HEAT EXCHANGER BEDS COMPOSED OF THERMOMAGNETIC MATERIAL

Abstract

Provided is a packed heat exchanger bed composed of thermomagnetic material particles having a mean particle diameter of 50 μm to 1 mm. The packed bed has porosity of 30-45%. A thermomagnetic material is a metal containing material such as (AyB1-y)2+δCwDxEz, La(FexAl1-x)13Hy or La(FexSi1-x)13Hy, La(FexAlyCoz)13 or La(FeSiyCoz)13, LaMnxFe2-xGe, Heusler alloys, Gd5(SixGe1-x)4, Fe2P-based compounds, manganites of the perovskite type, Tb5(Si4-xGex), XTiGe, Mn2-xZxSb, or Mn2ZxSb1-x, wherein A- E, P, and Z represent various metal atoms.

Description

This is a continuation of U.S. application Ser. No. 12/850,891, filed Aug. 5, 2010, which claimed priority to European patent application no. 09167550.4, filed Aug. 10, 2009, of which all of the disclosures are incorporated herein by reference in their entireties.

DESCRIPTION

The invention relates to packed heat exchanger beds composed of thermomagnetic material particles or composed of a thermomagnetic material monolith, to processes for production thereof and to the use thereof in refrigerators, air conditioning units, heat pumps or in power generation by direct conversion of heat.

BACKGROUND OF THE INVENTION

Thermomagnetic materials, also referred to as magnetocaloric materials, can be used for cooling, for example in refrigerators or air conditioning units, in heat pumps or for direct generation of power from heat without intermediate connection of a conversion to mechanical energy.

Such materials are known in principle and are described, for example, in WO 2004/068512. Magnetic cooling techniques are based on the magnetocaloric effect (MCE) and may constitute an alternative to the known vapor circulation cooling methods. In a material which exhibits a magnetocaloric effect, the alignment of randomly aligned magnetic moments by an external magnetic field leads to heating of the material. This heat can be removed from the MCE material to the surrounding atmosphere by a heat transfer. When the magnetic field is then switched off or removed, the magnetic moments revert back to a random arrangement, which leads to cooling of the material below ambient temperature. This effect can be exploited for cooling purposes; see also Nature, Vol. 415, Jan. 10, 2002, pages 150 to 152. Typically, a heat transfer medium such as water is used for heat removal from the magnetocaloric material.

The materials used in thermomagnetic generators are likewise based on the magnetocaloric effect. In a material which exhibits a magnetocaloric effect, the alignment of randomly aligned magnetic moments by an external magnetic field leads to heating of the material. This heat can be released by the MCE material into the surrounding atmosphere by a heat transfer. When the magnetic field is then switched off or removed, the magnetic moments revert back to a random alignment, which leads to cooling of the material below ambient temperature. This effect can be exploited firstly for cooling purposes, and secondly for conversion of heat to electrical energy.

The magnetocaloric generation of electrical energy is associated with magnetic heating and cooling. At the time of first conception, the process for energy generation was described as pyromagnetic energy generation. Compared to devices of the Peltier or Seebeck type, these magnetocaloric devices can have a significantly higher energy efficiency.

The research into this physical phenomenon began in the late 19^th century, when two scientists, Tesla and Edison, filed a patent on pyromagnetic generators.

For the thermomagnetic or magnetocaloric applications, the material should permit efficient heat exchange in order to be able to achieve high efficiencies. Both in the course of cooling and in the course of power generation, the thermomagnetic material is used in a heat exchanger.

DETAILED DESCRIPTION OF THE INVENTION

It is an object of the present invention to provide heat exchanger beds composed of thermomagnetic shaped bodies which are suitable for use in heat exchangers, especially for cooling purposes or for power generation. These shaped bodies should allow high heat transfer, have a low flow resistance for heat exchange media and possess a high magnetocaloric density.

The object is achieved in accordance with the invention by a packed heat exchanger bed composed of thermomagnetic material particles which have a mean diameter in the range from 50 μm to 1 mm and give rise to a porosity in the packed bed in the range from 30 to 45%.

The porosity is defined as the proportion by volume of empty space (interstices) in the heat exchanger bed.

The heat exchanger bed can be produced by a process in which a powder of the thermomagnetic material is subjected to shaping to form the thermomagnetic material particles and the material particles are subsequently packed to form the heat exchanger bed.

The object is additionally achieved by a heat exchanger bed composed of a thermomagnetic material monolith which has continuous channels with a cross-sectional area of the individual channels in the range from 0.001 to 0.2 mm² and a wall thickness of 50 to 300 μm, a porosity in the range from 10 to 60% and a ratio of surface to volume in the range from 3000 to 50 000 m²/m³.

Alternatively, the thermomagnetic material monolith may comprise or be formed from a plurality of parallel sheets with a sheet thickness of 0.1 to 2 mm, preferably 0.5 to 1 mm, and a plate separation (interstice) of 0.05 to 1 mm, preferably 0.05 to 0.2 mm. The number of sheets may, for example, be 5 to 100, preferably 10 to 50.

The heat exchanger bed is produced, for example, by extrusion, injection molding or molding of the thermomagnetic material to form the monolith.

The object is additionally achieved by the use of a heat exchanger bed as defined above in refrigerators, air conditioning units, heat pumps or in power generation by direct conversion of heat.

