Magnetocaloric effect of Mn-Fe-P-Si-B-V alloy and use thereof

Abstract

The invention provides an alloy comprising e.g. manganese, iron, vanadium, phosphor and silicon. The invention also provides an apparatus comprising a magnetic field generator, a heat sink, the thermo element, a heat source, and a control system, wherein in a controlling mode the control system is configured to select between (i) a first configuration wherein the magnetic field generator generates a magnetic field, the thermo element is exposed to the magnetic field, and heat from the thermo element is transferred to the heat sink, and (ii) a second configuration, wherein the thermo element is not exposed to the magnetic field, and heat from a heat source is transferred to the thermo element.

Claims

1. An alloy comprising metal elements and non-metal elements, wherein the metal elements comprise manganese, iron, and vanadium, and wherein the non-metal elements comprise phosphor and silicon.

2. The alloy according to claim 1, wherein an atom ratio of the metal elements to the non-metal elements is within the range of 1.8-2.1:1.

3. The alloy according to claim 1, wherein an atom ratio of the metal elements to the non-metal elements is within the range of 1.93-1.97:1.

4. The alloy according to claim 1, wherein an atom ratio of the vanadium element to the other metal elements is selected from the range of 0.01:1.94-0.04:1.86.

5. The alloy according to claim 1, further comprising one or more of C, N, B, wherein an atom ratio of C, N and B to phosphor and silicon ([C]+[N]+[B])/([P]+[Si]) is equal to or smaller than 0.1.

6. The alloy according to claim 1, wherein an atom ratio of the silicon element is in a molar fraction of the non-metal elements ranging from 0.3 to 0.6, with the remainder being (i) P, or (ii) P, and one or two out of C, N, B.

7. The alloy according to claim 1, wherein an atom ratio of the silicon element is in a molar fraction of the non-metal elements ranging from 0.3 to 0.6, with the remainder being P, and C, N, and B.

8. The alloy according to claim 1, obtainable by pre alloying starting materials for the alloy and a subsequent heat treatment at a temperature selected from the range of 1300-1500 K over a period of time selected from the range from minutes to weeks.

9. The alloy according to claim 1, shaped to facilitate fast heat transfer.

10. An apparatus configured to execute one or more of (a) cooling during a first operation mode, and (b) heating during a second operation mode, wherein the apparatus comprises a thermo element comprising the alloy according to claim 1.

11. The apparatus according to claim 10, further comprising: a magnetic field generator, a heat sink, and a control system, wherein in a controlling mode the control system is configured to select between (i) a first configuration wherein the magnetic field generator generates a magnetic field, the thermo element is exposed to the magnetic field, and the thermo element is in thermal contact with the heat sink, and (ii) a second configuration, wherein the thermo element is not exposed to the magnetic field, and the thermo element is not in thermal contact with the heat sink.

12. The apparatus according to claim 10, further comprising a fluid system, wherein the fluid system is configured to contain a fluid, and wherein the fluid system is configured to provide thermal contact between the thermo element and the fluid.

13. The apparatus according to claim 12, wherein the liquid comprises a nonflammable, nontoxic, greenhouse-effect neutral fluid that does not boil or freeze in the desired temperature range.

14. A system comprising the apparatus according to claim 10, wherein the system is configured to heat, to cool, or to heat and cool, respectively, or to generate mechanical energy.

15. The system according to claim 14, wherein the system is configured as a refrigerator, wherein in a controlling mode of the system, the system is configured to pump heat from sub ambient levels to a temperature in the range from ambient down to 21 OK to temperatures above ambient.

16. The system according to claim 14, wherein the system is configured as a heater, wherein in a controlling mode of the system, the system is configured to pump heat from sub ambient levels to temperatures above ambient up to 380K.

17. The system according to claim 14, further comprising a magnetic field source and a thermal switch, wherein the system is configured to generate mechanical and/or electrical energy.

18. A method for producing the alloy according to claim 1, comprising providing a combination of starting materials to produce the alloy, and heating the combination of starting material until the alloy is obtained.

19. The method according to claim 18, wherein the starting materials comprise at least one of elemental starting materials or a pre alloyed starting material, and wherein the heating comprises heating at a temperature selected from the range of 1300-1500 K.

20. (canceled)

21. The apparatus according to claim 10, further comprising: a magnetic field generator, a heat sink, a heat source, and a control system, wherein in a controlling mode the control system is configured to select between (i) a first configuration wherein the magnetic field generator generates a magnetic field, the thermo element is exposed to the magnetic field, and heat from the thermo element is transferred to the heat sink, and (ii) a second configuration, wherein the thermo element is not exposed to the magnetic field, and heat from the heat source is transferred to the thermo element.

Description

BRIEF DESCRIPTION OF THE DRAWINGS

[0057] Embodiments of the invention will now be described, by way of example only, with reference to the accompanying schematic drawings in which corresponding reference symbols indicate corresponding parts, and in which:

[0058] FIG. 1: Magnetizations as a function of temperature for Mn.sub.1.2-xV.sub.xFe.sub.0.75P.sub.0.5Si.sub.0.5 (x=0.00, 0.01, 0.02, 0.03, 0.04 and 0.05) alloys after annealing at 1323, 1373 and 1423 K; The T.sub.C for Mn.sub.1.2-xV.sub.xFe.sub.0.75P.sub.0.5Si.sub.0.5 alloys after annealing at 1323, 1373, 1423K is on the right bottom with V (at %) indicating the content;

[0059] The annealing temperatures are indicated in the Figures; this also applies to the following figures;

[0060] FIG. 2: Relationship between the lattice parameters a and c, c a, and the phase fraction of impurity and the V content of Mn.sub.1.2-xV.sub.xFe.sub.0.75P.sub.0.5Si.sub.0.5 (x=0.00, 0.01, 0.02, 0.03, 0.04, 0.05) alloys after annealing at 1323, 1373 and 1423K;

[0061] FIG. 3: (a) Neutron diffraction patterns and the refinement result of the Mn.sub.1.18V.sub.0.02Fe.sub.0.75P.sub.0.5Si.sub.0.5 alloy annealed at 1373 K; on the y-axis the intensity (counts) is indicated with I(C); NDP indicates neutron diffraction pattern, FC indicates fullprof calculated (NDP and FC essentially overlap); BP indicates Bragg positions; D indicates difference between NDP and FC; (b) Interatomic distance (ID) as a function of annealing temperature (T.sub.a (in Kelvin)) for Mn.sub.1.2Fe.sub.0.75P.sub.0.5Si.sub.0.5 alloys and the one pointed out by arrow represents the Mn.sub.1.18V.sub.0.02Fe.sub.0.75P.sup.0.5Si.sup.0.5 annealing at 1373 K;

[0062] FIG. 4: (a) Temperature dependence of |ΔS.sub.M| for a field change of 0-1 T (open symbols) and 0-2 T (solid symbols) for Mn.sub.1.2-xV.sub.xFe.sub.0.75P.sub.0.5Si.sub.0.5 (x=0.00, 0.01, 0.02, 0.03, 0.04) alloys after annealing at 1323 K; (b) Temperature dependence of |ΔS.sub.M| for a field change of 0-1 T (open symbols) and 0-2 T (solid symbols) for Mn.sub.1.2-xV.sub.xFe.sub.0.75P.sub.0.5Si.sub.0.5 (x=0.00, 0.01, 0.02, 0.03) alloys after annealing at 1373 K; (c) Temperature dependence of |ΔS.sub.M| for a field change of 0-1 T (open symbols) and 0-2 T (solid symbols) for Mn.sub.1.2-xV.sub.xFe.sub.0.75P.sub.0.5Si.sub.0.5 (x=0.00, 0.01, 0.02, 0.03, 0.05) alloys after annealing at 1423 K;

[0063] FIG. 5: (a) Temperature dependence of ΔT.sub.ad (adiabatic temperature change) for Mn.sub.1.2-xV.sub.xFe.sub.0.75P.sub.0.5Si.sub.0.5 (x=0.00, 0.01, 0.02) alloys annealed at 1323 K; (b) Temperature dependence of ΔT.sub.ad for Mn.sub.1.2-xV.sub.xFe.sub.0.75P.sub.0.5Si.sub.0.5 (x=0.00, 0.01, 0.02) alloys annealed at 1373 K. The solid, half-solid and open symbols represents the applied field of 1.5 and 1.0 T, respectively;

[0064] FIG. 6: (a) Lattice parameters of the a and c axis for series A and (b) c/a ratio and T.sub.C for series A; (c) Lattice parameters of the a and c axis for series B and (d) c a ratio and T.sub.C for series B; (e) Fraction (F; in volume %) of the second phase in series A and B; (f) Unit cell volume of series A and B;

[0065] FIG. 7: (a) Temperature dependence of the magnetization in series A under an applied magnetic field of 1 T; (b) Temperature dependence of the magnetization in series B under an applied magnetic field of 1 T;

