United States

Pressure sensor (PS) has important application in artificial intelligence and modern industries. Baromagnetic effect (BME), i.e., pressure-induced magnetic moment change, is regarded as the candidate technology for new PS. The reported large BME in Mn&lt;sub&gt;3&lt;/sub&gt;Ga&lt;sub&gt;0.95&lt;/sub&gt;N&lt;sub&gt;0.94&lt;/sub&gt;[1] has gained great attention. The origin comes from the pressure-induced spin re-orientation from Γ&lt;sup&gt;5g&lt;/sup&gt; antiferromagnetic (AFM) to M-1 ferrimagnetic phase. Recently, the ternary metallic compounds MM’X (M, M’ = transition metals, X = main elements) have attracted renewed attention due to their barocaloric effect[2], and giant negative thermal expansion[3]. In the MM’X family, previous research indicated that the AFM coupling of the stoichiometric MnNiGe is very robust. The substitution of Mn with Fe introduces Fe-Mn ferromagnetic (FM) coupling, which can help to establish a cone-spiral magnetic coupling[4]. Hence, a new cycloidal spiral AFM structure (CyS-AFM&lt;sup&gt;b&lt;/sup&gt;) was discovered in Mn&lt;sub&gt;0.87&lt;/sub&gt;Fe&lt;sub&gt;0.13&lt;/sub&gt;NiGe[5], which is sensitive to magnetic field and stress. As a result, a giant BME was achieved.&lt;br/&gt;The employed Mn&lt;sub&gt;0.87&lt;/sub&gt;Fe&lt;sub&gt;0.13&lt;/sub&gt;NiGe alloy were prepared by arc-melting technique. The CyS-AFM&lt;sup&gt;b&lt;/sup&gt; was discovered in Mn&lt;sub&gt;0.87&lt;/sub&gt;Fe&lt;sub&gt;0.13&lt;/sub&gt;NiGe below 150 K. A low magnetic field can make the CyS-AFM&lt;sup&gt;b&lt;/sup&gt; transform to a conical spiral FM with angle 70°(70°-CoS-FM&lt;sup&gt;b&lt;/sup&gt;), accompanied by a step rise of magnetization (Fig.1). More importantly, the new CyS-AFM&lt;sup&gt;b&lt;/sup&gt; is no longer insensitive to stress compared to the MnNiGe without Fe-doping. A pressure higher than 4kbar induces abnormal change of Mn(Fe)-Mn(Fe) distances hence transform the CyS-AFM&lt;sup&gt;b&lt;/sup&gt; into a conical spiral ferromagnetic configuration(45°-CoS-FM&lt;sup&gt;a&lt;/sup&gt;) with easily magnetized but much shortened magnetic moment (Fig.2). As a result, giant BME was observed under either a low magnetic field or a field of 2T~5T. The maximal BMC appears to be ~5.34 emu/g&lt;sup&gt;*&lt;/sup&gt;kbar under 0.35T while ~9.03emu/g&lt;sup&gt;*&lt;/sup&gt;kbar under 2.2T in a wide temperature range, which all far exceed those of the previous reported Mn&lt;sub&gt;3&lt;/sub&gt;Ga&lt;sub&gt;0.95&lt;/sub&gt;N&lt;sub&gt;0.94&lt;/sub&gt;.

![](https://assets.underline.io/uploads/markdown_image/1/image/09482e36daa9f397642695bac745587e.jpg)

Fig.1. a)M-H curve at 5K with the sketch of spin structure evolution with H, b)Variable magnetic field NPD patterns at 5K, and c)phase diagram.

![](https://assets.underline.io/uploads/markdown_image/1/image/40c700b274a5a459169e05205fd24437.jpg)

Fig.2. The sketch of a)the CyS-AFMb andb)the 45°-CoS-FMa, and the variable pressure NPD patterns at 120K.

2022 Joint MMM-INTERMAG

A new spin structure and giant baromagnetic effect in Mn0.87Fe0.13NiGe alloy

The 15th Joint MMM-INTERMAG Conference (2022 Joint) is sponsored jointly by AIP Publishing and the IEEE Magnetics Society. Members of the international scientific and engineering communities interested in recent developments in fundamental and applied magnetism are invited to attend and contribute to the technical sessions. The technical program will include invited and contributed papers in oral and poster sessions, invited symposia, a plenary session, and an evening session, with about 1500 presentations overall. This Conference provides an outstanding opportunity for worldwide participants to meet their colleagues and collaborators and discuss developments in all areas of magnetism research.

