EP3123817B1 - Method of producing an infrared radiation - Google Patents

Description

The invention relates to a device for generating radiation in the infrared range, in which a radiation generator is electrically supplied and at least partially transforms the electrical supply energy into the infrared radiation.

It has been known for some time prior art, plastics or plastic composites for various technical applications, for example, as a base material for garments, as insulation material, etc. enforce. One of these widely used types of plastic is polyethylene terephthalate (PET). This PET plastic is a thermoplastic produced by polycondensation of the polyester family.

PET has a polar basic structure and strong intermolecular forces. PET molecules are also linear, i. built without networking. Due to the polar-linear structure, PET is characterized by semi-crystalline regions and fibers which cause high resistance to breakage and dimensional stability even in temperature ranges above 80 ° C. Thus, PET is generally suitable as a material for these temperature ranges.

PET materials are made from monomers such as terephthalic acid or benzene dicarboxylic acid and ethylene glycol or dihydroxyethane or ethanediol. In order to produce quantities that are relevant for industrial application, industrial production takes place by transesterification of dimethyl terephthalate with ethanediol. In the context of this equilibrium reaction produces an undesirable increase in amount of ethanediol, or it is necessary for the reaction that this substance is distilled off again by the reaction, in order to influence the equilibrium favorable. The alternative possible melt phase polycondensation is unsuitable for the production of large quantities, because this form of production takes too long periods of time. In order to achieve a high PET quality, a solid state polycondensation is connected downstream, depending on the intended use, in order to achieve a further condensation. Another known production possibility of PET is the esterification of ethanediol with terephthalic acid.

In general, the PET molecules are long-chain structures that consist predominantly of carbon, hydrogen and some other atoms. The molecules have a spiral to tangled arrangement. This leads to a large number of free spaces in the atomic region between the molecules, especially in the amorphous state. By axial or biaxial orientation of the material, these clearances can be reduced, which leads for example to a higher strength of the material and to a reduced gas permeability.

In addition to the use of PET in pure form, the material modification of the prior art is also known. As a base material for composite materials, other elements can be added to the thermoplastic resin. In its pure state, PET is essentially an electrical non-conductor. By incorporating, for example, metallic atoms into the free spaces between the molecules or by attaching, for example, metallic atoms to the PET molecules, the material can be imparted to a certain extent with electrically conductive properties. Correspondingly metallically doped PET fibers thus conduct an electric current when a voltage is applied.

Furthermore, it is known that various, predominantly metallic, materials such as e.g. Alloys with gadolinium or other rare earth metals, have a magnetocaloric effect. The magnetocaloric effect heats the material when it is exposed to a magnetic field, and it cools down when the magnetic field influence stops. The cause of this heating reaction is the alignment of the magnetic moments of the material by the magnetic field and their dependence on the magnetic field strength. The alignment speed of the magnetic moments creates heat. A possible application could be the use as a coolant, wherein a cooling effect can be achieved by periodic magnetization and simultaneous removal of the resulting heat.

The magnetocaloric effect is heavily hysteresis-dependent depending on the alloy. In order to realize the magnetocaloric effect also in connection with applications, which means a possibly additive mechanical load, alloys are sought, which combine these physical effects and properties. Another problem of the technical application of this effect In addition to the undesirable hysteresis behavior is the fact that so far this effect is relatively weak pronounced in known alloys and material compositions.

The skin effect, also known as current displacement, is an effect in electrical conductors through which higher-frequency alternating current flows, which makes the current density inside a conductor lower than in external areas. It occurs in relation to the skin depth thick conductors and also in electrically conductive shields and cable shields. The skin effect favors the transfer impedance of shielded lines and the screen attenuation of conductive shields with increasing frequency, but increases the resistance of an electrical line. This practically means that the skin depth, i. the Leitschichtdicke, material-dependent decreases with increasing AC frequency. As a result of high alternating current frequencies of more than 100 kHz, a skin depth of 0.21 mm is present within a copper line.

The DE 20 2012 009 083 U1 discloses a sub-molecular surface heating system, which consists of at least one support, wherein individual nano and pico metals in certain matrices, completely isolated in a surface structure of polyamide / polyester, polyaramid, polymer, ceramite and other plastic compounds, in Plates, foils or be introduced in railway conductors.

From the US 2006/000823 A1 and the WO 2008/0642515 are PTC thermistors with a positive temperature coefficient known, which are formed by incorporation of conductive particles, such as metals or metal coated glass spheres, in thermoplastics.

The WO 2009/133048 describes a variety of magnetocaloric materials, particularly Fe2P-based compounds and Heussler alloys of the MnTP type, wherein T represents a transition metal and P represents a p-doping metal.

The object of the present invention is to improve a device of the aforementioned type such that generation of the radiation is supported with high efficiency and within a narrow and precisely definable frequency band.