[0066] FIG. 8: (a) Temperature dependence of |ΔS.sub.M| under a field change of 0-1.0 T (open symbols) and 0-2.0 T (filled symbols) for series A; (b) Temperature dependence of ΔT.sub.ad under a field change of 0-1.0 T (open symbols) and 0-1.5 T (filled symbols) for series A; (c) Temperature dependence of |ΔS.sub.M| under a field change of 0-1.0 T (open symbols) and 0-2.0 T (filled symbols) for series B; (d) Temperature dependence of ΔT.sub.ad under a field change of 01.0 T (open symbols) and 0-1.5 T (filled symbols) for series B; (e) Partial temperature dependence of ΔT.sub.ad under a field change of 0-1.0 T during heating (H) and cooling (C) for series A; (f) Partial temperature dependence of ΔT.sub.ad under a field change of 0-1.0 T during heating and cooling for series B;

[0067] FIG. 9: Field dependence of T.sub.C and dT.sub.C/dB (insets) for series A (a) and series B (b); (c) The magnetization as a function of the V content for series A measured at a temperature of 5 K. The insets are the magnetic moment per formula unit (μ.sub.f.u.) dependence of the V content for series B;

[0068] FIG. 10: (a) Latent heat under a magnetic field of 1 T and (b) magnetizations as a function of temperature for (Mn.sub.0.6-yFe.sub.0.4-w).sub.1.90V.sub.0.02P.sub.0.5Si.sub.0.5 (y+w=0.02) (1#-4#) alloys; (c) magnetizations as a function of the external magnetic field and (d) magnetizations as a function of temperature for Mn.sub.1.17Fe.sub.0.71V.sub.0.02P.sub.0.5Si.sub.0.5 (2#);

[0069] FIG. 11: The values of lattice parameters a and c (a), the fraction of impurity (b), c/a and T.sub.C (c), the volume of the crystal unit cell (d) for the (Mn.sub.0.6-yFe.sub.0.4-w).sub.1.90V.sub.0.02P.sub.0.5Si.sub.0.5 (1#-4#) alloys. (e) The in-situ lattice parameter dependence of temperature for the sample of 2#. (f) Evolution of the (c/a) ratio of the cell parameters as a function of the temperature for 2#. The data are normalized in respect to the value at the transition temperature T.sub.C. The measurements were performed upon warming. SN indicates: sample number;

[0070] FIG. 12: Temperature dependence of |ΔS.sub.M| (a) and temperature dependence of ΔT.sub.ad (b) for a field change of 1 T calculated from in field DSC measurement for the (Mn.sub.0.6-yFe.sub.0.4-w).sub.1.90V.sub.0.02P.sub.0.5Si.sub.0.5 (1#-4#) alloys. (c) and (d) shows their field dependence of |ΔS.sub.M| and ΔT.sub.ad, respectively. (e) shows their temperature dependence of ΔT.sub.cyclic and (f) gives the temperature dependence of ΔT.sub.cyclic of 2# and Gd under different external magnetic field (which are 0.68, 1.00, 1.25, 0.65, and 1.0 Tesla, respectively);

[0071] FIG. 13: The DSC curves of (Mn.sub.0.6-yFe.sub.0.4-w).sub.1.90V.sub.0.02P.sub.0.5Si.sub.0.5 (y=0.00, w=0.02) under a magnetic field of 0 and 1T during heating (H) and cooling (C);

[0072] FIG. 14: The ΔT.sub.ad of (Mn.sub.0.6-yFe.sub.0.4-w).sub.1.90V.sub.0.02P.sub.0.5Si.sub.0.5 (y=0.00, w=0.02) under different applied magnetic field. The extrapolated value of ΔT.sub.ad under 1.93 T is 5.6 K;

[0073] FIG. 15: Magnetization as a function of temperature for Mn.sub.1.17Fe.sub.0.72-xV.sub.xP.sub.0.5Si.sub.0.5 alloys;

[0074] FIG. 16: Magnetization as a function of temperature for Mn.sub.1.17Fe.sub.0.72-xV.sub.xP.sub.0.5Si.sub.0.5 alloys annealed at 1343 and 1373 K;

[0075] FIG. 17: The values of lattice parameters (LP) a and c (a), c/a and dM/dT (b) (V % indicates V content (at %)); the fraction of impurity (I) and the volume (V) of the crystal unit cell (c) for Mn.sub.1.17Fe.sub.0.72-xV.sub.xP.sub.0.5Si.sub.0.5 alloys; IV indicates (IV: impurity volume (vol. %));

[0076] FIG. 18: Temperature dependence of |ΔS.sub.M| for a magnetic field change of 1 T calculated from in field DSC measurement for Mn.sub.1.17Fe.sub.0.72-xV.sub.xP.sub.0.5Si.sub.0.5 alloys; herein H indicates heating and C indicates cooling;

[0077] FIG. 19: Temperature dependence of ΔT.sub.ad for a magnetic field change of 1 T calculated from in field DSC measurement for Mn.sub.1.17Fe.sub.0.72-xV.sub.xP.sub.0.5Si.sub.0.5 alloys; herein H indicates heating and C indicates cooling;

[0078] FIG. 20: Magnetic field dependence of ΔT.sub.ad for magnetic field changes of 0-0.25 up to 0-1.5 T calculated from in field DSC measurement for Mn.sub.1.17Fe.sub.0.72-xV.sub.xP.sub.0.5Si.sub.0.5 alloys;

[0079] FIG. 21: Magnetizations as a function of temperature for (Mn, Fe).sub.1.90V.sub.0.02(P, Si) alloys;

[0080] FIG. 22: Temperature dependence of ΔT.sub.ad for a magnetic field change of 1 T calculated from in field DSC measurement for (Mn, Fe).sub.1.90V.sub.0.02(P, Si) alloys;

[0081] FIG. 23: The DSC curves of Mn.sub.1.14Fe.sub.0.74V.sub.0.02P.sub.0.49Si.sub.0.51 under a magnetic field of 0 and 1T during heating (H) and cooling (C);

[0082] FIG. 24: The ΔT.sub.ad of Mn.sub.1.14Fe.sub.0.74V.sub.0.02P.sub.0.49Si.sub.0.51 under different applied magnetic field. The extrapolated value of ΔT.sub.ad under 1.93 T is 4.5 K;

[0083] FIG. 25: Magnetizations as a function of temperature for (Mn, Fe).sub.1.90V.sub.0.02(P, Si) alloys prepared in the second series;

[0084] FIG. 26: Temperature dependence of ΔT.sub.ad for a magnetic field change of 1 T calculated from in field DSC measurement for (Mn, Fe).sub.1.90V.sub.0.02(P, Si) alloys prepared in the second series;

[0085] FIG. 27: Fraction of impurity (I (%) indicates impurity (vol %) for (Mn, Fe).sub.1.90V.sub.0.02(P, Si) alloys prepared in the first (1) and the second (2) series; SN indicates sample number;

[0086] FIG. 28: Magnetizations as a function of temperature for (Mn, Fe).sub.1.90V.sub.0.02(P, Si) alloys annealed at 1343 K;

[0087] FIG. 29: (a) Temperature dependence of ΔT.sub.ad for a magnetic field change of 1 T calculated from in field DSC measurement for (Mn, Fe).sub.1.90V.sub.0.02(P, Si) alloys annealed at 1343 K; herein H indicates heating and C indicates cooling; (b) The ΔT.sub.ad of Mn.sub.1.14Fe.sub.0.74V.sub.0.02P.sub.0.49Si.sub.0.51 under different applied magnetic field. The extrapolated value of ΔT.sub.ad under 1.93 T is 4.3 K;

[0088] FIG. 30: Fraction of impurity (I (%) indicates impurity (vol %) for (Mn, Fe).sub.1.90V.sub.0.02(P, Si) alloys annealed at 1343 K; SN indicates sample number;

[0089] FIG. 31: Magnetizations as a function of the applied magnetic field for (Mn, Fe).sub.1.90V.sub.0.02(P, Si) alloys annealed at 1343 K measured by the loop process; The schematic drawings are not necessarily to scale.

DETAILED DESCRIPTION OF THE EMBODIMENTS

[0090] Below, especially a combined effect of Annealing Temperature and Vanadium Substitution For Magnetocaloric Mn.sub.1.2-xV.sub.xFe.sub.0.75P.sub.0.5Si.sub.0.5 alloys is described.

[0091] Recently, near room temperature magnetic refrigeration technology has attracted broad attention due to its high efficiency, low impact on the environment, low noise, and long service life compared with the conventional vapor-compression technology. The giant magnetocaloric effect (GMCE) materials, which are utilized as refrigerant, form a key factor to determine the efficiency of this technology.

[0092] The magnetocaloric effect (MCE, from magnet and calorie) is a magneto-thermodynamic phenomenon in which an adiabatic temperature change or an isothermal entropy change of a magnetic material is caused by exposing the material to a changing magnetic field. The term giant magnetocaloric effect GMCE especially refers to materials that show enhanced temperature or entropy change in the vicinity of a magneto-structural or magneto-elastic phase-transition (see E. Bruck, Journal of Physics D, 2005, 38, pp R381). Such GMCE materials are particular suited for commercial applications as they strongly reduce the magnetic field strength that is required to operate a magnetocaloric device and thus reduces the investment costs connected to generating large magnetic fields.