The 2022 Joint Conference will offer both in-person and prerecorded on-demand content.

For tickets to the event, please register at the following link: https://magnetism.org/register

Please register for the Joint MMM-Intermag conference to join the event.

This Conference provides an outstanding opportunity for worldwide participants to meet their colleagues and collaborators and discuss developments in all areas of magnetism research.

Pressure sensor (PS) has important application in artificial intelligence and modern industries. Baromagnetic effect (BME), i.e., pressure-induced magnetic moment change, is regarded as the candidate technology for new PS. The reported large BME in Mn3Ga0.95N0.94[1] has gained great attention. The origin comes from the pressure-induced spin re-orientation from Γ5g antiferromagnetic (AFM) to M-1 ferrimagnetic phase. Recently, the ternary metallic compounds MM’X (M, M’ = transition metals, X = main elements) have attracted renewed attention due to their barocaloric effect[2], and giant negative thermal expansion[3]. In the MM’X family, previous research indicated that the AFM coupling of the stoichiometric MnNiGe is very robust. The substitution of Mn with Fe introduces Fe-Mn ferromagnetic (FM) coupling, which can help to establish a cone-spiral magnetic coupling[4]. Hence, a new cycloidal spiral AFM structure (CyS-AFMb) was discovered in Mn0.87Fe0.13NiGe[5], which is sensitive to magnetic field and stress. As a result, a giant BME was achieved. The employed Mn0.87Fe0.13NiGe alloy were prepared by arc-melting technique. The CyS-AFMb was discovered in Mn0.87Fe0.13NiGe below 150 K. A low magnetic field can make the CyS-AFMb transform to a conical spiral FM with angle 70°(70°-CoS-FMb), accompanied by a step rise of magnetization (Fig.1). More importantly, the new CyS-AFMb is no longer insensitive to stress compared to the MnNiGe without Fe-doping. A pressure higher than 4kbar induces abnormal change of Mn(Fe)-Mn(Fe) distances hence transform the CyS-AFMb into a conical spiral ferromagnetic configuration(45°-CoS-FMa) with easily magnetized but much shortened magnetic moment (Fig.2). As a result, giant BME was observed under either a low magnetic field or a field of 2T~5T. The maximal BMC appears to be ~5.34 emu/g*kbar under 0.35T while ~9.03emu/g*kbar under 2.2T in a wide temperature range, which all far exceed those of the previous reported Mn3Ga0.95N0.94.

![](https://assets.underline.io/uploads/markdown_image/1/image/09482e36daa9f397642695bac745587e.jpg)

Fig.1. a)M-H curve at 5K with the sketch of spin structure evolution with H, b)Variable magnetic field NPD patterns at 5K, and c)phase diagram.

![](https://assets.underline.io/uploads/markdown_image/1/image/40c700b274a5a459169e05205fd24437.jpg)

Fig.2. The sketch of a)the CyS-AFMb andb)the 45°-CoS-FMa, and the variable pressure NPD patterns at 120K.

poster

Gadolinium (Gd) films have been considered for micro and nano-scale application, because of their high magnetic moment and a Curie point close to room temperature (RT) [1]. Recently, free-standing thick films have been pointed out as promising active substance in energy conversion micro-devices [2] due to their magnetocaloric properties (MC). Indeed, as put in [2], good MC properties, surface quality, absence of substrate, and flexibility are the main features to get a caloric membrane to be deployed in a micro-electromechanical system (MEMS). Unfortunately, a systematic study of the optimal preparation parameters to obtain the aforementioned properties, is still lacking. Actually, film thickness, growth temperature, and the choice of the buffer layer, are all key features affecting the final result after substrate removal. Here, polycrystalline Gd films are prepared by sputtering on a silicon substrate with a thermally oxidized layer. Thickness of the film is varied from 100 nm to 17 μm, exploring growth temperatures in an interval between RT up to 666 K. Buffer layers of tungsten (W) and tantalum (Ta) are used. More than 45 Gd thick films with various growth temperatures, thicknesses and buffer layers have been prepared. The first result is that notwithstanding the growth temperature and thickness, tungsten buffer makes the substrate removal more difficult, particularly over large film surfaces (e.g. tens millimetres size). Increasing the growth temperature improves the magnetic properties [3] and changes the surface morphology. For instance, surface roughness is 10 nm and 121 nm for films prepared at 543 K and 666 K, respectively. Using tantalum, wide area free-standing films of various thicknesses from 5 to 17 μm have been obtained, with a flexibility depending on the growth temperature. Thinner free-standing films, namely 3 μm Ta/Gd/Ta have also been obtained showing smaller sizes (i.e. few millimeters size). In summary, the main result here is the identification of optimal preparation conditions (buffer layer, growth temperature and thickness) to obtain large, smooth and flexible Gd films to be used in MEMS device as a magnetocaloric membrane.