It has been found in accordance with the invention that a packed heat exchanger bed composed of thermomagnetic material particles is a highly efficient material geometry which allows optimal operation of the heat exchanger bed when the thermomagnetic material particles have a mean diameter in the range from 50 μm to 1 mm and there is a porosity in the packed bed in the range from 30 to 45%. The individual material particles may have any desired form. The material particles are preferably in spherical form, pellet form, sheet form or cylinder form. The material particles are more preferably in spherical form. The diameter of the material particles, especially of the spheres, is 50 μm to 1 mm, more preferably 200 to 400 μm. The material particles, especially spheres, may have a size distribution. The size distribution is preferably narrow, such that predominantly spheres of one size are present. The diameter preferably differs from the mean diameter by not more than 20%, more preferably by not more than 10%, especially by not more than 5%.

In the packed bed, this results in a porosity in the range from 30 to 45%, more preferably from 36 to 40%.

Material particles, especially spheres with the above dimensions, as a packed heat exchanger bed, give high heat transfer coefficients between solid and fluid (heat exchanger fluid), the pressure drop being low. This allows an improved coefficient of performance (COP) of the heat exchanger bed. The high heat transfer coefficient allows the packed beds to be operated at higher frequencies than customary, and hence allows greater energy extraction.

It is possible for a single thermomagnetic material to be present in the packed heat exchanger beds, but it is also possible that a series of different magnetocaloric materials with different Curie temperatures are combined. This allows a large temperature change overall to be achieved in a single heat exchanger bed. Preference is given in accordance with the invention to combining thermomagnetic materials whose maximum difference in Curie temperature is 1 to 10° C., more preferably 2 to 6° C.

For the particular operating conditions, the performance of the packed heat exchanger bed can be optimized by using material particles, especially spheres, of different diameter. A lower diameter, especially sphere diameter, leads to a higher coefficient of heat transfer and hence allows better heat exchange. This, however, is associated with a higher pressure drop through the heat exchanger bed. Conversely, the use of larger material particles, especially spheres, leads to slower heat transfer, but to lower pressure drops.

The packed heat exchanger bed composed of the thermomagnetic material particles can be produced in any suitable manner. The thermomagnetic material particles are first produced, for example by shaping a powder of the thermoelectric material to form the thermomagnetic material particles. Subsequently, the material particles are packed to form the heat exchanger bed. This can be done by pouring the material particles into a suitable vessel, in which case the settling of the bed can be improved by shaking. Floating in a fluid with subsequent settling of the material particles is also possible. It is additionally possible to settle the individual material particles in a controlled manner to form a homogeneous structure. In this case, it is possible, for example, to achieve a tight cubic packing of spheres.

The movement resistance of the packed heat exchanger bed can be achieved by any suitable measures. For example, the vessel in which the packed heat exchanger bed is present can be closed on all sides. This can be done, for example, using a mesh cage. In addition, it is possible to join the individual material particles to one another, for example by surface melting of the material particles in the packed bed or by sintering the material particles to one another in the packed bed. The surface melting or sintering should be effected such that the interstices between the material particles are very substantially preserved.

The formation of the packed heat exchanger bed by thermomagnetic material particles in sheet, cylinder, pellet or sphere form or similar form is advantageous, since a large ratio of surface to mass is achieved therewith. This achieves an improved heat transfer rate coupled with relatively low pressure drop.

A second advantageous embodiment of the heat exchanger bed is a thermomagnetic material monolith which has continuous channels. The monolith can be considered as a block of thermomagnetic material, in which case two opposite end sides of the block have entry and exit orifices for a fluid which are connected by channels which run through the entire monolith. Corresponding monoliths can be derived, for example, from a tube bundle in which the individual tubes of thermomagnetic material are joined to one another. The channels are preferably parallel to one another and generally run through the monoliths in a straight line. When particular use requirements are made, it is also possible to provide a curved profile of the channels. Corresponding monolith forms are known, for example, from automotive exhaust gas catalysts. The thermomagnetic material monoliths may thus have, for example, a cellular form, in which case the individual cells may have any desired geometry. For example, the channels may have a hexagonal cross section as in the case of a honeycomb, or a rectangular cross section. Star-shaped cross sections, round cross sections, oval cross sections or other cross sections are also possible in accordance with the invention, provided that the following conditions are observed:

• • cross-sectional area of the individual channels in the range from 0.001 to 0.2 mm², more preferably 0.01 to 0.03 mm², especially 0.015 to 0.025 mm²
  • wall thickness of 50 to 300 μm, more preferably 50-150 μm, especially 85 to 115 μm
  • porosity in the range from 10 to 60%, more preferably 15 to 35%, especially 20 to 30%
  • ratio of surface to volume in the range from 3000 to 50 000 m²/m³, more preferably 5000 to 15 000 m²/m³.

The individual channels may have, for example, with a rectangular cross section, cross-sectional dimensions of 50 μm×25 μm to 600 μm×300 μm, especially about 200 μm×100 μm. The wall thickness may especially preferably be about 100 μm. The porosity may more preferably be about 25%. The porosity is thus typically significantly lower than the porosity of a packed sphere bed. This allows more magnetocaloric material to be introduced into a given volume of the magnetic field. This leads to a greater thermal effect with equal expenditure to provide the magnetic field.

The shaped bodies have continuous channels. This allows a liquid heat carrier medium to flow through, such as water, water/alcohol mixtures, water/salt mixtures or gases such as air or noble gases. Preference is given to using water or water/alcohol mixtures, in which case the alcohol may be a mono- or polyhydric alcohol. For example, the alcohols may be glycols.

The monoliths may be formed, for example, from layers of magnetocaloric material with thin parallel channels in the layers.

The very large ratio of surface to volume allows excellent heat transfer, coupled with a very low pressure drop. The pressure drop is, for instance, one order of magnitude lower than for a packed bed of spheres which has the identical heat transfer coefficient. The monolith form thus allows the coefficient of performance (COP), for example of a magnetocaloric cooling device, to be improved considerably once again.