[0093] Giant MCE may occur in some materials that undergo a first-order magnetic transition (FOMT), such as Gd.sub.5Ge.sub.2Si.sub.2, LaFe.sub.13-xSi.sub.x, MnFeP.sub.1-xAs.sub.x, MnFeP.sub.1-x-ySi.sub.xB.sub.y, MnCoGeB.sub.x and Heusler alloys. Among them, the MnFeP.sub.1-x-ySi.sub.xB.sub.y alloys are currently regarded as one of the most promising materials that can be industrialized as magnetic refrigerant because of their cheap and non-toxic elements, high cooling capacity and tunable T.sub.C near room temperature. However, thermal hysteresis (ΔT.sub.hys) in MnFeP.sub.1-x-ySi.sub.x alloys still limits their application since it lowers the efficiency of the cooling cycle. Lots of research has been done to reduce ΔT.sub.hys while maintaining the GMCE. In order to obtain a limited ΔT.sub.hys, the compositions can be tuned to shift the FOMT towards the border with a second order magnetic phase transition (SOMT), as demonstrated for the MnFeP.sub.1-x-ySi.sub.xB.sub.y or for the transition metal substitution in Mn.sub.1-yCo.sub.yFe.sub.0.95P.sub.0.50Si.sub.0.50 and MnFe.sub.0.95-xNi.sub.xP.sub.0.50Si.sub.0.50. Additionally, ΔT.sub.hys can also be controlled by the annealing time and temperature. For example, in Mn.sub.1.15Fe.sub.0.85P.sub.0.55Si.sub.0.45 alloys, ΔT.sub.hys decreases with the annealing temperature. The effect of the annealing temperature and time on the magnetic phase transition of Mn.sub.1.000Fe.sub.0.950P.sub.0.595Si.sub.0.330B.sub.0.075 alloys has been investigated and the annealing temperature was found to show a strong influence on ΔT.sub.hys. Mn.sub.1.2Fe.sub.0.75P.sub.0.5Si.sub.0.5 alloys annealed at 1373 K in a two-step heat treatment process was reported to have strong FOMT with a relative low ΔT.sub.hys of 5 K.

[0094] Sintering of MnFePSi alloys can be regarded as a solid state diffusion process as the annealing temperature is below the melting point (1553 K). The diffusion rate of each element strongly depends on the annealing temperature. Therefore, introducing extra elements in the MnFePSi alloy requires a different annealing temperature. Here we disclose the combined effect of a changing annealing temperature (1323, 1373 and 1423 K) and V substitution (x=0.00, 0.01, 0.02, 0.03, 0.04, 0.05) in Mn.sub.1.2-xV.sub.xFe.sub.0.75P.sub.0.5Si.sub.0.5 alloys, resulting in a change in aspect ratio at the hexagonal crystal structure and the magnetic properties. The substitution of Mn by V can be controlled by adjusting the annealing temperature in order to optimize the GMCE.

[0095] Below, the preparation of Mn.sub.1.2-xV.sub.xFe.sub.0.75P.sub.0.5Si.sub.0.5 alloys is described.

[0096] Polycrystalline Mn.sub.1.2-xV.sub.xFe.sub.0.75P.sub.0.5Si.sub.0.5 (x=0.00, 0.01, 0.02, 0.03, 0.04, 0.05) alloys were prepared by a powder metallurgy method. The starting materials Mn (99.7%), Fe (99.7%), red P (99%), Si (99.7%) and V (99.5%) powders were mechanically ball milled in a PULVERRISETTE 5 planetary mill for 10 h in an Ar atmosphere with a constant rotation speed of 380 rpm, then pressed into small tablets, and finally sealed in quartz ampoules under 200 μmbar of Ar. These tablets were then annealed at 1323, 1373 and 1423 K for 2 h in order to crystalize and slowly cooled down to room temperature. Subsequently, they were heated up to the same annealing temperature for 20 h to homogenize and quenched in water.

[0097] The X-ray diffraction (XRD) patterns were collected on a PANalytical X-pert Pro diffractometer with Cu-Kα radiation (1.54056 Å) at room temperature (RT). The room-temperature neutron diffraction data were collected on the neutron powder diffraction instrument PEARL at the research reactor of Delft University of Technology (see also L. van Eijck, L. D. Cussen, G. J. Sykora, E. M. Schooneveld, N.J. Rhodes, A. van Well, and C. Pappas, J. App. Crystallogr. 49, 1 (2016)). The crystal structures and atom occupancies were refined using the Rietveld refinement method implemented in the Fullprof software package. Differential scanning calorimetry (DSC) was carried out using a TA-Q2000 instrument at a rate of 10 K/min. The temperature and magnetic field dependence of the magnetization was measured by a superconducting quantum interference device (SQUID) magnetometer (Quantum Design MPMS 5XL) in the reciprocating sample option (RSO) mode. The adiabatic temperature change (ΔT.sub.ad) is measured in a Peltier cell based differential scanning calorimetry using a Halbach cylinder magnetic field (≤1.5 T). In this setup, the iso-field calorimetric scans were performed at a rate of 50 mK.Math.min.sup.−1, while the temperature has been corrected for the effect of the thermal resistance of the Peltier cells.

[0098] Below, the effect of annealing temperature and V substitution to Mn.sub.1.2xV.sub.xFe.sub.0.75P.sub.0.5Si.sub.0.5 alloys is described.

[0099] Magnetization as a function of temperature for Mn.sub.1.2-xV.sub.xFe.sub.0.75P.sub.0.5Si.sub.0.5 (x=0.00, 0.01, 0.02, 0.03, 0.04 and 0.05) alloys after annealing at 1323, 1373 and 1423 K are shown in FIG. 1. The values are extracted from iso-field measurements (decreasing from 2 to 0.2 T in steps of 0.2 T) to ensure that the virgin effect is removed. The ferromagnetic-to-paramagnetic transition temperature T.sub.C is determined by the corresponding maximum temperature of dM/dT in the curves. T.sub.C tends to decrease with increasing V substitution after annealing at 1323, 1373 and 1423K, as shown in the right bottom of FIG. 1. However, the decrease shows distinct features when the annealing temperature is changed. Except for the alloys annealed at 1323K, T.sub.C decreases linearly when annealed at 1373 and 1423 K. Since T.sub.C is relevant to the internal structure changes or the internal symmetry changes. These changes are in a good agreement with the trends for the c a ratio in the refined lattice parameters (see FIG. 2(d)).

[0100] ΔT.sub.hys is defined as the hysteresis during the heating and cooling process, which will hinder the efficiency of the magnetic cooling device. It is important to minimize ΔT.sub.hys while maintaining a sufficient MCE. In this work, ΔT.sub.hys is determined by the difference in the transition temperature during heating and cooling in a field of 1 T. The transition temperature is defined as the extreme value of |dM/dT| versus Tin the heating or cooling process, as shown in FIG. 1. The values of T.sub.C, ΔT.sub.hys and Latent heat (L) for Mn.sub.1.2-xV.sub.xFe.sub.0.75P.sub.0.5Si.sub.0.5 (x=0.00, 0.01, 0.02, 0.03, 0.04, 0.05) alloys after annealing at 1323, 1373 and 1423 K are shown in table 1. Since materials with a pronounced FOMT usually show large L values, the values of L can be regarded as a sign of the strength of the FOMT. In general, V substitutions of Mn can reduce both ΔT.sub.hys and L. When x increases from 0.00 to 0.05, ΔT.sub.hys decreases dramatically from 12.8 K to 1.4 K when annealing at 1423 K, while it decreases from 2.1 K to below experimental resolution when annealing at 1323 K. Note that the limited ΔT.sub.hys for the Mn.sub.1.2-xV.sub.xFe.sub.0.75P.sub.0.5Si.sub.0.5 alloys annealed at 1323 K is promising for practical applications. The ΔT.sub.hys and the L values for the alloy with x=0.02 are somewhat larger than that with x=0.01 for annealing at 1323 and 1373 K, which suggest a stronger first-order transition. As shown in table 2, the increase in occupation of Fe on the 3f site enhances the FOMT.