Producing gadolinium free-standing and flexible films, with high quality surface for energy applications: the role of thickness and growth temperature

ABO3 type compounds with perovskite structure are known to exhibit a very rich variety of phase transitions ranging from ferroelectric, antiferroelectric, ferrielectric, antiferrodistortive octahedral tilt, ferromagnetic, antiferromagnetic, ferrimagnetic, John-Teller, metal-insulator and superconducting transitions [1]. The richness of these phenomena is further enhanced by introducing substitutional disorder at the A or B sites leading to relaxor ferroelectricity, dipole-glass, spin-glass and quantum phase transitions [2]. The technological applications of these perovskites is due to the functional properties imported by such phase transitions. In this context, the B-site disordered iron-niobate family has evinced considerable interest due to the temperature stable giant dielectric constant and multiferroicity. The low temperature magnetic transitions and the ground state of these complex perovskites is now fully understood [3,4]. However, understanding of the high temperature behaviour is still lacking. In the present investigation, we report high temperature phase transitions in Sr(Fe1/2Nb1/2)O3 (SFN) using dc magnetization and x-ray diffraction measurements. Our dc magnetization M (T) study reveals two magnetic transitions around 620 K and 700 K for the first time. The magnetic transition occurring around 620 K is linked with the structural phase transition as confirmed by temperature dependent x-ray diffraction studies. The integrated intensity of the strongest superlattice reflection (ISL) and the octahedral tilt angle (φ) decrease continuously with increasing temperature and vanishes across the structural phase transition. We have fitted temperature variation of both ISL and φ using the expressions B(TC-T)β and B(TC-T)2β, respectively, where B is constant, TC is the structural phase transition temperature and β is critical exponent. The value of β comes out to be 0.24 which suggests the tricritical nature of the phase transition. Another transition around 700 K in the M (T) plot occurs close to the peak temperature in the loss tangent (tanδ). We believe that this transition is most likely driven by oxygen vacancies.

![](https://assets.underline.io/uploads/markdown_image/1/image/6e631abc07abd6eec3192e6391959901.jpg)

DC magnetization versus temperature plot of Sr(Fe1/2Nb1/2)O3 at 100 Oe field

Magneto-structural phase transition in the B-site disordered Sr(Fe1/2Nb1/2)O3 perovskite: A combined dc magnetization and x-ray diffraction study

Magnetocaloric effect is a new nonconventional method that can be used to provide cooling power with several benefits compared to conventional gas-compression based cooling. Heusler alloys are promising candidates for micro-magnetic cooling applications thank their desirable behaviour. Preparation of Heulser alloys in a form of glass-coated microwires by the Taylor-Ulitovsky technique allows easy and fast production of microwires with protective glass coating and many additional advantages such as scalability of the size of cooling material. Previous works show the possibility of tuning the structural and magnetic transformation temperature of glass coated Heusler microwires by changing the chemical composition and valence electron concentration ratio e/a. This is one of the most favourable properties of glass coated Heusler microwires. Combining structural and magnetic transformation may enhance the amplitude of the magnetocaloric effect when both transformations overlap, the evaluation of their contribution may become complicated. Therefore, we would like to present the possible analyses which can provide information about the magnetocaloric effect or the transformation temperatures including both structural and magnetic transitions. Direct measurements of magnetocaloric effect, indirect measurement of magnetocaloric effect, resistivity measurements, Arrott plot method, universal curves, method of critical exponent n, Kouvel-Fisher method with Arrott-Noakes plots and many others can be used to study the magnetocaloric effect and transformations on a presented group of alloys. This research was supported by Slovak Grant Agency VEGA 1/0053/19, Slovak Grant Agency grant number APVV-16-0079.