The thermomagnetic material itself may be selected from any suitable thermomagnetic materials. Suitable materials are described in a multitude of documents, for example in WO 2004/068512.

Preferred thermomagnetic materials are selected from

• (1) compounds of the general formula (I)

(A_yB_1-y)_2+δC_wD_xE_z   (I)

• • where
  • A is Mn or Co,
  • B is Fe, Cr or Ni,
  • C, D and E at least two of C, D and E are different, have a non-vanishing concentration and are selected from P, B, Se, Ge, Ga, Si, Sn, N, As and Sb, where at least one of C, D and E is Ge or Si,
  • δ is a number in the range from −0.1 to 0.1,
  • w, x, y, z are numbers in the range from 0 to 1, where w+x+z=1;
• (2) La- and Fe-based compounds of the general formulae (II) and/or (III) and/or (IV)

La(Fe_xAl_1-x)₁₃H_y or La(Fe_xSi_1-x)₁₃H_y   (II)

• • where
  • x is a number from 0.7 to 0.95,
  • y is a number from 0 to 3, preferably from 0 to 2;

La(Fe_xAl_yCo_z)₁₃ or La(Fe_xSi_yCo_z)₁₃   (III)

• • where
  • x is a number from 0.7 to 0.95,
  • y is a number from 0.05 to 1−x,
  • z is a number from 0.005 to 0.5;

LaMn_xFe_2-xGe   (IV)

• • where
  • x is a number from 1.7 to 1.95 and
• (3) Heusler alloys of the MnTP type where T is a transition metal and P is a p-doping metal having an electron count per atom e/a in the range from 7 to 8.5,
• (4) Gd- and Si-based compounds of the general formula (V)

Gd₅(Si_xGe_1-x)₄   (V)

• • where x is a number from 0.2 to 1,
• (5) Fe₂P-based compounds,
• (6) manganites of the perovskite type,
• (7) compounds which comprise rare earth elements and are of the general formulae (VI) and (VII)

Tb₅(Si_4-xGe_x)   (VI)

• • where x=0, 1, 2, 3, 4,

XTiGe   (VII)

• • where X=Dy, Ho, Tm,
• (8) Mn- and Sb- or As-based compounds of the general formulae (VIII) and (IX)

Mn_2-xZ_xSb   (VIII)

Mn₂Z_xSb_1-x   (IX)

• • where
  • Z is Cr, Cu, Zn, Co, V, As, Ge,
  • x is from 0.01 to 0.5,
  • where Sb may be replaced by As when Z is not As.

It has been found in accordance with the invention that the aforementioned thermomagnetic materials can be used advantageously in heat exchangers, magnetic cooling, heat pumps or thermomagnetic generators or regenerators when they have an inventive structure.

Particular preference is given in accordance with the invention to the metal-based materials selected from compounds (1), (2) and (3), and also (5).

Materials particularly suitable in accordance with the invention are described, for example, in WO 2004/068512, Rare Metals, Vol. 25, 2006, pages 544 to 549, J. Appl. Phys. 99, 08Q107 (2006), Nature, Vol. 415, Jan. 10, 2002, pages 150 to 152 and Physica B 327 (2003), pages 431 to 437.

In the aforementioned compounds of the general formula (I), C, D and E are preferably identical or different and are selected from at least one of P, Ge, Si, Sn and Ga.

The thermomagnetic material of the general formula (I) is preferably selected from at least quaternary compounds which, as well as Mn, Fe, P and optionally Sb, additionally comprise Ge or Si or As or Ge and Si, Ge and As or Si and As, or Ge, Si and As.

Preferably at least 90% by weight, more preferably at least 95% by weight, of component A is Mn. Preferably at least 90% by weight, more preferably at least 95% by weight, of B is Fe. Preferably at least 90% by weight, more preferably at least 95% by weight, of C is P. Preferably at least 90% by weight, more preferably at least 95% by weight, of D is Ge. Preferably at least 90% by weight, more preferably at least 95% by weight, of E is Si.

The material preferably has the general formula MnFe(P_wGe_xSi_z).

x is preferably a number in the range from 0.3 to 0.7, w is less than or equal to 1−x and z corresponds to 1−x−w.

The material preferably has the crystalline hexagonal Fe₂P structure. Examples of suitable materials are MnFeP_{0.45 to 0.7}, Ge_{0.55 to 0.30} and MnFeP_{0.5 to 0.70}, (Si/Ge)_{0.5 to 0.30}.

Suitable compounds are additionally M_n1+xFe_1-xP_1-yGe_y with x in the range from −0.3 to 0.5, y in the range from 0.1 to 0.6. Likewise suitable are compounds of the general formula Mn_1+xFe_1-xP_1-yGe_y-zSb_z with x in the range from −0.3 to 0.5, y in the range from 0.1 to 0.6 and z less than y and less than 0.2. Also suitable are compounds of the formula Mn₁₊xFe_1-xP_1-yGe_y-zSi_z with x in the range from 0.3 to 0.5, y in the range from 0.1 to 0.66, z less than or equal to y and less than 0.6.

Also suitable are further Fe₂P-based compounds proceeding from Fe₂P and FeAs₂, optionally Mn and P. They correspond, for example, to the general formulae MnFe_1-xCo_xGe, where x=0.7−0.9, Mn_5-xFe_xSi₃ where x=0−5, Mn₅Ge_3-xSi_x where x=0.1−2, Mn₅Ge_3-xSb_x where x=0−0.3, Mn_2-xFe_xGe₂ where x=0.1−0.2, Mn_3-xCo_xGaC where x=0−0.05.