TABLE-US-00001 TABLE 1 The values of T.sub.C, ΔT.sub.hys and the Latent heat (L) for Mn.sub.1.2−xV.sub.xFe.sub.0.75P.sub.0.5Si.sub.0.5 (x = 0.00, 0.01, 0.02, 0.03, 0.04, 0.05) alloys after annealing at 1323, 1373 and 1423K, respectively. Annealed Annealed at Annealed at at 1423K 1373K 1323K T.sub.C ΔT.sub.hys L T.sub.C ΔT.sub.hys L T.sub.C ΔT.sub.hys L x (K) (K) (kJ/kg) (K) (K) (kJ/kg) (K) (K) (kJ/kg) 0.00 256.4 12.8 7.6 276.8 4.5 8.0 281.2 2.1 6.2 0.01 250.5 10.7 7.1 265.7 3.5 7.6 270.6 1.3 4.8 0.02 236.4 9.1 5.9 265.1 4.7 8.4 260.1 1.8 4.2 0.03 230.4 5.4 5.6 248.2 3.7 6.3 251.5 1.3 3.9 0.04 215.3 3.8 4.5 246.7 / 5.5 234.9 1 3.3 0.05 212.5 1.4 3.5 238.4 / 4.9 213.5 0 0.04

[0101] A Rietveld refinement of the room temperature XRD data shows that, in the Mn.sub.1.2-xV.sub.xFe.sub.0.75P.sub.0.5Si.sub.0.5 alloys, the hexagonal Fe.sub.2P-type lattice structure (space group P-62m) phase corresponds to the main phase and a MnFe.sub.2Si-type lattice structure(space group Fm3m) is found as impurity phase. The phase fraction of impurities in each annealing temperature (see FIG. 2) is roughly at the same level for x≤0.04, which allows for independent comparison of the effects of V substitutions on the alloys annealed at the same annealing temperature. For the alloys with x≤0.03 annealing at 1323 and 1373 K, the impurity phase fraction is around 8.0±1.0 volume percentage (vol. %). But the impurity increases to around 11.5±0.5 vol. % when the annealing temperature rises to 1423 K. These results indicate that a large impurity phase fraction will be introduced at a higher annealing temperature.

[0102] Based on the crystal structure refinement results (shown in FIG. 2), the trends as a function of the V substitution concentration in lattice parameter change are similar for all the three annealing temperatures: the a axis decreases while the c axis increases, leading to an increase in the c a ratio. The size of the change varies with the annealing temperature. For x=0.05, the change in c a ratio is 1.0%, 0.5%, 0.4% at an annealing temperature of 1323, 1373 and 1423 K, respectively. There is a smaller change at higher annealing temperatures, which may be caused by loss of one component of the alloy either segregating into the inter-grain secondary phase or evaporation.

[0103] Below, the Room temperature neutron diffraction and atom site occupancy change of Mn.sub.1.2-xV.sub.xFe.sub.0.75P.sub.0.5Si.sub.0.5 alloys is described.

[0104] For the Mn—Fe—P—Si alloy, it is reported that the Fe atoms mainly occupy the 3f site, the Mn atoms the 3g site, the P atoms and Si atoms the 2c or 1b sites and the Si atoms have a high preference in the 2c site. X-ray absorption and powder diffraction experiments combined with density functional theory (DFT) calculations revealed that an electronic redistribution takes place in Mn—Fe—P—Si—B which is the origin of the giant entropy change and results in a large change in the electron density for the Fe and the surrounding Si/P atoms. The previous first-principles calculation results suggest that larger magnetic moments will develop on the 3f and 3g site when there are more coplanar Si nearest neighbors. Consequently, the Si atoms on the 2c site may also contribute to strengthen the magnetic moments. Thus, it suggests that the 3f site is highly affected by the ferromagnetic transition. In order to investigate the relationship between the site occupancies and the magneto-elastic phase transition, it is significant to investigate both the atom positions and the site occupation in the Fe.sub.2P-type structure.

[0105] FIG. 3 (a) shows the neutron diffraction pattern and the refinement result of the Mn.sub.1.18V.sub.0.02Fe.sub.0.75P.sub.0.5Si.sub.0.5 alloy annealed at 1373 K, indicating that the calculation is consistent with the experimental result. Note that V can hardly be detected by neutron diffraction as the sample holder is made from V. The V scatters incoherently and thereby contributes mainly to the background. Therefore, the site occupation of V in the Fe.sub.2P-type structure is not refined here. According to the refinement of the neutron diffraction patterns, the higher annealing temperature results in a higher occupancy of the Fe atoms on the 3f site and Si atoms on the 2c site (see table 2). Therefore, this increase can illustrate why the higher annealing temperature leads to a stronger first-order magneto-elastic transition with higher |ΔS.sub.M| values for a field change of 2 T, as shown in FIG. 5. For the alloys annealed at 1373 K, the sample with x=0.02 has a higher |ΔS.sub.M| value for a field change of 1 T than the sample with x=0 (see FIG. 4(b)). This is probably due to its slightly higher Fe occupation on 3f site and the Si atoms on the 2c site (shown in table 2).

[0106] As mentioned above, that will enhance the FOMT.

[0107] FIGS. 3 (b) and 3 (c) illustrate the interatomic distance as a function of annealing temperature T.sub.a (K) for Mn.sub.1.2Fe.sub.0.75P.sub.0.5Si.sub.0.5 alloys, amongst others Mn.sub.1.18V.sub.0.02Fe.sub.0.75P.sub.0.5Si.sub.0.5 annealed at 1373 K. Note that the FOMT becomes stronger with increasing annealing temperature. In the Fe.sub.2P-type structure, Mn/Fe (3f)-P/Si (2c) hybridizes in the same plane while Mn (3g)-P/Si (1b) is in the other plane. According to the previous X-ray magnetic circular dichroism experiments, a similar moment evolution was observed in both Mn and Fe, suggesting that the origin of GMCE might come from both Mn and Fe layer. Consequently, the mean distance of the Mn/Fe (3f)-P/Si (2c) and the Mn (3g)-P/Si (1b) intra layer will strongly affect the hybridization between the metallic and non-metallic elements. For the Mn.sub.1.2Fe.sub.0.75P.sub.0.5Si.sub.0.5 alloy with similar amount of impurity annealed at 1323 and 1373 K, the mean distance of the intra layer Mn/Fe (3f)-P/Si (2c) and Mn (3g)-P/Si (1b) decreases with increasing annealing temperature and therefore increases the GMCE. Compared to the alloy without V annealed at 1373 K, the Mn.sub.1.18V.sub.0.02Fe.sub.0.75P.sub.0.5Si.sub.0.5 annealed at 1373 K, which has larger GMEC, also has smaller mean distance of the intra layer Mn/Fe (3f)-P/Si (2c) and Mn (3g)-P/Si (1b). However, for the Mn.sub.1.2Fe.sub.0.75P.sub.0.5Si.sub.0.5 alloy annealed at 1423 K with the largest GMCE, the impurity is higher than other three samples, suggesting that it has lower Si content in the Fe.sub.2P-type phase. Thus, the interatomic distance is not comparable with other samples. But it should be note that its intra layer distance Mn/Fe (3f)-Mn/Fe (3f) is the lowest among these samples. In conclusion, the changing of the GMCE strength induced by the annealing temperature is the result of both the different occupation on 3f site and 2c site and the varying interatomic distances.

[0108] FIG. 3 (d) shows on the x-axis also the annealing temperature Ta, and on the left y-axis a (Å) and on the right axis c (Å). The a value decreases with annealing temperature; the c value increases with annealing temperature.

TABLE-US-00002 TABLE 2 The site occupation of the 3f, 3g, and 2c sites for the Mn.sub.1.2Fe.sub.0.75 P.sub.0.5Si.sub.0.5 alloys annealed at 1323, 1373 and 1423K and the Mn.sub.1.18V.sub.0.02Fe.sub.0.75P.sub.0.5 Si.sub.0.5 alloy annealed at 1373K. Space group: P-62 m. Atomic positions : 3f(x.sub.1, 0,0), 3g (x.sub.2, 0, 1/2), 2c (1/3, 2/3, 0), and 1b (0, 0, 1/2). Site Parameters x = 0.00, 1323K x = 0.00, 1373K x = 0.00, 1423K x = 0.02, 1373K a     6.107(4)     6.098(2)     6.083(0)     6.093(1) c     3.427(7)     3.442(4)     3.460(6)     3.448(8) V(Å)   110.72(7)   110.86(2)    110.899(1)   110.88(7) 3f x1    0.25401(4)    0.25594(5)    0.25443(5)    0.25591(4) n(Fe)/n(Mn) 0.197/0.053(4) 0.200/0.050(1) 0.199/0.051(3) 0.206/0.044(3) 3g x2    0.59250(7)    0.59145(9)    0.59179(0)    0.59179(8) n(Mn)/n(Fe) 0.249/0.000(7) 0.247/0.003(1) 0.248/0.002(3) 0.248/0.002(3) 2c n(P)/n(Si) 0.146/0.020(3) 0.119/0.047(2) 0.114/0.052(9) 0.099/0.067(1) 1b n(P)/n(Si) 0.080/0.003(1) 0.068/0.015(1) 0.080/0.003(1) 0.062/0.021(4) Rp(%) 6.18 8.9 7.77 6.92 wRp(%) 8.5 10.9 11 8.98 χ.sup.2 6.96 10.2 13.4 5.06

[0109] Below, the Magnetocaloric effect and magneto-elastic phase transition of Mn.sub.1.2-xV.sub.xFe.sub.0.75P.sub.0.5Si.sub.0.5 alloys is described.