Magnetocaloric Effect Study on Heusler Based Glass-Coated Microwires

Mn0.5Fe0.5NiSi0.95Al0.05 is a member of the MnTX (T = Ni, Co; X = p-block elements) family of intermetallic compounds. It exhibits a first-order ferromagnetic transition coupled with a structural phase transition at 315 K. Near this transition a large magnetic entropy changes of ~17 J kg-1 K-1, for a field change of ΔH = 2 T, has been reported for Mn0.5Fe0.5NiSi0.95Al0.05.[1] In this work, we present an experimental study on the crystalline, magnetic, and magnetocaloric properties of Ni deficient (Mn-rich) Mn0.525Fe0.5Ni0.975Si0.95Al0.05. The study has been performed by x-ray diffraction, scanning electron microscopy, and dc magnetization measurements. X-ray diffraction measurements showed that the sample simultaneously exhibited the orthorhombic and hexagonal structures at room temperature. The ferromagnetic transition temperature occurred at ~338 K, which is significantly larger than 315 K observed in Mn0.5Fe0.5NiSi0.95Al0.05. A maximum magnetic entropy changes of ΔSM = -9.5 and 25 J kg-1K-1 for ΔH = 2 T and 5 T, respectively, has been observed. Reasonably large refrigeration capacity of 60 J /kg and 160 J/kg for field changes of ΔH = 2 T and 5 T, respectively, has also been observed. The experimental results and related discussions will be presented in detail. Work at SUNY, Buffalo State was supported by the startup fund from SUNY Buffalo State College and Undergraduate Summer Research Fellowship award, Undergraduate Research Office, Buffalo State.

Near room temperature magnetocaloric properties in Ni deficient Mn0.525Fe0.5Ni0.975Si0.95Al0.05

Magnetic cooling obtained from magnetocaloric (MC) effect can be used as a substitute to usual refrigeration [1]. Recently, few reports illustrated the MC effect in Gd based compounds [1-2]. Das et al. [2], found the MC effect in exchange frustrated bulk magnet, GdCrTiO5, where the origin of strong frustration is due to exchange interaction of Gd3+ and Cr3+ sublattices. There are limited reports on the magnetic properties of bulk GdCrTiO5 [2-4], but none focused on the nano-dimension. Therefore, in the present case, the structural and magnetic properties of sol-gel synthesized and subsequent calcined (at 800 °C) GdCrTiO5 nanoparticles were explored. The synthesized GdCrTiO5 nanoparticles stabilizes in a orthorhombic crystal structure with space group Pbam, with lattice parameters, a, b, c of 7.381(2), 8.679(2), 5.862(2) Å, respectively, as confirmed from the x-ray diffraction measurements. The transmission electron microscopy shows the particle size as 37 ± 1 nm. The temperature dependence of dc magnetization, M(T), was measured for GdCrTiO5 nanoparticles and the Néel temperature, TN = 190 ± 2 K, obtained. At low fields, the spins of the Cr and Gd align in opposite directions to each other and the net moment align in the opposite direction to the applied field, in the temperature range 10 to 108 K. Additionally, spin reorientation is observed at temperature of TSR = 17 ± 3 K. Irreversibility appeared in field-cool-cooling (FCC) and field-cool-warming (FCW) curves at low temperatures, indicating a ferromagnetic-antiferromagnetic (FM-AFM) transition. This FM-AFM transition and TSR was not observed in bulk GdCrTiO5 [2-4]. Both FM nature and exchange bias effect is further established from the field-dependent magnetization measurements. Furthermore, a change in isothermal magnetic entropy (-ΔSm) of 22 ± 3 J.kg-1.K-1 is found below 10 K, for a 7 T change in field. The obtained magnetic properties in this report are discussed in terms of exchange frustration originating from the competing interactions of the magnetic sublattices of the Cr3+ and Gd3+ in the GdCrTiO5 nanoparticles.

![](https://assets.underline.io/uploads/markdown_image/1/image/426fc49bea4c68ae303d0c9fb7b3f46d.jpg)

Fig. 1. M(T) data for GdCrTiO5 nanoparticles.

Anomalous Magnetic Properties of GdCrTiO5 Nanoparticles

In this paper, we report the variations observed in magnetothermal, magnetocaloric, and magnetic properties of the Gd2In1-xGex (0 ≤ x ≤ 0.2) system of compounds concerning the changes in substitution of Ge. Changes have been recorded in a temperature sweeping range of 2-300 K while the magnetic field was increased from 0 to a maximum of 5 T. All the compositions set into the Ni2In-type hexagonal structure and no structural changes are observed with the change in the value of x. Though the transition temperature values, which are TC ≈ 191 K and TN ≈ 100 K in case of x = 0, have only subtle shifts with the Ge substitution yet promising changes have been observed in the magnetocaloric effect. At x = 0.2 the isothermal magnetic entropy variation peak touches the value of ~ 2.5 J/kg.K in a field change from 0 to 5 T. This showcases that the compounds reported can meet the challenge of the influential applicants in the race of magnetocaloric compounds.