Preferred La- and Fe-based compounds of the general formulae (II) and/or (III) and/or (IV) are La(Fe_0.90Si_0.10)₁₃, La(Fe_0.89Si_0.11)₁₃, La(Fe_0.880Si_0.120)₁₃, La(Fe_0.877Si_0.123)₁₃, LaFe_11.8Si_1.2, La(Fe_0.88Si_0.12)₁₃H_0.5, La(Fe_0.88Si_0.12)₁₃H_1.0, LaFe_11.7Si_1.3H_1.1, LaFe_11.57Si_1.43H_1.3, La(Fe_0.88Si_0.12)H_1.5, La(Fe_11.2Co_0.7Si_1.1, LaFe_11.5Al_1.5C_0.1, LaFe_11.5Al_1.5C_0.2, LaFe_11.5Al_1.5C_0.4, LaFe_11.5Al_1.5Co_0.5, La(Fe_0.94Co_0.06)_11.83Al_1.17, La(Fe_0.92Co_0.08)_11.83Al_1.17.

Suitable manganese-comprising compounds are MnFeGe, MnFe_0.9Co_0.1Ge, MnFe_0.8Co_0.2Ge, MnFe_0.7Co_0.3Ge, MnFe_0.6Co_0.4Ge, MnFe_0.5Co_0.5Ge, MnFe_0.4Co_0.6Ge, MnFe_0.3Co_0.7Ge, MnFe_0.2Co_0.8Ge, MnFe_0.15Co_0.85Ge, MnFe_0.1Co_0.9Ge, MnCoGe, Mn₅Ge_2.5Si_0.5, Mn₅Ge₂Si, Mn₅Ge_1.5Si_1.5, Mn₅GeSi₂, Mn₅Ge₃, Mn₅Ge_2.9Sb_0.1, Mn₅Ge_2.8Sb_0.2, Mn₅Ge_2.7Sb_0.3, LaMn_1.9Fe_0.1Ge, LaMn_1.85Fe_0.15Ge, LaMn_1.8Fe_0.2Ge, (Fe_0.9Mn_0.1)₃C, (Fe_0.8Mn_0.2)₃C, (Fe_0.7Mn_0.3)₃C, Mn₃GaC, MnAs, (Mn, Fe)As, Mn_1+δAs_0.8Sb_0.2, MnAs_0.75Sb_0.25, Mn_1.1As_0.75Sb_0.25, Mn_1.5As_0.75Sb_0.25.

Heusler alloys suitable in accordance with the invention are, for example, Ni₂MnGa, Fe₂MnSi_1-xGe_x with x=0−1 such as Fe₂MnSi_0.5Ge_0.5, Ni_52.5Mn_22.4Ga_24.7, Ni_50.9Mn_24.7Ga_24.4, Ni_55.2Mn_18.6Ga_26.2, Ni_51.6Mn_24.7Ga_23.8, Ni_52.7Mn_23.5Ga_23.4, CoMnSb, CoNb_0.2Mn_0.8Sb, CoNb_0.4Mn_0.6SB, CoNb_0.6Mn_0.4Sb, Ni₅₀Mn₃₅Sn₁₅, Ni₅₀Mn₃₇Sn₁₃, MnFeP_0.45As_0.55, MnFeP_0.47As_0.53, Mn_1.1Fe_0.9P_0.47As_0.53, MnFeP_0.89-xSi_xGe_0.11, X=0.22, X=0.26, X=0.30, X=0.33.

Additionally suitable are Fe₉₀Zr₁₀, Fe₈₂Mn₈Zn₁₀, Co₆₆Nb₉Cu₁Si₁₂B₁₂, Pd₄₀M_22.5Fe_17.5P₂₀, FeMoSiBCuNb, Gd₇₀Fe₃₀, GdNiAl, NdFe₁₂B₆GdMn₂.

Manganites of the perovskite type are, for example, La_0.6Ca_0.4MnO₃, La_0.67Ca_0.33MnO₃, La_0.8Ca_0.2MnO₃, La_0.7Ca_0.3MnO₃, La_0.958Li_0.025Ti_0.1Mn_0.9O₃, La0.65Ca0.35Ti_0.1Mn_0.9O₃, La_0.799Na_0.199MnO_2.97, La_0.88Na_0.099Mn_0.977O₃, La_0.877K_0.096Mn_0.974O₃, La_0.65Sr_0.35Mn_0.95Cn_0.05O₃, La_0.7Nd_0.1Na_0.2MnO₃, La_0.5Ca_0.3Sr_0.2MnO₃.

Gd- and Si-based compounds of the general formula (V)

Gd₅(Si_xGe_1-x)₄

where x is a number from 0.2 to 1

are, for example, Gd₅(Si_0.5Ge_0.5)₄, Gd₅(Si_0.425Ge0.575)₄, Gd₅(Si_0.45Ge_0.55)₄, Gd₅(Si_0.365Ge_0.635)₄, Gd₅(Si_0.3Ge_0.7)₄, Gd₅(Si_0.25Ge_0.75)₄.

Compounds comprising rare earth elements are Tb₅(Si_4-xGe_x) with x=0, 1, 2, 3, 4 or XTiGe with X=Dy, Ho, Tm, for example Tb₅Si₄, Tb₅(Si₃Ge), Tb(Si₂Ge₂), Tb₅Ge₄, DyTiGe, HoTiGe, TmTiGe.

Mn- and Sb- or As-based compounds of the general formulae (VIII) and (IX) preferably have the definitions of z=0.05 to 0.3, Z=Cr, Cu, Ge, As, Co.

The thermomagnetic materials used in accordance with the invention can be produced in any suitable manner.

The thermomagnetic materials are produced, for example, by solid phase reaction of the starting elements or starting alloys for the material in a ball mill, subsequent pressing, sintering and heat treatment under inert gas atmosphere and subsequent slow cooling to room temperature. Such a process is described, for example, in J. Appl. Phys. 99, 2006, 08Q107.