[0110] The iso-field magnetization curves (not shown here) of annealed Mn.sub.1.2-xV.sub.xFe.sub.0.75P.sub.0.5Si.sub.0.5 (x=0.00, 0.01, 0.02, 0.03, 0.04, 0.05) for a magnetic field change of 0-2 T are measured in the vicinity of T.sub.C at temperature intervals of 1 K. The |ΔS.sub.M| values of the alloys are derived from extracted isothermal magnetization curves based on the Maxwell relation. Temperature-dependence of |ΔS.sub.M| for a field change of 0-1 T (open symbols) and 0-2 T (solid symbols) for Mn.sub.1.2-xV.sub.xFe.sub.0.75P.sub.0.5Si.sub.0.5 (x=0.00, 0.01, 0.02, 0.03, 0.04, and 0.05) alloys after annealing at 1323, 1373 and 1423 K are shown in FIGS. 4 (a), (b) and (c), respectively. With increasing annealing temperatures, |ΔS.sub.M| increases and T.sub.C decreases, which agrees with the previous reported effect of annealing temperature for MnFe.sub.0.95P.sub.0.595Si.sub.0.33B.sub.0.075 alloys. On the other hand, for increasing V substitutions, |ΔS.sub.M| decreases and T.sub.C decreases. The alloy with x=0.02 annealed at 1373 K even has a larger |ΔS.sub.M| value (18.4 J/(kg K)) than that with x=0.00 (17.2 J/(kg K)) under an external field of 1 T. But when the external field is at a field change of 0-2 T, these two samples have equal values of |ΔS.sub.M|. This indicates that the alloy with 0.02 at % has better low-field (1 T) performance, which is attributed to high Fe occupancy in the 3f site and Si occupancy on the 2c site. Since the magnetic field we apply in current heat pump prototypes now is around 1 T with low-cost NdFeB permanent magnets, it is very significant to have high performance under this field. The current alloys with x=0.00 annealed at 1323 K (|ΔS.sub.M|=8.2 J/(kgK) at 282 K for a field change of 0-1 T with ΔT.sub.hys=2.1 K) is comparable to the Boron doping alloys such as the MnFe.sub.0.95P.sub.0.595Si.sub.0.33B.sub.0.075 alloys annealed at 1323 K (|ΔS.sub.M|=6.2 J/(kgK) at 285 K for a field change of 0-1 T) and the MnFe.sub.0.95P.sub.0.593Si.sub.0.33B.sub.0.077 alloys annealed at 1373K (|ΔS.sub.M|=9.8 J/(kg K) at 281 K with ΔT.sub.hys=1.6 K). These results suggest that a decreasing annealing temperature can tune the strong first-order magnetic transition to the boundary between the first-order to second-order magnetic transition in the Mn.sub.1.2Fe.sub.0.75P.sub.0.5Si.sub.0.5 alloys.

[0111] FIG. 5 (a) illustrates the temperature dependence of DSC in-field ΔT.sub.ad for several Mn.sub.1.2-xV.sub.xFe.sub.0.75P.sub.0.5Si.sub.0.5 alloys annealed at 1323 K while FIG. 5 (b) illustrates the temperature dependence of ΔT.sub.ad for Mn.sub.1.2-xV.sub.xFe.sub.0.75P.sub.0.5Si.sub.0.5 alloys annealed at 1373 K. ΔT.sub.ad is determined by using the following equation:

[00001]$\begin{array}{cc}\Delta T_{\mathrm{ad}}=\frac{T}{\mathrm{Cp}\left(H\right)}{\Delta S}_M\left(H\right)& \left(4.1\right)\end{array}$

where C.sub.p(H) is the specific heat. Note that there are two peaks in the vicinity of T.sub.C for the sample x=0.00. It is reasonable as two different Fe.sub.2P-type phases with close compositions have been reported to co-exist if annealing is preferred at relative lower temperatures. When x increases from 0.00 to 0.02 for the sample annealed at 1323 K, the values of ΔT.sub.ad increases from 1.8 to 2.7 K and |ΔS.sub.M| decrease from 8.2 to 7.6 Jkg.sup.−1K.sup.−1 under an external field change of 1 T. Compared to the alloy without V, a significant ΔT.sub.ad of 2.7 K for a field change of 1 T and a limited hysteresis (1.8 K) are achieved in the alloy with x=0.02 annealed at 1323 K, indicating that it is a promising candidate for magnetic heat-pumping.

[0112] For the sample annealed at 1373 K, the values of ΔT.sub.ad increases from 3.3 to 4.8 K for an external field change of 1 T by increasing x from 0.00 to 0.02. The intermediate hysteresis in these samples is about 4.5 K. It is important to distinguish the value of ΔTada in this work from the Cyclic (direct) field-induced temperature changes (ΔT.sub.cyclic) in first order materials showing a large hysteresis. ΔT.sub.cyclic reflects the practical working situation of the magnetic refrigeration while the ΔT.sub.ad is more reflecting the potential. Therefore, for the materials with a large hysteresis, ΔT.sub.ad turns out to be much higher than ΔT.sub.cyclic. Thus, it is concluded that V substitution can increase ΔT.sub.ad when annealed at 1323 and 1373 K.

[0113] The combined influence of V substitution for Mn and a variation of the annealing temperature is investigated in the Mn.sub.1.2-xV.sub.xFe.sub.0.75P.sub.0.5Si.sub.0.5 alloys. Increasing the V content results in a decrease in the a-axis and increase on the c-axis, which leads to a decrease in T.sub.C. The occupancy of Fe atoms on the 3f site and the Si atoms on the 2c site are enhanced when the annealing temperature and/or the V content increases, which will result in a higher |ΔS.sub.M|. Decreasing the mean distance of the intra layer Mn/Fe (3f)-P/Si (2c) and Mn (3g)-P/Si (1b) also contributes to an increase on |ΔS.sub.M|. The alloy with x=0.02 annealed at both 1323 and 1373 K has a larger |ΔS.sub.M| value than the alloy with x=0.00 for a field change of 0-1 T while its value is equal for a field change of 0-2 T, indicating that the alloy with x=0.02 has better low-field performance in a field change of 1 T. This competitive low-field performance promotes the application of low-cost NdFeB permanent magnets or even the ferrite permanent magnets, which will help development of a low-field prototype. Compared to a V free alloy, a larger temperature change ΔT.sub.ad of 2.7 K and less hysteresis of 1.8 K are achieved by optimizing the alloy with x=0.02 annealed at 1323 K, which is comparable to the MnFe.sub.0.95P.sub.0.595Si.sub.0.33B.sub.0.075 alloy. Mn.sub.1.2-xV.sub.xFe.sub.0.75P.sub.0.5Si.sub.0.5 alloys can therefore form a promising alternative for magnetic refrigeration near room temperature.

[0114] Below Ultra-low Hysteresis and Giant Magnetocaloric Effect near the critical Point of First to Second order Phase Transition in Mn1-xVxFe(P,Si,B) Alloys is described.

[0115] Thermal hysteresis (ΔT.sub.hys) is an important issue that limits the real application of the GMCE in these FOMT materials. The discontinuous nature of the transition is the feature that provides the GMCE. Therefore, in the premise of keeping the GMCE, the thermal hysteresis should be made as narrow as possible by manipulating the microstructure or by tuning the composition. Through 0.075 at. % of B substitution in the MnFeP.sub.1-x-ySi.sub.xB.sub.y alloys, the optimized ΔT.sub.hys can be decreased to 1.6 K according to temperature-dependent magnetization curves at a magnetic field of 1 T and ΔT.sub.hys is 2.0 K according to in-field DSC measurements at a magnetic field of 1 T (see the supporting information of ref F. Guillou, G. Porca'ri, H. Yibole, N. H. van Dijk, and E. Bruck. Taming the First-Order Transition in Giant Magnetocaloric Materials. Advanced Materials, 17 (2014) 2671-2675), while maintaining a GMCE. In this case, the material can be cycled for 10 thousand times and the sample geometry remains intact. A higher level of B substitution can decrease the ΔT.sub.hys further, but may fail to provide a sufficiently large GMCE. It is desirable to find a new approach to further decrease the ΔT.sub.hys and simultaneously provide a large GMCE. One of the design criteria is that the adiabatic temperature change (ΔT.sub.ad) should especially be larger than 2 K, since cooling may be ineffective when ΔT.sub.ad drops below 2 K. In this work, through V substitution, an ultra-low ΔT.sub.hys (0.7 K) and a GMEC of ΔT.sub.ad (2.3 K) at a magnetic field of 1 T is achieved simultaneously.

[0116] The crystal structure of MnFeP.sub.1-x-ySi.sub.xB.sub.y shows a significant change in lattice parameters across the magnetic phase transition, while it keeps its hexagonal structure (magneto-elastic transition). Applying a magnetic field results in a shift of the transition temperature (T.sub.c) to higher temperatures. The shift of T.sub.c induced by magnetic fields, defined as dT.sub.c/dB, is positive for a conventional first-order magnetic transition materials such as MnFeP.sub.1-x-ySi.sub.xB.sub.y and La—Fe—Si, while it is negative for the inverse first-order magnetic transition materials, for instance the Ni—Mn—X-Heusler alloys with X=Sn, Sb and In or Fe—Rh. For the conventional first-order magnetic transition materials, this shift is attributed to the magnetic field stabilization of the phase with the higher magnetization, being the low-temperature ferromagnetic phase. In a magnetic field thermal energy is then needed to induce the magnetic phase transition. If the value of dT.sub.c/dB is enhanced, the magnetic phase transition can be induced in lower magnetic field. As a consequence, low-field permanent magnets could be utilized, which would significantly reduce the costs of commercial applications. The magnetic field currently used in the commercial prototypes is generated by NdFeB permanent magnets with external magnetic fields varying from a 0.9 to 1.5 T. The materials cost to reach a field of 1.5 T may be 10 times higher than the costs to reach a field of 0.9 T. It is therefore of interest to explore the lower field potential of this GMCE system by studying dT.sub.c/dB. In this work, we investigated the effect of V substitution on the ΔT.sub.hys, dT.sub.c/dB, the lattice parameters and the magnetic properties in polycrystalline Mn—V—Fe—P—Si—B alloys.