![](https://assets.underline.io/uploads/markdown_image/1/image/4724d1db55dd31b90895358fbd9adc22.jpg)

First derivative of the magnetization curve of the compound Gd2In0.8Ge0.2 revealing the transition temperature clearly. The TN (Néel temperature) is the antiferromagnetic transition temperature while TC (Curie temperature) is the ferromagnetic transition temperature.

![](https://assets.underline.io/uploads/markdown_image/1/image/c153c4dca4cd946b35e4fb0d2350021a.jpg)

Change in isothermal magnetic entropy vs. temperature for the Gd2In1-xGex (0 ≤ x ≤ 0.2) system of compounds in the vicinity of TN.

Modifications in the magnetocaloric effect owing to composition changes in Gd2In1-xGex (0 ≤ x ≤ 0.2) system of compounds

Rare-earth orthochromites (RCrO3, R = rare-earth element) with a distorted perovskite structure have attracted attention due to their unusual physical properties, including temperature-induced magnetization reversal, spin-reorientation, spin-flipping, Magneto-caloric effect (MCE), and exchange-bias [1]. These materials represent a new class of multiferroic, which exhibit the coexistence of ferroelectric and magnetic orders below the Néel temperature (TN) [2]. It has been found that the magnetic behavior of RCrO3 compounds is strongly influenced by the Cr3+–Cr3+ super-exchange interaction rather than the R3+–Cr3+ and R3+–R3+ super-exchange interactions [1, 3]. In this contribution, the structural and magnetic properties of magneto-caloric DyCrO3 are studied. The sample was prepared by sol-gel method and calcined at 900 °C to yield an average particle size of 175 ± 10 nm with an average crystallite size of 65.07 ± 0.06 nm and lattice strain of 0.0038 ± 0.0006, as determined from transmission electron microscopy (TEM) and Williamson-Hall analysis of x-ray diffraction patterns, respectively. Rietveld refinement of the powder x-ray diffraction patterns was performed using GSAS software (Fig. 1), based on centro-symmetric space group Pbnm. Magnetization measurements as a function of temperature, with different probing magnetic fields, were carried out to determine the various magnetic transitions in the sample under zero field cooled (ZFC) and field cooled (FC) modes (Fig. 2). DyCrO3 orders AFM ascribed to the Cr magnetic order at TNCr ≈ 147 K. The magnetization increases for T &lt; TNCr. This is the paramagnetic response of Dy3+ ions, as these continuously rotate to align with the Cr3+, before the Dy3+ order at TNDy at about 5 K [4]. This magnetic transition contributes to the MCE of DyCrO3.This behavior is in agreement with previously reported values [5]. The transition temperatures observed in the curves are validated with measurements. The cause of observed anomalies in magnetic transition will be discussed considering the magnetic interactions and structural changes.

![](https://assets.underline.io/uploads/markdown_image/1/image/337c315947dc543b01368af5183af4ab.jpg)

Fig. 1

![](https://assets.underline.io/uploads/markdown_image/1/image/28b3b93b5c44ff7ab8b854447a9a183d.jpg)