Processing via melt spinning is also possible. This makes possible a more homogeneous element distribution which leads to an improved magnetocaloric effect; cf. Rare Metals, Vol. 25, October 2006, pages 544 to 549. In the process described there, the starting elements are first induction-melted in an argon gas atmosphere and then sprayed in the molten state through a nozzle onto a rotating copper roller. There follows sintering at 1000° C. and slow cooling to room temperature.

In addition, reference may be made to WO 2004/068512 for the production.

The materials obtained by these processes frequently exhibit high thermal hysteresis. For example, in compounds of the Fe₂P type substituted by germanium or silicon, large values for thermal hysteresis are observed within a wide range of 10 K or more.

Preference is therefore given to a process for producing the thermomagnetic materials, comprising the following steps:

• • a) reacting chemical elements and/or alloys in a stoichiometry which corresponds to the metal-based material in the solid and/or liquid phase,
  • b) if appropriate converting the reaction product from stage a) to a solid,
  • c) sintering and/or heat treating the solid from stage a) or b),
  • d) quenching the sintered and/or heat-treated solid from stage c) at a cooling rate of at least 100 K/s.

The thermal hysteresis can be reduced significantly and a large magnetocaloric effect can be achieved when the metal-based materials are not cooled slowing to ambient temperature after the sintering and/or heat treatment, but rather are quenched at a high cooling rate. This cooling rate is at least 100 K/s. The cooling rate is preferably from 100 to 10 000 K/s, more preferably from 200 to 1300 K/s. Especially preferred cooling rates are from 300 to 1000 K/s.

The quenching can be achieved by any suitable cooling processes, for example by quenching the solid with water or aqueous liquids, for example cooled water or ice/water mixtures. The solids can, for example, be allowed to fall into ice-cooled water. It is also possible to quench the solids with subcooled gases such as liquid nitrogen. Further processes for quenching are known to those skilled in the art. What is advantageous here is controlled and rapid cooling.

The rest of the production of the thermomagnetic materials is less critical, provided that the last step comprises the quenching of the sintered and/or heat-treated solid at the inventive cooling rate. The process may be applied to the production of any suitable thermomagnetic materials for magnetic cooling, as described above.

In step (a) of the process, the elements and/or alloys which are present in the later thermomagnetic material are converted in a stoichiometry which corresponds to the thermomagnetic material in the solid or liquid phase.

Preference is given to performing the reaction in stage a) by combined heating of the elements and/or alloys in a closed vessel or in an extruder, or by solid phase reaction in a ball mill. Particular preference is given to performing a solid phase reaction, which is effected especially in a ball mill. Such a reaction is known in principle; cf. the documents cited above. Typically, powders of the individual elements or powders of alloys of two or more of the individual elements which are present in the later thermomagnetic material are mixed in pulverulent form in suitable proportions by weight. If necessary, the mixture can additionally be ground in order to obtain a microcrystalline powder mixture. This powder mixture is preferably heated in a ball mill, which leads to further comminution and also good mixing, and to a solid phase reaction in the powder mixture. Alternatively, the individual elements are mixed as a powder in the selected stoichiometry and then melted.

The combined heating in a closed vessel allows the fixing of volatile elements and control of the stoichiometry. Specifically in the case of use of phosphorus, this would evaporate easily in an open system.

The reaction is followed by sintering and/or heat treatment of the solid, for which one or more intermediate steps can be provided. For example, the solid obtained in stage a) can be subjected to shaping before it is sintered and/or heat treated.

Alternatively, it is possible to send the solid obtained from the ball mill to a melt-spinning process. Melt-spinning processes are known per se and are described, for example, in Rare Metals, Vol. 25, October 2006, pages 544 to 549, and also in WO 2004/068512.

In these processes, the composition obtained in stage a) is melted and sprayed onto a rotating cold metal roller. This spraying can be achieved by means of elevated pressure upstream of the spray nozzle or reduced pressure downstream of the spray nozzle. Typically, a rotating copper drum or roller is used, which can additionally be cooled if appropriate. The copper drum preferably rotates at a surface speed of from 10 to 40 m/s, especially from 20 to 30 m/s. On the copper drum, the liquid composition is cooled at a rate of preferably from 10² to 10⁷ K/s, more preferably at a rate of at least 10⁴ K/s, especially with a rate of from 0.5 to 2×10⁶ K/s.

The melt-spinning, like the reaction in stage a) too, can be performed under reduced pressure or under an inert gas atmosphere.

The melt-spinning achieves a high processing rate, since the subsequent sintering and heat treatment can be shortened. Specifically on the industrial scale, the production of the thermomagnetic materials thus becomes significantly more economically viable. Spray-drying also leads to a high processing rate. Particular preference is given to performing melt spinning.

Alternatively, in stage b), spray cooling can be carried out, in which a melt of the composition from stage a) is sprayed into a spray tower. The spray tower may, for example, additionally be cooled. In spray towers, cooling rates in the range from 10³ to 10⁵ K/s, especially about 10⁴ K/s, are frequently achieved.

The sintering and/or heat treatment of the solid is effected in stage c) preferably first at a temperature in the range from 800 to 1400° C. for sintering and then at a temperature in the range from 500 to 750° C. for heat treatment. For example, the sintering can then be effected at a temperature in the range from 500 to 800° C. For shaped bodies/solids, the sintering is more preferably effected at a temperature in the range from 1000 to 1300° C., especially from 1100 to 1300° C. The heat treatment can then be effected, for example, at from 600 to 700° C.