[0117] Below, the preparation of Mn1-xVxFe(P,Si,B) alloys is described.

[0118] Polycrystalline Mn.sub.1-xV.sub.xFe.sub.0.95P.sub.0.593Si.sub.0.33B.sub.0.077 (x=0.00, 0.01, 0.02, 0.03) alloys were prepared by a powder metallurgy method. The starting materials in the form of Mn, Fe, red P, Si, B, and V powders were mechanically ball milled for 10 h in an Ar atmosphere with a constant rotation speed of 380 rpm, then pressed into small tablets, and finally sealed in quartz ampoules under 200 μmbar of Ar before employing the various heat treatment conditions. These tablets were annealed at 1323 K for 2 h in order to crystalize and slowly cooled down to room temperature. Then they were heated up to the same annealing temperature for 20 h to homogenize the alloy and finally quenched in water. This batch samples is regarded as series A. In order to tune the T.sub.C to room temperature for the sample with V, the Mn.sub.1-xV.sub.xFe.sub.0.95P.sub.0.563Si.sub.0.36B.sub.0.077 (x=0.00, 0.01, 0.02, 0.03) alloys with a higher Si content were prepared with the same procedure as series A, except for a higher annealing temperature of 1373 K. This batch samples is regarded as series B.

[0119] The X-ray diffraction (XRD) patterns were collected on a PANalytical X-pert Pro diffractometer with Cu-Kα radiation (1.54056 Å) at room temperature. The temperature and magnetic field dependence of the magnetization was measured with a commercial superconducting quantum interference device (SQUID) magnetometer (Quantum Design MPMS 5XL) in the reciprocating sample option (RSO) mode. The adiabatic temperature change (ΔT.sub.ad) is measured in a Peltier cell based differential scanning calorimetry using a Halbach cylinder providing a magnetic field of 1.5 T. In this setup, the iso-field calorimetric scans were performed at a slow rate of 50 μmKmin.sup.−1 in order to probe the equilibrium state, while the temperature has been corrected for the effect of the thermal resistance of the Peltier cells.

[0120] Below, the characterization of crystal structure of Mn1-xVxFe(P,Si,B) alloys is described.

[0121] In FIGS. 6a-6d the XRD patterns for series A (a and b) and series B (c and d) are illustrated. For the Mn.sub.1-xV.sub.xFe.sub.0.95P.sub.0.563Si.sub.0.36B.sub.0.077 (x=0.00, 0.01) alloys in series B, as T.sub.C is higher than room temperature, the XRD patterns are measured at 323 K, where they are in the paramagnetic state. Other samples are measure at room temperature since their T.sub.C values are below room temperature. At the selected temperatures, all the samples are measured at paramagnetic state. The hexagonal Fe.sub.2P-type (space group P-62m) phase is identified as the main phase in all these alloys and the cubic MnFe.sub.2Si-type phase (space group Fm3m) is identified as the impurity phase. Based on the refinement results, the estimated fraction of the impurity phase is 1.6-2.4 vol. % in series A and 3.7-4.5 vol. % in the series B, respectively (see FIG. 6e). The amount of impurity phase is decreases by V substitution for series B. Above a difference in annealing temperature was found to result in a variation in the site occupancy and atom position. The lattice parameter in series A and series B shows a different behavior. For series A, an increase in V substitution leads to a decrease in the a axis and an increase in the c axis. The c/a ratio increases, while T.sub.C decreases for an increasing V substitution. Note that, the unit cell volume of the crystal remains unchanged for x=0.01 and 0.02. Only when the V content reaches x=0.03, the volume drops by 0.7% compared to x=0.00. For series B, the lattice parameters show a different trend. Oppositely, an increasing V substitution leads to an increase in the a axis, while the c axis decreases for x=0.00, 0.01 and 0.02. The evolution of the unit cell volume for series B was found to differ from series A, as the unit cell volume slightly increases for x=0.02 and 0.03, but still is smaller than x=0.00. Since the covalent radius of V (132±5 pm) is slightly smaller than that of Mn (139±5 pm), a decrease in the unit cell volume may be a sign of the substitution of Mn by V in the Fe2P-type structure. The temperature in the drawings indicate the annealing temperature at 1323 K (FIGS. 6a-6b), at 1373 K (FIGS. 6c-6d), and at 1323 or 1373 K (in both FIGS. 6e-6f).

[0122] Below, the magnetocaloric Effect of Mn1-xVxFe(P,Si,B) alloys is described.

[0123] Temperature dependence of the magnetization in series A and B are shown in FIGS. 7 (a) and (b), respectively. The temperature dependence of −dM/dT is also shown in the corresponding insets. Generally, the maximum of −dM/dT is regarded an indication of the strength for FOMT. The maximum of −dM/dT in our materials decreases for an increasing V content except for the sample with x=0.02, indicating it moves closer to SOMT. The transition temperature T.sub.C is determined from the maximum value of the −dM/dT in the M-T curve during heating. For series A, T.sub.C tends to decrease with increasing V substitution. Moreover, the reduction of T.sub.C becomes weaker with increasing V content, as shown in table 3. It reduces from about 18.1, 15.3 and 12.7 K from x=0.00 to 0.03 in steps of 0.01 at. % V. For series B, T.sub.C first increases at x=0.01 and then decreases with increasing V substitution.

[0124] The DSC patterns for series A and B are measured (not shown here), and the derived latent heat is listed in Table 3. It was earlier found that the alloy with x=0 is already at the border of the FOMT to the second order magnetic transition (SOMT). Increasing the V substitution from 0.00 to 0.03 results in a strong reduction of the latent heat by 67% from 5.2 to 1.7 J/g for the alloys annealed at 1323 K and by 55% from 6.2 to 2.8 J/g for the alloys annealed at 1373 K (listed in table 3), indicating that the samples transfer more towards the SOMT. As mentioned above, the reduction in latent heat mainly contributes to the increase in dT.sub.C/dB. Additionally, smaller latent heat will result in a smaller thermal hysteresis.

TABLE-US-00003 TABLE 3 The Curie temperature (T.sub.C), thermal hysteresis (ΔT.sub.hys-MT), latent heat (L), magnetic entropy change (|ΔS.sub.M|) and adiabatic temperature change ΔT.sub.ad at a field change of 1 T for series A and B. Annealed T T.sub.C ΔT.sub.hys-MT L |ΔS.sub.M| ΔT.sub.ad (K) Sample (K) (K) (kJ/kg) (J/(kg .Math. K)) (K) series A x = 0.00 290.0 1.1 5.2 6.5 2.7 series A x = 0.01 270.4 0.8 3.4 3.3 / series A x = 0.02 255.2 0.9 2.4 4.6 1.6 series A x = 0.03 242.5 0.7 1.7 2.7 / series B x = 0.00 300.2 1.5 6.2 11.3 3.5 series B x = 0.01 310.2 0.8 2.5 4.8 1.8 series B x = 0.02 286.2 0.5 3.7 5.6 2.3 series B x = 0.03 264.2 0.1 2.8 4.8 1.6 1373* x = 0.00 281 1.6 3.8 9.8 2.5 *The sample is Mn.sub.1Fe.sub.0.95P.sub.0.593Si.sub.0.33B.sub.0.077 alloy annealed at 1373K in two-step heat treatment.

[0125] A large ΔT.sub.hys is usually accompanied with a strong FOMT in the materials families of Gd.sub.5(Si,Ge).sub.4, La(Fe,Si).sub.13, and Heuslers NiMn(In,Ga,Sn) and (Mn,Fe).sub.2(P,Si,B) alloys. Even though they have a giant MCE, the large ΔT.sub.hys limits their application in real devices since it will lower the heat exchanging efficiency dramatically. Materials optimized to be near the critical point between a first and second order transition are promising candidates for applications as they combine a low thermal hysteresis with a considerable GMCE. Here, we find that ΔT.sub.hys can be reduced further by substituting Mn by V in (Mn,Fe).sub.2(P,Si,B) alloys. ΔT.sub.hys-MT is determined by calculating the difference in the maximum value of −dM/dT during cooling and heating in an applied magnetic field of μ.sub.0H=1 T. For series A, ΔT.sub.hys-MT decreases by 36% from 1.1 to 0.7 K when x increases from 0.00 to 0.03. For series B, ΔT.sub.hys-MT decreases by 93% from 1.5 to 0.1 K when x increases from 0.00 to 0.03. The thermal hysteresis decreases with increasing V substitution, which tunes the series A and B alloys towards a second order magnetic transition which makes these materials more suitable for commercialization of magnetic refrigerators.