This object is achieved by a device according to claim 1, wherein the radiation generator comprises at least one fiber of plastic with electrical conductivity, wherein the fiber material is formed by a base material made of PET, which elements are incorporated and that the elements have an atomic size and are provided with a distance such that electron clouds overlap at least partially.

The doping elements can additionally impart the PET material with the capability of at least partially conducting electrical energy. On the one hand, the doping elements can generate properties as absorbers for radiant energy, on the other hand they can generate properties as electrical conductors. By incorporating, for example, metallic atoms into the free spaces between the molecules or by attaching metallic atoms, for example, to the PET molecules, the PET material can be given a certain amount of electrically conductive properties.

Correspondingly metallically doped PET fibers thus conduct an electric current when a voltage is applied. Depending on the electrical resistance of this composite material, this generates radiation or absorbs it as a function of the applied current. The effects are supported as a function of the previously described skin effect and by additive absorption of radiant energy. This means that the PET composite material according to the invention represents a new material alternative for the radiation absorption or radiation generation to the known metal fiber materials.

In addition, the mechanical properties of PET with regard to its breaking strength and dimensional stability are also exploited in temperature ranges above 80 ° C in order to open up areas of application with these increased mechanical requirements to the absorber material.

A further property of the absorber material according to the invention consists in its property, which is dependent on the respective doping elements, of being at least partially electrically conductive. In particular, when the PET composite material is a base material for any heat source of any kind, the physical effects of absorptivity and electrical conductivity can increase the amount of heat to be delivered combined and thus increased by the fact that in addition to the emitted heat radiation due to the radiation absorption by means of a voltage applied to the PET composite material voltage due to the electrical resistance of the material is additionally generated by electrical means heat energy.

A further interesting application of the PET composite material is opened by its property to realize the magnetocaloric effect and at the same time have the PET's own improved mechanical material properties. By means of suitable doping elements, it is thus also possible to impress cooling effect properties on the material according to the invention.

The teaching of the invention recognizes that the elements suitable for PET doping in particular MnFePhosphorverbindungen, MnFe (As, PwGexSiz) s; FeMn-phosphorus compounds with As, Si-phosphorus substitution possibly combined with La (FeMnP) AICo; Compounds with Mn-Zn are.

A preferred application is the use of the doping structural formula MnFe (As, PwGexSiz) s. This compound has high cooling capabilities at temperatures of 200 to 600 K, especially at 280 to 500 K. This compound shows a very strong magnetocaloric effect. The use of this compound is environmentally friendly due to the fact that the environmentally problematic substances, in particular the Mn molecules, are bound in the basic PET matrix. Very efficient results can be achieved when x = 0.3-0.7 and / or w less than 1-x and z = 1-x-w in its structural connection. Preferably, in this specific setting, the material is realized in a hexagonal Fe2P structure.

The preparation of the various material compositions can be carried out in a ball mill and under a protective gas atmosphere.

For example, an alloy of 5 g FeMnP 0.7 Ge 0.3 having a critical temperature of about 350 K can be prepared by mixing the pure elements having a quality of 3N in the following amounts: FeMnP 0.7 Ge 0.3. In a closed ball mill, these elements are milled under a protective atmosphere until an amorphous or microcrystalline product is obtained. Depending on the properties of the mill, such a product can be obtained within 20 minutes to a few hours. The Powder is then heated in a closed ampule in a protected atmosphere until a temperature of about 800 to 1050 degrees C is reached. Thereafter, this is tempered to a temperature of about 650 degrees C. The alloy crystallizes in a hexagonal Fe2P structure.

An alloy of 5 g FeMnP 0.5 Ge 0.5 having a critical temperature of about 600 K is prepared by mixing the pure elements having a quality of 3N in the following amounts: Fe = 1.72 g, Mn = 1.69 g, P = 0.476 g and Ge = 1.12 g. In a closed ball mill, these elements are milled under a protective atmosphere until an amorphous or microcrystalline product is obtained. Depending on the properties of the mill, such a product can be obtained within 20 minutes to a few hours. The powder is then heated in a closed ampule in a protected atmosphere until a temperature of about 800 to 1050 degrees C is reached. Thereafter, this is tempered to a temperature of about 650 degrees C.

The alloy also crystallizes in a hexagonal Fe2P structure.

An alloy of 5g FeMnP 0.5 Ge 0.1 Si 0.4 having a critical temperature of about 300 K is prepared by mixing the pure elements having a quality of 3N in the following amounts: Fe = 1.93 g, Mn = 1.90 g, P = 0.535 g, Ge = 1.251 g and Si = 0.388 g. In a closed ball mill, these elements are milled under a protective atmosphere until an amorphous or microcrystalline product is obtained. Depending on the properties of the mill, such a product can be obtained within 20 minutes to a few hours. The powder is then heated in a closed ampule in a protected atmosphere until a temperature of about 800 to 1050 degrees C is reached. Thereafter, this is tempered to a temperature of about 650 degrees C. The alloy also crystallizes in a hexagonal Fe2P structure.