The sintering is performed preferably for a period of from 1 to 50 hours, more preferably from 2 to 20 hours, especially from 5 to 15 hours. The heat treatment is performed preferably for a period in the range from 10 to 100 hours, more preferably from 10 to 60 hours, especially from 30 to 50 hours. The exact periods can be adjusted to the practical requirements according to the materials.

In the case of use of the melt-spinning process, the period for sintering or heat treatment can be shortened significantly, for example to periods of from 5 minutes to 5 hours, preferably from 10 minutes to 1 hour. Compared to the otherwise customary values of 10 hours for sintering and 50 hours for heat treatment, this results in a major time advantage.

The sintering/heat treatment results in partial melting of the particle boundaries, such that the material is compacted further.

The melting and rapid cooling in stage b) thus allows the duration of stage c) to be reduced considerably. This also allows continuous production of the thermomagnetic materials.

The pressing can be carried out, for example, as cold pressing or as hot pressing. The pressing may be followed by the sintering process already described.

In the sintering process or sintered metal process, the powders of the thermomagnetic material are first converted to the desired shape of the shaped body, and then bonded to one another by sintering, which affords the desired shaped body. The sintering can likewise be carried out as described above.

It is also possible in accordance with the invention to introduce the powder of the thermomagnetic material into a polymeric binder, to subject the resulting thermoplastic molding material to a shaping, to remove the binder and to sinter the resulting green body. It is also possible to coat the powder of the thermomagnetic material with a polymeric binder and to subject it to shaping by pressing, if appropriate with heat treatment.

According to the invention, it is possible to use any suitable organic binders which can be used as binders for thermomagnetic materials. These are especially oligomeric or polymeric systems, but it is also possible to use low molecular weight organic compounds, for example sugars.

The thermomagnetic powder is mixed with one of the suitable organic binders and filled into a mold. This can be done, for example, by casting or injection molding or by extrusion. The polymer is then removed catalytically or thermally and sintered to such an extent that a porous body with monolith structure is formed.

Hot extrusion or metal injection molding (MIM) of the thermomagnetic material is also possible, as is construction from thin sheets which are obtainable by rolling processes. In the case of injection molding, the channels in the monolith have a conical shape, in order to be able to remove the moldings from the mold. In the case of construction from sheets, all channel walls can run in parallel.

The particular processes are controlled so as to result in heat exchanger beds which have a suitable combination of high heat transfer, low flow resistance and high magnetocaloric density. Preference is given to an optimal ratio of high magnetocaloric density and sufficient porosity, so as to ensure efficient heat removal and efficient heat exchange. In other words, the inventive shaped bodies exhibit a high ratio of surface to volume. By virtue of the high surface area, it is possible to transport large amounts of heat out of the material and to transfer them into a heat transfer medium. The structure should be mechanically stable in order to cope with the mechanical stresses by a fluid cooling medium. In addition, the flow resistance should be sufficiently low as to result in only a low pressure drop through the porous material. The magnetic field volume should preferably be minimized.

Stacks of heat exchanger beds or monoliths can be thermally insulated from one another by appropriate intermediate layers, for example by carbon sieves. This prevents heat losses as a result of conduction of heat within the material. By virtue of appropriate design, the intermediate layers may also serve for homogeneous distribution of the heat exchanger medium.

The heat exchanger beds obtained in accordance with the invention are preferably used in refrigerators, air conditioning units, heat pumps or heat exchangers, or in power generation by direct conversion of heat. The materials should exhibit a large magnetocaloric effect within a temperature range between −100° C. and +150° C.

The heat transfer rate limits the cycle speed and hence has a great influence on the power density.

In power generation, a coil of an electrically conductive material is arranged around the thermomagnetic material. In this coil, a current is induced through alteration of the magnetic field or of the magnetization, and can be used to perform electrical work. Preference is given to selecting the coil geometry and the geometry of the thermomagnetic material so as to result in a maximum energy yield with minimum pressure drop. The coil winding density (turns/length), the coil length, the charge resistance and the temperature change of the thermomagnetic material are important influencing parameters for the energy yield.

The thermomagnetic material is present in an external magnetic field. This magnetic field can be generated by permanent magnets or electromagnets. Electromagnets may be conventional electromagnets or superconductive magnets.

The thermomagnetic generator is preferably designed such that the thermal energy from geothermal sources or from the waste heat of industrial processes or from solar energy or solar collectors can be converted, for example, in photovoltaics. Specifically in regions with geothermal activity, the inventive thermomagnetic generator allows simple power generation exploiting geothermal heat. In industrial processes, process heat or waste heat frequently arises, which is typically discharged to the environment and is not utilized further. Wastewaters frequently also have a higher temperature on exit than on entry. The same applies to cooling water. The thermomagnetic generator thus allows the recovery of electrical energy from waste heat which is otherwise lost. By virtue of the fact that the thermomagnetic generator can be operated in the region of room temperature, it is possible to utilize this waste heat and to convert it to electrical energy. The energy conversion is effected preferably at temperatures in the range from 20 to 150° C., more preferably at temperatures in the range from 40 to 120° C.

In (concentrated) photovoltaic systems, high temperatures are frequently attained, such that it is necessary to cool. This heat to be removed can be converted to power in accordance with the invention.

For power generation, the thermomagnetic material is contacted alternately with a warm reservoir and a cool reservoir and hence subjected to a warming and cooling cycle. The cycle time is selected according to the particular technical prerequisites.

The examples which follow describe the production of thermomagnetic materials suitable for the inventive application and the design of monoliths and catalyst beds.

EXAMPLES

Example 1

Evacuated quartz ampoules which comprised pressed samples of MnFePGe were kept at 1100° C. for 10 hours in order to sinter the powder. This sintering was followed by heat treatment at 650° C. for 60 hours in order to bring about homogenization. Instead of slow cooling in the oven to room temperature, the samples were, however, immediately quenched in water at room temperature. The quenching in water caused a certain degree of oxidation at the sample surfaces. The outer oxidized shell was removed by etching with dilute acid. The XRD patterns showed that all samples crystallized in a structure of the Fe₂P type.