Fig. 2

Rare-earth chromite DyCrO3: Structural and magnetic properties

First-order magnetic phase transitions (FOMPTs) generally occur due to concurrent discontinuous changes in magnetic and crystallographic sublattices. FOMPTs that involve changes in crystallographic symmetry are known as magneto-structural (MSTs), and they are commonly known as magneto-elastic (METs) when lattice symmetry remains invariant across the transition. Both MSTs and METs can give rise to plethora of functionalities. Here we report a peculiar magnetic phase transition in a lanthanide-based compound – Nd2In – which is neither MST nor MET, but it has handful of features generally observed across FOMPTs. Nd2In shows a non-hysteric paramagnetic-ferromagnetic transition with a nearly discontinuous change in magnetization at TC ~ 109 K, a typical FOMPT feature, and a broad second-order transition at ~52 K. The transition at TC is also manifested as a sharp peak in heat capacity around TC and much larger than recently reported1 magnetocaloric effect with the maximum calculated entropy change (ΔS) of -13 J/ Kg K in a 2 T magnetic field change. This behavior is qualitatively similar to other R2In compounds where magnetoelastic FOMPTs are well established.2,3 Further, the temperature and magnetic field dependence of ΔS can be expressed as ΔS ~ Hn, where the local exponent, n, varies with both magnetic field and temperature, showing clear maxima with n &gt; 2, a characteristic feature of FOMPT.4 The temperature-dependent X-ray powder diffraction study, on the other hand, shows no evidence of lattice volume discontinuity or change of crystal symmetry across TC. Acknowledgement: This work was performed at Ames Laboratory and was supported by the Division of Materials Science and Engineering of the Office of Basic Energy Sciences of the U.S. Department of Energy (DOE). Ames Laboratory is operated for the U.S DOE by Iowa State University under Contract No. DE-AC02-07CH11358.

Peculiar magnetic phase transition and large magnetocaloric effect in Nd2In

We investigate magnetic, thermal, and magnetocaloric properties of rare earth intermetallic compounds with 0.25, 0.5 and 0.75, through a theoretical model Hamiltonian that considers contributions of the crystalline electric field anisotropy in both Tm and Dy magnetic sublattices, disorder in exchange interactions among Tm-Tm, Dy-Dy and Tm-Dy magnetic ions, and the Zeeman effect. Employing earlier reported [1] and new experimental measurements, we first determine a single free variable, the intersublattice magnetic exchange parameter, to properly model the temperature and magnetic field dependencies of heat capacity and magnetization. Then we used the modeling results to explain the emergence of an anomalous spin reorientation transition and its influence on the magnetocaloric effect in the title compounds. Theoretical results agree with experimental data reasonably well.

Magnetic and magnetocaloric properties of TmxDy1-xAl2 (x = 0.25, 0.50 and 0.75)

Multi-component alloys contain more than 4 elements in percentages between 12 to 35%, this can lead to single or dual phase alloys. These dual phase alloys have been shown to have promising magnetic properties [1,2], therefore further investigation is required. Two studies were carried out on the CoFeNi0.5AlCrx alloy to investigate how the structural and magnetic properties change as a function of Cr concentration and post-synthesis heat treatment. The addition of Cr to CoFeNi0.5Al changed the alloy from single phase BCC to dual phase BCC, due to the formation of nanoparticles within a matrix (Fig 1a). The Cr also reduced the saturation magnetisation at 300K. The dual phases gave rise to 2 different magnetic phases: i. high Curie temperature (Tc) almost independent of Cr, ii. low Tc decreasing with increasing Cr (Fig 1b). For CoFeNi0.5Cr0.5Al, four post heat treatments were investigated, these were either heated at 1423K for 5 or 10hrs, then either furnace cooled or water quenched. All the samples were BCC, with the water quenched 10hrs (WQ10) and furnace cooled 5 and 10hrs (FC5 and FC10) alloys all having nanoparticles within a matrix, while the water quenched 5hrs (WQ5) alloy had no clear separation of phases. These differences were observed in the Tc, as for WQ10, FC5 and FC10 alloys there were 2 distinct transition in the M-T curves (Fig 1c), while for WQ5 the transition appear as one broad change. The magnetocaloric properties were studied for all the CoFeNi0.5AlCrx alloys. It was found that Cr decreased the change in entropy (ΔS) for both Tc (Fig 1d). For all alloys, the low Tc had a smaller ΔS compared to the high Tc but a larger refrigerant capacity due to a wider temperature transition. For CoFeNi0.5AlCr0.25, the two Tc were within 100K of each other, such that the ΔS curves overlapped giving a wider temperature range, and a refrigerant capacity of 150J/K. Thus tuning the two transitions to be &lt;100K of each other increases the refrigerant capacity.

![](https://assets.underline.io/uploads/markdown_image/1/image/585620410c5d908d21de5098c3a453fc.jpg)


Figure 1a. SEM images of CoFeNi0.5AlCrx, Magnetisation as a function of temperature at 20 kA/m for 1b. CoFeNi0.5AlCrx and 1c. CoFeNi0.5AlCr0.5 and 1d. Change in entropy as a function of Cr concentration (open shapes = low Tc, and solid shapes = high Tc)

A new spin structure and giant baromagnetic effect in Mn0.87Fe0.13NiGe alloy

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