An alternative embodiment is obtained by modifications of alloys of the starting materials rather than the pure elements - this is particularly advantageous when Si is used in the alloy. This is based on the fact that FeSi alloys are very stable and are obtained when pure Fe and Si are available in the mill.

An alloy of 10 g Fe0.86 Mn1.14 P0.5 Si0.35 Ge0.15, which has a critical temperature of 390 K, is obtained by mixing the pure elements having a quality of 3N and the alloy Fe2P having a quality of 2N (Alpha Aesar 22951), in the following amounts: Fe2P = 4.18 g, Mn = 4.26 g, P = 0.148 g, Si = 0.669 g and Ge = 0.742 g.

In a closed ball mill, these elements are milled under a protective atmosphere until an amorphous or microcrystalline product is obtained. Depending on the properties of the mill, such a product can be obtained within 20 minutes to a few hours. The powder is then heated (sintered) in a sealed ampule in a protected atmosphere until a temperature of about 800 to 1050 degrees C is reached. Thereafter, this is tempered to a temperature of about 650 degrees C. The present invention is not limited to the exemplary embodiment. The quantities can vary in many ways.

Fig. 1

den physikalischen Skin-Effekt anhand einer Diagrammdarstellung, d.h. die äquivalente Leitschichtdicke ö in mm verschiedener Metalle über der Wechselstromfrequenz f in kHz

Fig. 2

in einer zusammengestellten Darstellung das Absorptionsverhalten verschiedener Atmosphärengase in Abhängigkeit der Wellenlänge

Fig. 3

die Mikrostruktur von FeMnP0,5Si0,5,

In the drawings, the underlying effects of the invention and embodiments of the internal structure of the material are shown schematically. Show it:

Fig. 1

the physical skin effect on the basis of a diagram, ie the equivalent guide layer thickness δ in mm of different metals over the alternating current frequency f in kHz

Fig. 2

in a summarized representation the absorption behavior of different atmospheric gases as a function of the wavelength

Fig. 3

the microstructure of FeMnP0.5Si0.5,

FIG. 1 shows the physical effect of current displacement in near-surface edge layers of a current-carrying conductor based on a diagram, ie, the equivalent Leitschichtdicke δ in mm of different metals over the AC frequency f in kH.

FIG. 2 Illustrates in an assembled representation the absorption behavior of different atmospheric gases as a function of the wavelength.

FIG. 3 shows the known microstructure of FeMnP 0.5 Si 0.5.

These Heusler alloys often undergo a martensitic transition between the martensitic and austenitic phases, which generally occurs due to temperature induction and is first order. Ni2MnGa arrangements are ferromagnetic with a Curie temperature of 376 K and a magnetic moment of 4.17 ILB, which is largely confined to the Mn atoms and associated with the Ni atoms with a small momentum of about 0.3 IIB , As can be expected from its cubic structure, the initial phase has a low magnetocrystalline anisotropy energy (Ha = 0.15T). However, in its martensitic phase, the compound has much greater anisotropy (Ha = 0.8 T).

The martensitic transformation temperature is close to 220 K. This martensitic transformation temperature can be easily varied to about room temperature by changing the composition of the alloy to a stoichiometric alloy. The low-temperature phase evolves from the initial phase by a diffusionless, position-changing transformation towards a tetragonal structure, a = b = 5.90 A, c = 5.44 A. A martensite phase generally accommodates the stem associated with transformation (that is 6.56% of c for Ni2MnGa), through the formation of twin variants.

This means that a cubic crystal splits into two tetragonal crystallites that share a contact plane. These twins are packed together in matching orientations to the strain energy (much like the magnetization of a ferromagnet on different orientations by breaking up into domains to minimize the magnetostatic energy). The alignment of these twin variants by the movement of the twin boundaries leads to large macroscopic trunks.

In the tetragonal phase with higher magnetic anisotropy, an applied magnetic field can cause a change in strain, and therefore these materials can be used as actuators. In addition to this ferromagnetic shape memory effect, one can observe very close to the martensitic transition temperature that there is a large change in magnetization for low-level magnetic fields. This change in magnetization is also related to the magnetocrystalline anisotropy.

This change in magnetization, resulting in a moderate magnetic entropy change of a few J / molK, is enhanced when is implemented on a single crystal. If the composition is present in this material in such a way that the magnetic and structural transformation occurs at the same temperature and is tuned to the greatest magnetic entropy, changes are observed.