[0126] The iso-field magnetization curves (not shown here) of series A and B for a magnetic field change of 0-2 T are measured in the vicinity of T.sub.C with a temperature interval of 1 K. The values of |ΔS.sub.M| for the alloys is derived from extracted isothermal magnetization curves using the Maxwell relation. The temperature dependence of |ΔS.sub.M| for series A and B are shown in FIGS. 8 (a) and (c), respectively. |ΔS.sub.M| decreases with increasing V substitution. However, the alloy with x=0.02 in series A has a higher |ΔS.sub.M| value even though it has a lower latent heat. In series A, the MCE (|ΔS.sub.M|=6.5 J/(kgK) at 289 K under a field change of 0-1 T with ΔT.sub.hys=1.1 K) of the alloy with x=0.00 is comparable to a previously studied one prepared by a second step annealing method (|ΔS.sub.M|=9.2 J/(kgK) at 279.1 K under a field change of 0-1 T with ΔT.sub.hys=1.6 K).

[0127] FIG. 8 (b) illustrates the temperature dependence of in-field DSC values of ΔT.sub.ad for a partial series A (x=0.00 and 0.02), while FIG. 8 (d) illustrates the temperature dependence of ΔT.sub.ad for series A (x=0.00, 0.01, 0.02 and 0.03). When x increases from 0.00 to 0.02 in series A, the value of ΔT.sub.ad decreases from 2.7 to 1.6 K under a field change of 1 T. When x increases from 0.00 to 0.02 in series B, the values of ΔT.sub.ad decreases from 3.5 to 2.3 K under afield change of 1 T. Note that, in series B, the value of ΔT.sub.hys-DSC, determined by the difference of the heating and cooling process of in-field DSC under a field change of 1 T, decreases from 2.4 to 0.7 K when x increases from 0.00 to 0.02. The value of ΔT.sub.ad for Mn.sub.0.98V.sub.0.02Fe.sub.0.95P.sub.0.563Si.sub.0.36B.sub.0.077 (ΔT.sub.ad=2.3 K) in series B is competitive to the MnFe.sub.0.95P.sub.0.563Si.sub.0.36B.sub.0.077 alloys (ΔT.sub.ad=2.5 K), but its value of ΔT.sub.hys-DSC is reduced by 85%. It is clearly promising to achieve at the same time a giant value of ΔT.sub.ad and an extremely low ΔT.sub.hys-DSC, which can significantly improve the heat exchange efficiency of the magnetic cooling system.

[0128] Below, a mechanism of ultra-low hysteresis and giant magnetocaloric for Mn1-xVxFe(P,Si,B) alloys is described.

[0129] The magnetic field dependence of T.sub.C and dT.sub.c/dB for series A and B are shown in FIGS. 9 (a) and (b). The magnetic field (on the horizontal axis) has been corrected by the demagnetizing field using a demagnetization factor of ⅓, as the shape of measuring powders can be simplified as spheres. In order to demonstrate the change in dT.sub.C/dB, the value of T.sub.C (B)-T.sub.C (0) versus the magnetic field is shown in FIGS. 9 (a) and (b). The Clausius-Clapeyron relation for a FOMT corresponds to dT.sub.C/dB=−T.sub.CΔM/L, where B is the applied magnetic field and ΔM is the jump in magnetization, implying that dT.sub.C/dB should increase with an increase of ΔM and a decrease of the latent heat. For the alloys annealed at 1323 and 1373 K, dT.sub.C/dB can be enhanced from 4.0 to 5.0 K/T when the V content is changed from x=0.00 to x=0.02. A value of 5.0 K/T is comparable to the dT.sub.C/dB value of (Mn,Fe).sub.2(P,As) alloys, where dT.sub.C/dB was found to be 5.2 K/T. This increase is mainly caused by the decrease of the latent heat (see table 3) since the values of T.sub.C and ΔM are reduced (see FIG. 8). Moreover, FIG. 9 (c) demonstrates that the magnetic moment per formula unit (μ.sub.f.u.) for series B increases from 3.75 to 3.96 μ.sub.B/.sub.f.u. when x increases from 0.00 to 0.02. The value of μ.sub.f.u. for series B was calculated as mentioned in reference. A larger value of μ.sub.f.u. suggests a larger value of |ΔS.sub.M|. The higher values for dT.sub.c/dB and μ.sub.f.u. explains why a ultra-low thermal hysteresis and a giant GMEC can be achieved simultaneously in the alloys with V. By B substitution, the thermal hysteresis reaches a minimum, while ΔT.sub.ad remains 2 K. Introducing V as a new substitutional element is found to be capable of increasing both dT.sub.C/dB and μ.sub.f.u. and can further decease the hysteresis without losing the GMCE. Thus, the current Mn.sub.1xV.sub.xFe(P,Si,B) compounds provide a feasible alternative for high-frequency near room temperature magnetic cooling applications.

[0130] The ultra-low hysteresis and giant MCE of Mn.sub.1-xV.sub.xFe.sub.0.95P.sub.0.563Si.sub.0.36B.sub.0.077 alloys annealed at 1373 K paves a path to high frequency magnetic refrigeration applications. T.sub.C tends to decrease with increasing V. For the alloys annealed at 1373 K, the latent heat can be reduced by 55% from 6.2 to 2.8 J/g and ΔT.sub.hys-MT decreases by 93% from 1.5 to 0.1 K when x increases from 0.00 to 0.03. The field dependence of the transition temperature (dT.sub.C/dB) is enhanced from 4.0 to 5.0 K/T by V substitution of Mn. Higher values of dT.sub.C/dB and μ.sub.f.u. value are the key reasons that a large GMCE value can be provided even though hysteresis has been reduced to ultra-low values. Finally, an ultra-low value of ΔT.sub.hysDSC (0.7 K) and a giant ΔT.sub.ad (2.3 K) can be achieved in a field of 1 T. Thus, the current Mn1-xVxFe(P,Si,B) compounds can provide a feasible alternative for high-frequency near-room temperature magnetic cooling applications using permanent magnets.

[0131] Below, further information in relation to Low Hysteresis and Large Latent Heat in the Off-stoichiometric Mn—Fe—P—Si—V Magnetocaloric Alloys is described.

[0132] Below, a preparation method is described.

[0133] Polycrystalline (Mn.sub.0.6-yFe.sub.0.4-w).sub.1.90V.sub.0.02P.sub.0.5Si.sub.0.5 (y+w=0.02) alloys were prepared by a powder metallurgy method. The starting materials in the form of Mn (99.7%), Fe (99.7%), red P (99%), Si (99.7%) and V (99.5%) powders were mechanically ball milled for 10 h in an Ar atmosphere with a constant rotation speed of 380 rpm, then pressed into small tablets, and finally sealed in quartz ampoules under 200 μmbar of Ar before employing the various heat treatment conditions. These tablets were annealed at 1373 K for 25 h in order to crystalize and finally quenched in water.

[0134] Below, experimental results are described.

TABLE-US-00004 TABLE 4 The values of T.sub.C, ΔT.sub.hys, the latent heat (L), |Δ S.sub.M| and ΔT.sub.ad under a magnetic field change of 1 T, ΔT.sub.cyclic under a magnetic field change of 1.1 T for (Mn.sub.0.6−yFe.sub.0.4−w).sub.1.90V.sub.0.02 P.sub.0.5Si.sub.0.5 (1#-4#) alloys. Sample T.sub.C ΔT.sub.hys L |ΔS.sub.M| ΔT.sub.ad ΔT.sub.cyclic Cyclic Number (K) (K) (kJ/kg) (J/(kg .Math. K)) (K) (K) Shape y = 0.00, w = 0.00 310.6 1.5 9.3 8.7 2.4 1.6 Powders y = 0.00, w = 0.02 288.6 0.6 6.3 9.2 3.0 2.0 Powders y = 0.01, w = 0.01 292.9 1.0 7.3 8.9 2.4 1.6 Powders y = 0.02, w = 0.00 292.6 1.2 7.1 8.5 2.8 1.8 Powders Gd 290.1 0.0 / 3.0 3.5 2.2 Spheres Fe.sub.2P—B 281 2.0 3.8 9.8 2.5 2.7 Plates

[0135] Below, Giant Magnetocaloric Mn1.17Fe0.72-xVxP0.5Si0.5 alloys is described.

[0136] Below, a preparation method is described.

[0137] Polycrystalline Mn.sub.1.17Fe.sub.0.72-xV.sub.xP.sub.0.5Si.sub.0.5 alloys were prepared by a powder metallurgy method. The starting materials in the form of Mn (99.7%), Fe (99.7%), red P (99%), Si (99.7%) and V (99.5%) powders were mechanically ball milled for 10 h in an Ar atmosphere with a constant rotation speed of 380 rpm, then pressed into small tablets, and finally sealed in quartz ampoules under 200 μmbar of Ar before employing the various heat treatment conditions. These tablets were annealed at 1343 K for 25 h in order to crystalize and finally quenched in water.

