean Field Theory (MFT) and Random Magnetic Anisotropy (RMA) Analysis

5.4.1. Nanocrystalline Pr₂Co₇H_x (x = 0–1) Compounds

The ferromagnetic alignment of the magnetic moments of Pr and Co atoms, M ${}_{Pr}$ and M ${}_{Co}$ , can be described using the following expression:

$$\begin{array}{c}\hfill M=M_{Co}+M_{Pr}\end{array}$$

M P r and M C o were estimated using mean field theory (MFT). The magnetization M can be determined using expression (5).  M C o and M P r were expected to follow the Brillouin functions ^[72]. M(T) was fitted for different C contents x. The experimental data align well with the theoretical curves. T C was found to be in agreement with the experimentally derived temperature. M P r , M C o and M were also determined for Pr 2 Co 7 C ${}_{0.25}$ (Figure 5a). The J ${}_{Co-Co}$ and J ${}_{Co-Pr}$ exchange interactions increased as a function of x, while J ${}_{Pr-Pr}$ was found to be constant around 2.10 ${}^{-23}$ J. Inserting C into the Pr 2 Co 7 induced an enhancement of T C rom 600 to 730 K when x was increased from 0 to 1 (Figure 5b). The increase in T C can be ascribed to electronic and magnetovolumic effects.

Figure 5. (a) Calculated change in the magnetic moments (M ${}_{Pr}$ (T), M C o (T)) and magnetization (M(T)) of the nanocrystalline  Pr₂Co₇C_0.25 compound. (b) The solid lines are the M(T) of nanocrystalline Pr₂Co₇H_x found calculated in the MFT analysis. The symbols show the experimental data. 

5.4.2. Nanocrystalline Pr₂Co₇H_x (x = 0–10.08) Compounds

The exchange interactions of nanocrystalline Pr 2 Co 7 H x were calculated as a function of H content using the MFT . J C o − C o and J C o − P r increased when the H content increased. The exchange interaction J ${}_{Pr-Pr}$ was around 2 × 10 ${}^{-23}$ J. M ${}_{Pr}$ (T), M ${}_{Co}$ (T), and M(T) were fitted. The T C values were found to be in good agreement with the experimentally determined values. T C increased as a function of H content from 600 K at x = 0 to 691 K at x = 3.75, dealing with an increase of about 9.1%, then decreasing for x > 3.75. The peak value appearance of T C at x = 3.75 resulted from the H content dependence of the exchange interaction parameter of J C o − C o . The enhancement of the T C of Pr 2 Co 7 H x hydrides for x ≤ 3.75 could be the result of two effects: the electronic effect associated with a decrease in the hybridization of Co(3d) atoms with their neighbors and the magnetovolume effect associated with Co-Co distances, which suggests a decrease in antiferromagnetic interaction ^[73]. The Co-Co exchange interactions increased from 166 × 10 ${}^{-23}$ J for x = 3.75. The decrease in T C for x > 3.75 was mostly due to the reduction in Co-Co exchange interactions from 178 × 10 − 23 to 130 × 10 − 23 J for x = 10.8.

5.5. Magnetocaloric Effect of the Nanocrystalline Pr₂Co₇ Compound

The measurements of the $M\left(H\right)$ curves were carried out around the Curie temperature T C going from 562 to 598 K for 2:7 (R) and from 585 to 615 K for 2:7 (H). The same type of magnetization behavior as for Pr 2 Co 7 could be observed. On the other hand, when $T>T_C$ , the Pr 2 Co 7 compound was paramagnetic, and its magnetization increased gradually with the applied field. The magnetization increased rapidly with the applied field until saturation was achieved. It should be noticed that, for the 2:7 R structure, saturation was not achieved compared to the 2:7 H structure; this was related to the presence of strong uniaxial anisotropy in this compound. Scholars traced the Arrott curves $M^2=f({\mu }_{0}H/M)$ for the Pr 2 Co 7 compound in its 2:7 H and 2:7 R structures based on the $M\left(H\right)$ isotherms found. It should be remarked that these curves showed a positive slope; this confirmed that the Pr 2 Co 7 compound for the two structures had a second-order phase transition from the paramagnetic to the ferromagnetic state ^[74].

It calculated the evolution of the magnetic entropy $\Delta S_M$ as a function of temperature T and applied field H. Figure 6 and Figure 7 show the thermal variations in the changes in magnetic entropy for the 2:7 H and 2:7 R structures, respectively. The $-\Delta S_M^{\max }$ of the 2:7 R structure was greater than that for the 2:7 H structure. As shown in Figure 7, the maximum value was about 3.7 J/(kg.K) under a magnetic field of 0–15 kOe. There were two important contributions to the maximum change in magnetic entropy Δ S M : the M ${}_s$ and $▵M_T\left(H\right)$ , which was the difference between two successive isotherms at a particular magnetic field around the temperature T C . The peak that corresponded to Δ S M became a plateau starting at T C . This transition from a single peak to a plateau was seen for the first time for a second-order magnetic transition. The relative cooling power (RCP) values were 102.7 and 8.5 J/kg, respectively, for the 2:7 R and 2:7 H structures. The calculation was based on the variation of Δ S M according to the equation: $RCP=-▵S_M\delta T_{FWHM}$ ^[8], where Δ S M and $T_{FWHM}$ are the maximum of the entropy variation and the full width at half maximum of the temperature dependence of the change in magnetic entropy Δ S M .