The following compositions were obtained:

Mn_1.1Fe_0.9P_0.81Ge_0.19; Mn_1.1Fe_0.9P_0.78Ge_0.22, Mn_1.1Fe_0.9P_0.75Ge_0.25 and Mn_1.2Fe_0.8P_0.81Ge_0.19. The values observed for the thermal hysteresis are 7 K, 5 K, 2 K and 3 K for these samples in the given sequence. Compared to a slowly cooled sample, which has a thermal hysteresis of more than 10 K, the thermal hysteresis has been greatly reduced.

The thermal hysteresis was determined in a magnetic field of 0.5 tesla.

The Curie temperature can be adjusted by varying the Mn/Fe ratio and the Ge concentration, as can the value of the thermal hysteresis.

The change in the magnetic entropy, calculated from the direct current magnetization using the Maxwell relationship, for a maximum field change of from 0 to 2 tesla, is 14 J/kgK, 20 J/kgK and 12.7 J/kgK respectively for the first three samples.

The Curie temperature and the thermal hysteresis decrease with increasing Mn/Fe ratio. As a result, the MnFePGe compounds exhibit relatively large MCE values in a low field. The thermal hysteresis of these materials is very low.

Example 2

Melt-Spinning of MnFeP(GeSb)

The polycrystalline MnFeP(Ge, Sb) alloys were first produced in a ball mill with high energy input and by solid phase reaction methods, as described in WO 2004/068512 and J. Appl. Phys. 99, 08 Q107 (2006). The material pieces were then introduced into a quartz tube with a nozzle. The chamber was evacuated to a vacuum of 10⁻² mbar and then filled with high-purity argon gas. The samples were melted by means of a high frequency and sprayed through the nozzle owing to a pressure difference to a chamber containing a rotating copper drum. The surface speed of the copper wheel was adjustable, and cooling rates of about 10⁵ K/s were achieved. Subsequently, the spun ribbons were heat treated at 900° C. for one hour.

X-ray diffractometry reveals that all samples crystallize in the hexagonal Fe₂P structure pattern. In contrast to samples not produced by the melt-spinning method, no smaller contaminant phase of MnO was observed.

The resulting values for the Curie temperature, the hysteresis and the entropy were determined for different peripheral speeds in the melt-spinning. The results are listed in Tables 1 and 2 which follow. In each case, low hysteresis temperatures were determined.

	TABLE 1
	V (m/s)	Tc (K)	ΔThys (K)	−ΔS (J/kgK)
Ribbons
Mn1.2Fe0.8P0.73Ge0.25Sb0.02	30	269	4	12.1
Mn1.2Fe0.8P0.70Ge0.20Sb0.10	30	304	4.5	19.0
	45	314	3	11.0
MnFeP0.70Ge0.20Sb0.10	20	306	8	17.2
	30	340	3	9.5
MnFeP0.75Ge0.25	20	316	9	13.5
	40	302	8	—
Mn1.1Fe0.9P0.78Ge0.22	20	302	5	—
	40	299	7	—
Mn1.1Fe0.9P0.75Ge0.25	30	283	9	11.2
Mn1.2Fe0.8P0.75Ge0.25	30	240	8	14.2
Mn1.1Fe0.9P0.73Ge0.27	30	262	5	10.1
Bulk
MnFeP0.75Ge0.25		327	3	11.0
Mn1.1Fe0.9P0.81Ge0.19		260	7	14.0
Mn1.1Fe0.9P0.78Ge0.22		296	5	20.0
Mn1.1Fe0.9P0.75Ge0.25		330	2	13.0
Mn1.2Fe0.8P0.81Ge0.19		220	3	7.7
Mn1.2Fe0.8P0.75Ge0.25		305	3	—
Mn1.2Fe0.8P0.73Ge0.27		313	5	—
Mn1.3Fe0.7P0.78Ge0.22		203	3	5.1
Mn1.3Fe0.7P0.75Ge0.25		264	1	—

	TABLE 2
	Tc (K)	ΔThys (K)	−ΔS (J/kgK)
Bulk
MnFeP0.75Ge0.25	327	3	11.0
Mn1.16Fe0.84P0.75Ge0.25	330	5	22.5
Mn1.18Fe0.82P0.75Ge0.25	310	3	16.1
Mn1.20Fe0.80P0.75Ge0.25	302	1	12.0
Mn1.22Fe0.78P0.75Ge0.25	276	4	11.7
Mn1.26Fe0.74P0.75Ge0.25	270	1	8.5
Mn1.1Fe0.9P0.81Ge0.19	260	6	13.8
Mn1.1Fe0.9P0.78Ge0.22	296	4	20.0
Mn1.1Fe0.9P0.77Ge0.23	312	2	14.6
Mn1.1Fe0.9P0.75Ge0.25	329	2	13.0
Ribbons
Mn1.20Fe0.80P0.75Ge0.25	288	1	20.3
Mn1.22Fe0.78P0.75Ge0.25	274	2	15.3
Mn1.24Fe0.76P0.75Ge0.25	254	2	16.4
Mn1.26Fe0.74P0.75Ge0.25	250	4	14.4
Mn1.30Fe0.70P0.75Ge0.25	230	0	9.8

Example 3

A simple magnetocaloric regenerator formed from a packed or structured bed of a cascade of magnetocaloric materials a magnet arrangement and a heat transfer fluid was examined with the following results:

1. For given operating conditions:

Form of the magnetocaloric material	Power (W)	Pressure drop (Pa)
Spheres, d = 0.3 mm	160.5	1.8 × 104
Spheres, d = 0.05 mm	162.9	5.6 × 105
Spheres, d = 0.03 mm	163.0	1.52 × 106
Monolith, channels with square cross	154.6	1.71 × 103
section, side length 0.3 mm
Cylinder, d = h = 5 mm	Heat transfer too slow to build up a
	temperature gradient
Cylinder, d = h = 0.5 mm	154.3	9.11 × 103

It is evident that spheres of diameter 0.3 mm and the monolith give rise to good heat transfer performances, while only low pressure drops occurred (especially in the monolith).