[0138] Below, a preparation method is described.

[0139] Polycrystalline (Mn, Fe).sub.1.90V.sub.0.02(P, Si) alloys, in which the Mn/Fe and P/Si ratio change simultaneously, were prepared by a powder metallurgy method. The starting materials in the form of Mn (99.7%), Fe (99.7%), red P (99%), Si (99.7%) and V (99.5%) powders were mechanically ball milled for 10 h in an Ar atmosphere with a constant rotation speed of 380 rpm, then pressed into small tablets, and finally sealed in quartz ampoules under 200 μmbar of Ar before employing the various heat treatment conditions. These tablets were annealed at 1373 K for 25 h in order to crystalize and finally quenched in water.

[0140] Further (comparative) examples are described below, preparation of these materials is not limited to powder metallurgy. Melting synthesis is also possible like described by e.g. S. Rundquist and F. Jellinek, Acta. Chem. Scand. (1959) 13 pp 425.

TABLE-US-00005 TABLE 5a comparative) examples Stoichiometry Mn Fe P Si B V (at %) (at %) (at %) (at %) (at %) (at %) (at %) 1.95 1.2 0.75 0.5 0.5 0 0 1.95 1.19 0.75 0.5 0.5 0 0.01 1.95 1.18 0.75 0.5 0.5 0 0.02 1.95 1.17 0.75 0.5 0.5 0 0.03 1.95 1.16 0.75 0.5 0.5 0 0.04 1.95 1.15 0.75 0.5 0.5 0 0.05 1.95 1.2 0.75 0.5 0.5 0 0 1.95 1.19 0.75 0.5 0.5 0 0.01 1.95 1.18 0.75 0.5 0.5 0 0.02 1.95 1.17 0.75 0.5 0.5 0 0.03 1.95 1.16 0.75 0.5 0.5 0 0.04 1.95 1.15 0.75 0.5 0.5 0 0.05 1.95 1.2 0.75 0.5 0.5 0 0 1.95 1.19 0.75 0.5 0.5 0 0.01 1.95 1.18 0.75 0.5 0.5 0 0.02 1.95 1.17 0.75 0.5 0.5 0 0.03 1.95 1.16 0.75 0.5 0.5 0 0.04 1.95 1.15 0.75 0.5 0.5 0 0.05 1.95 1 0.95 0.593 0.33 0.077 0 1.95 0.99 0.95 0.593 0.33 0.077 0.01 1.95 0.98 0.95 0.593 0.33 0.077 0.02 1.95 0.97 0.95 0.593 0.33 0.077 0.03 1.95 1 0.95 0.563 0.36 0.077 0 1.95 0.99 0.95 0.563 0.36 0.077 0.01 1.95 0.98 0.95 0.563 0.36 0.077 0.02 1.95 0.97 0.95 0.563 0.36 0.077 0.03 1.95 1 0.95 0.563 0.36 0.077 0 1.95 0.99 0.95 0.563 0.36 0.077 0.01 1.95 0.98 0.95 0.563 0.36 0.077 0.02 1.95 0.97 0.95 0.563 0.36 0.077 0.03 1.95 0.9 1.05 0.563 0.36 0.077 0 1.95 0.89 1.05 0.563 0.36 0.077 0.01 1.95 0.88 1.05 0.563 0.36 0.077 0.02 1.95 0.87 1.05 0.563 0.36 0.077 0.03 1.95 0.9 1.05 0.563 0.36 0.077 0 1.95 0.89 1.05 0.563 0.36 0.077 0.01 1.95 0.88 1.05 0.563 0.36 0.077 0.02 1.95 0.87 1.05 0.563 0.36 0.077 0.03 1.92 1.18 0.74 0.5 0.5 0 0 1.9 1.17 0.73 0.5 0.5 0 0 1.88 1.16 0.72 0.5 0.5 0 0 1.86 1.15 0.71 0.5 0.5 0 0 1.84 1.13 0.71 0.5 0.5 0 0 1.82 1.12 0.7 0.5 0.5 0 0 1.9 1.17 0.73 0.5 0.5 0 0 1.9 1.15 0.73 0.5 0.5 0 0.02 1.9 1.16 0.72 0.5 0.5 0 0.02 1.9 1.17 0.71 0.5 0.5 0 0.02 1.88 1.16 0.72 0.5 0.5 0 0 1.88 1.14 0.72 0.5 0.5 0 0.02 1.88 1.15 0.71 0.5 0.5 0 0.02 1.88 1.16 0.7 0.5 0.5 0 0.02

[0141] The thermal hysteresis of samples is less than 2.0 K and dM/dT is larger than 5 Am.sup.2/kgK. T.sub.C covers temperature range of 230-350 K.

TABLE-US-00006 TABLE 5b comparative) examples Stoichiometry Mn Fe P Si B V (at %) (at %) (at %) (at %) (at %) (at %) (at %) 1.95 1.19 0.75 0.5 0.5 0 0.01 1.95 1.18 0.75 0.5 0.5 0 0.02 1.95 1.17 0.75 0.5 0.5 0 0.03 1.95 1.16 0.75 0.5 0.5 0 0.04 1.95 1 0.95 0.593 0.33 0.077 0 1.95 0.98 0.95 0.593 0.33 0.077 0.02 1.95 1 0.95 0.563 0.36 0.077 0 1.95 0.98 0.95 0.563 0.36 0.077 0.02 1.95 0.97 0.95 0.563 0.36 0.077 0.03 1.95 1 0.95 0.563 0.36 0.077 0 1.95 0.9 1.05 0.563 0.36 0.077 0 1.95 0.9 1.05 0.563 0.36 0.077 0 1.88 1.16 0.72 0.5 0.5 0 0 1.9 1.15 0.73 0.5 0.5 0 0.02 1.9 1.16 0.72 0.5 0.5 0 0.02 1.9 1.17 0.71 0.5 0.5 0 0.02

[0142] The term “plurality” refers to two or more.

[0143] The terms “substantially” or “essentially” herein, and similar terms, will be understood by the person skilled in the art. The terms “substantially” or “essentially” may also include embodiments with “entirely”, “completely”, “all”, etc. Hence, in embodiments the adjective substantially or essentially may also be removed. Where applicable, the term “substantially” or the term “essentially” may also relate to 90% or higher, such as 95% or higher, especially 99% or higher, even more especially 99.5% or higher, including 100%.

[0144] The term “comprise” includes also embodiments wherein the term “comprises” means “consists of”.

[0145] The term “and/or” especially relates to one or more of the items mentioned before and after “and/or”. For instance, a phrase “item 1 and/or item 2” and similar phrases may relate to one or more of item 1 and item 2. The term “comprising” may in an embodiment refer to “consisting of” but may in another embodiment also refer to “containing at least the defined species and optionally one or more other species”.

[0146] Furthermore, the terms first, second, third and the like in the description and in the claims, are used for distinguishing between similar elements and not necessarily for describing a sequential or chronological order. It is to be understood that the terms so used are interchangeable under appropriate circumstances and that the embodiments of the invention described herein are capable of operation in other sequences than described or illustrated herein.

[0147] The devices, apparatus, or systems may herein amongst others be described during operation. As will be clear to the person skilled in the art, the invention is not limited to methods of operation, or devices, apparatus, or systems in operation.

[0148] It should be noted that the above-mentioned embodiments illustrate rather than limit the invention, and that those skilled in the art will be able to design many alternative embodiments without departing from the scope of the appended claims.

[0149] In the claims, any reference signs placed between parentheses shall not be construed as limiting the claim.

[0150] Use of the verb “to comprise” and its conjugations does not exclude the presence of elements or steps other than those stated in a claim. Unless the context clearly requires otherwise, throughout the description and the claims, the words “comprise”, “comprising”, and the like are to be construed in an inclusive sense as opposed to an exclusive or exhaustive sense; that is to say, in the sense of “including, but not limited to”.

[0151] The article “a” or “an” preceding an element does not exclude the presence of a plurality of such elements.

[0152] The invention may be implemented by means of hardware comprising several distinct elements, and by means of a suitably programmed computer. In a device claim, or an apparatus claim, or a system claim, enumerating several means, several of these means may be embodied by one and the same item of hardware. The mere fact that certain measures are recited in mutually different dependent claims does not indicate that a combination of these measures cannot be used to advantage.

[0153] The invention also provides a control system that may control the device, apparatus, or system, or that may execute the herein described method or process. Yet further, the invention also provides a computer program product, when running on a computer which is functionally coupled to or comprised by the device, apparatus, or system, controls one or more controllable elements of such device, apparatus, or system.

[0154] The invention further applies to a device, apparatus, or system comprising one or more of the characterizing features described in the description and/or shown in the attached drawings. The invention further pertains to a method or process comprising one or more of the characterizing features described in the description and/or shown in the attached drawings.

[0155] The various aspects discussed in this patent can be combined in order to provide additional advantages. Further, the person skilled in the art will understand that embodiments can be combined, and that also more than two embodiments can be combined. Furthermore, some of the features can form the basis for one or more divisional applications.