Figure 6. Magnetic entropy Δ S M (T) around the Curie temperature T C for the 2:7 H structure.

Figure 7. Magnetic entropy Δ S M (T) around the Curie temperature T C  for the 2:7 R structure.

6. Extrinsic Magnetic Properties

6.1. Nanocrystalline Pr ${}_2$ Co ${}_{7-x}$ Fe ${}_x$ (x = 0, 0.25, 0.5, 0.75, and 1) Compounds

To obtain a nanocrystalline state with excellent extrinsic magnetic properties, annealing was performed at different temperatures. At each annealing temperature T ${}_a$ , the hysteresis loops were measured. The evolution of Hc ${}_c$ as a function of T a initially exhibited a characteristic increase in H ${}_c$ with T a up to a maximum Hc c value, which was followed by a decrease in Hc c at higher temperatures of T a > 973 K. The most favorable microstructure for optimal magnetic properties corresponded to T a between 973 and 1073 K. The highest Hc c obtained for the nanocrystalline Pr ${}_2$ Co ${}_{6.5}$ Fe ${}_{0.5}$ compounds was Hc c = 11.5 kOe and Hc c = 12 kOe, respectively. The respective values of remanent magnetization M ${}_r$ were 43 and M r = 48 emu/g. The decrease in Hc c could mainly be due to the decrease in magnetocrystalline anisotropy after the substitution. Hc c depended principally on the magnetocrystalline anisotropy H a . The substitution of Co by Fe implied a reduction of the contribution of the $3d$ axial and, thus, a decrease in Hc c as a function of x, as has been shown by X-ray diffraction in oriented powders ^[68]. Scholars studied the evolution of (BH) ${}_{\max }$ . The (BH) max value increased with T a and then decreases when T a increased for all values of Fe content x.

6.2. Nanocrystalline Pr 2 Co 7 H x (x = 0–1) Compounds

Figure 8 shows the hysteresis loops of the Pr 2 Co 7 , Pr 2 Co 7 C ${}_{0.25}$ and Pr 2 Co 7 C ${}_{0.75}$ compounds annealed at 1073 K and measured at 293 K. The hysteresis loops show that these compounds are isotropic and confirm that they have only one ferromagnetic phase. Scholars present in Figure 9 the evolution of H c as a function of annealing temperature T a for the Pr 2 Co 7 H x compounds. The curve passes through a maximum for $T_a$ = 1073 K. Two regions are thus highlighted; they are correlated to the mean grain size and the defects. The Hc c increases with T a in the lattice with the 2:7 H structure, i.e., with the grain size and the reduction of the defects, until the critical value found at 1073 K. The grains get bigger and Hc c decreases.

Figure 8. Hysteresis loops of the Pr 2 Co 7 , Pr 2 Co 7 C 0.25 and Pr 2 Co 7 C 0.75 compounds, measured at 293 K. 

Figure 15. (a) The evolution of the coercivity H c as a function of annealing temperature T a of the Pr 2 Co 7 H x compounds ( $x=0,0.25$ ). (b) The grain size as a function of C content x is shown in the inset.

6.3. Nanocrystalline Pr 2 Co 7 H x (x = 0–10.8) Compounds

The demagnetization curves found in the hysteresis loops of the Pr 2 Co 7 H x hydrides (x = 0.25, 6.1, and 10.8) were smooth, indicating a fine and uniform grain size $\mathsf{\Phi }$ for these hydrides ^[73]. The Pr 2 Co 7 H 0.25 hydride had the highest extrinsic magnetic properties compared to the other Pr 2 Co 7 H x hydrides: Hc c = 6.1 KOe, (BH) max = 5.8 MGOe, M r = 40 emu/g, and remanence ratio M r /M max = 0.62. The Hc c decreased with x from about 11.5 KOe at x = 0 to 0.33 KOe at x = 10.8. The M r values ranged from 42.5 to 40.25 emu/g. The decrease in Hc c and (BH) max as a function of H content could mainly be due to the decrease in magnetocrystalline anisotropy resulting from the H absorption. The main interest lies in the fact that hydrogenation increased Tc c by a factor of almost 9.1% for x = 3.75 compared with the Pr 2 Co 7 compound. The Pr 2 Co 7 H 3.75 hydride could be considered as a soft material; it finds its applications in the field of magnetic recording or storage of information.

This entry is adapted from the peer-reviewed paper 10.3390/magnetochemistry8020020