2. For operation at different frequencies (all other operating conditions remaining the same):

The table which follows lists the net power (which is the cooling power minus the power required for the pumping of the heat transfer fluid) at different operating frequencies:

		Power at different
	Form of the magnetocaloric	operating frequencies (W)
	material	1 Hz	5 Hz	10 Hz
	Monoliths, square channels,	153.2	645.2	1024.6
	side length 0.1 mm
	Monoliths, square channels,	108.6	0*	0*
	side length 0.3 mm
	Spheres, d = 0.05 mm	96.1	522.2	986.1
	Spheres, d = 0.3 mm	90.1	259.1	0*
	N.B.:
	0* means that the power required for the pumping of the fluid is greater than the cooling power obtained.

Claims

1. A packed heat exchanger bed composed of thermomagnetic material particles which have a mean diameter in the range from 50 μm to 400 μm and give rise to a porosity in the packed bed of from 30 to 45%.

2. The heat exchanger bed according to claim 1, wherein the material particles have a mean diameter of from 50 μm to 200 μm.

3. The heat exchanger bed according to claim 1, wherein the material particles are in spherical form, pellet form, sheet form or cylinder form.

4. The heat exchanger bed according to claim 1, wherein the porosity of the packed bed is 36 to 45%.

5. A heat exchanger bed composed of a thermomagnetic material monolith which has continuous channels with a cross-sectional area of the individual channels of from 0.001 to 0.2 mm2 and a wall thickness of 50 to 300 μm, a porosity of from 10 to 60% and a ratio of surface to volume of from 3,000 to 50,000 m2/m3, or which has a plurality of parallel sheets with a sheet thickness of 0.1 to 2 mm and a sheet separation of 0.05 to 1 mm.

6. The heat exchanger bed according to claim 5, wherein the porosity is 20 to 30%.

7. The heat exchanger bed according to claim 5, wherein the cross-sectional area of the individual channels is from 0.01 to 0.03 mm2 and the wall thickness is from 50 to 150 μm.

8. The heat exchanger bed according to claim 1, wherein the thermomagnetic material is at least one selected from the group consisting of (1)-(8):

(1) at least one compound of the formula (I) (AyB1-y)2+δCwDxEz   (I),

 wherein

 A is Mn or Co,

 B is Fe, Cr or Ni,

 C, D and E at least two of C, D and E are different, have a non-vanishing concentration and each independently is selected from the group consisting of P, B, Se, Ge, Ga, Si, Sn, N, As and Sb, where at least one of C, D and E is Ge or Si,

 δ is a number of from −0.1 to 0.1,

 w, x, y, z each independently is from 0 to 1, wherein w+x+z=1;

(2) at least one La- and Fe-based compound of the formulae (II) and/or (III) and/or (IV) La(FexAl1-x)13Hy or La(FexSi1-x)13Hy   (II)

 wherein

 x is a number of from 0.7 to 0.95,

 y is a number of from 0 to 3; La(FexAlyCoz)13 or La(FexSiyCoz)13   (III),

 wherein

 x is a number of from 0.7 to 0.95,

 y is a number of from 0.05 to 1−x,

 z is a number of from 0.005 to 0.5; LaMnxFe2-xGe   (IV),

 wherein

 x is a number of from 1.7 to 1.95, and

(3) at least one Heusler alloy of the MnTP type, wherein T is a transition metal and P is a p-doping metal having an electron count per atom e/a of from 7 to 8.5,

(4) at least one Gd- and Si-based compound of the formula (V) Gd5(SixGe1-x)4   (V)

 wherein x is a number of from 0.2 to 1,

(5) at least one Fe2P-based compound,

(6) at least one manganite of the perovskite type,

(7) at least one compound which comprises at least one rare earth element and has the formulae selected from the group consisting of (VI) and (VII) Tb5(Si4-xGex)   (VI),

 wherein x=0, 1, 2, 3, or 4, XTiGe   (VII),

 wherein X=Dy, Ho, or Tm,

(8) at least one Mn- and Sb- or As-based compound of the formulae (VIII) and (IX) Mn2-xZxSb   (VIII) Mn2ZxSb1-x   (IX)

 wherein

 Z is Cr, Cu, Zn, Co, V, As, or Ge,

 x is from 0.01 to 0.5,

 wherein Sb may be replaced by As when Z is not As.

9. The heat exchanger bed according to claim 8, wherein the thermomagnetic material is at least one quaternary compound of the formula (I) which, in addition to Mn, Fe, P and optionally Sb, further comprises Ge; Si; As; Ge and Si; Ge and As; Si and As; or Ge, Si, and As.

10. A process for producing heat exchanger beds according to claim 1, comprising subjecting a powder of the thermomagnetic material to shaping to form the thermomagnetic material particles and subsequently packing the material particles to form the heat exchanger bed.

11. A process for producing heat exchanger beds according to claim 5 by extrusion, injection molding or molding of the thermomagnetic material to form the monolith.

12. A refrigerator, an air conditioning unit, a heat pump, or a thermomagnetic generator comprising the packed heat exchanger bed according to claim 1.