For magnetic applications, extremely large changes in length in the martensitic transition will lead to aging effects. It is known in magnetic shape memory alloys that often only single crystals are driven while polycrystalline materials spontaneously pulverize after several cycles. One can increase the temperature effects by pressure on the crystalline formations, but also aging effects and declination of the polycrystallines are then observed.

Fe2P-based compounds offer the opportunity to prevent ionization processes, the binary intermetallic compound Fe2P can be considered as a base alloy for a workable mixture of materials. This compound crystallizes in the hexagonal, non-point symmetric FeMnPhosphor structure, and has all the positive properties to be used as a transponder for home cooling systems.

Substitutions of Fe and / or Mn are conceivable with AS, Zi, Ni, Ge, Si. Fe occupies the 3g and 3f sides and p the 1b and 2c sides. This gives a stack of alternating P-rich and P-lean layers. The neutron diffraction reveals that the magnetic moment of the Fe on the 3g side is about 2my-B, while the momentum on the 3f side is about 1my-B. The hexagonal shape has poor opportunities to be recovered by aging as a magnetic source.

A significant reason for the electrically conductive properties of the PET fibers by the doping is that in the dielectric support structure of the polyester, although the metal particles are spatially separated from each other, but that the electron clouds of the metal particles overlap each other. The embedding of the doping elements in the polyester prevents decomposition processes and prevents external influences.

In particular, reoxidation, friction decomposition are avoided and flexibility is improved.

It can be achieved with respect to the radiation exactly fixed, sharply delimited and reproducible frequency responses.

In particular, with regard to the radiation emission, it is possible to achieve the generation of infrared radiation in the frequency range of 4.5 μm to 11.5 μm by suitable doping.

As an alternative to using PET fibers, it is also possible to use aramids. The production of the fibers can be carried out by means of electro-spinning method.

A typical diameter of the fibers is in the range 2 μm to 6 μm. The doping with the metal particles is preferably carried out in a gas plasma.

A typical fiber length is in the range of 2 cm to 4 cm.

Particularly suitable doping elements are the following chemical elements, either in the pure state or as an alloy. In particular, the use of rare-earth metals is considered. It is also possible, for example, to use iron, manganese, phosphorus, silicon, lanthanum, germanium, sodium, zinc or arsenic. In addition, aluminum, copper and / or nickel are also usable.

Alternatively, alkaline earth metals or alkali metals can be used as doping elements. Considered, for example, magnesium, calcium, sodium and potassium.

Claims (13)

1. A device for generating a radiation in the infrared region, in which a radiation generator is supplied electrically and the electric supply transforms at least partially to the infrared radiation, the radiation generator comprising at least one fibre of plastic having an electrical conductivity, the fibrous material being formed by a base material of PET or aramid in which elements are embedded, and the elements having an atomic size and being provided with a distance such that electron clouds overlap at least in sections, characterized in that the embedded elements are incorporated within the PET or aramid base material in an unequal density distribution, the elements in material cross-sectional regions having a skin effect being arranged so as to be less dense than in material cross-sectional regions having a current densification effect.
2. The device according to claim 1, characterized in that the embedded elements have current conduction proprieties such that the fibre is at least partially electrically conducting.
3. The device according to claim 1 or 2, characterized in that the embedded elements have magneto-caloric effects such that the fibre undergoes at least partially a temperature increase through the influence of a magnetic field.
4. The device according to any of the preceding claims, characterized in that the embedded elements in material cross-sectional regions near the surface of the equivalent conductive layer thickness δ are embedded in a higher density than outside this region.
5. The device according to any of the preceding claims, characterized in that the embedded elements are incorporated into the PET base material by doping.
6. The device according to any of the preceding claims, characterized in that the embedded elements are formed by MnFe phosphorous compounds.
7. The device according to any of the preceding claims 1 to 5, characterized in that the embedded elements are formed by MnFe(As,PwGexSiz)s.
8. The device according to claim 7, characterized in that the embedded elements have the following values: x=0.3-0.7 and, or w less than or equal to 1-x and z=l-x-w.
9. The device according to any of the preceding claims 1 to 5, characterized in that the embedded elements are formed by FeMn phosphorous compounds with As,Si-phosphorous substitution and in combination with La(FeMnP)AICo.
10. The device according to any of the preceding claims 1 to 5, characterized in that the embedded elements are formed by compounds comprising Mn-Zn.
11. The device according to any of the preceding claims 1 to 5, characterized in that the embedded elements are formed by an alloy comprising FeMnP0.7Ge0.3.
12. The device according to any of the preceding claims 1 to 5, characterized in that the embedded elements are formed by an alloy comprising FeMnP0.5Ge0.5.
13. The device according to any of the preceding claims 1 to 5, characterized in that the embedded elements are formed by an alloy comprising Fe0.86Mn1.14P0.5Si0.35Ge0.15.

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