DE10245088B3 - Powder-metallurgically produced soft magnetic molded part with high maximum permeability, process for its production and its use - Google Patents

Abstract

What is described is a magnetic molded part made of coated powder particles, the powder particles consisting of a ferromagnetic material, the powder particles being at least partially electrically insulated from one another by an insulation located between the powder particles and the molded part being mechanically solidified by annealing, a process for its production and its use ,

Description

The invention relates to a powder metallurgy manufactured soft magnetic molded part with high maximum permeability, and a Process for producing this molded part from metallic powder particles, wherein the powder particles with an electrical insulation layer be provided so that when using the molded part as a magnetic core in alternating fields, such as those in fast-switching Solenoid valves can occur the eddy current losses are low. The invention further relates to the use of this molding in dynamic applications such as for example as magnetic cores in solenoid valves in injection systems from Motor vehicles, as cores of ignition coils, as yokes in solenoid systems for valve control or as a rotor or Stator in motor applications.

• 1. ein maximaler spezifischer Widerstand, aus welchem minimale Wirbelstromverluste resultieren;
• 2. eine minimale Koerzitivfeldstärke, durch welche minimale Hystereseverluste bewirkt werden;
• 3. eine maximale Permeabilität;
• 4. ein maximaler Füllgrad mit Magnetmaterial, d.h. eine hohe Dichte, aus der eine maximale Sättigungspolarisation resultiert.

When developing soft magnetic powder composite materials of the type mentioned above, the following properties are optimized at the same time:

• 1. a maximum specific resistance, from which minimal eddy current losses result;
• 2. a minimal coercive field strength, by means of which minimal hysteresis losses are caused;
• 3. maximum permeability;
• 4. a maximum degree of filling with magnetic material, ie a high density, from which a maximum saturation polarization results.

In particular, the demands on the specific resistance and the coercive field strength can usually be difficult to agree with each other, since the necessary annealing for Reduction of the coercive field strength usually also a reduction in specific resistance leads.

However, studies show given coercivities the best level of resistance when you have relatively large values at the same time for permeability and density calls. It ensures a reduction in the coercive force while maintaining a high resistance levels.

The US 2,601,212 proposes a process for the production of soft magnetic powder composites for applications in the high frequency range in which phosphated carbonyl iron is mixed with 1 to 6% by weight of organosilanes as a binder. After pressing, the molded parts are cured at temperatures around 150 ° C. Annealing and thus decomposition of the organosilanes does not take place, which means that the organosilanes are polymerized and are present in the finished molded part as a binder polymer. The molded parts produced in this way are unsuitable for use frequencies below 10 kHz.

A method which takes this fact into account is in the DE 34 39 397 described. According to this process, powder particles which are provided with a phosphate insulation are subjected to annealing in an oxidizing atmosphere at a temperature of at most 600 ° C. The annealing treatment leads to a reduction in the coercive field strength of the iron and increases the strength of the molded part due to the formation of iron oxide between the powder particles.

A similar process with subsequent annealing shows that protection of the powder particles provided with a phosphate insulation while pressing using an organic resin layer is possible.

These known from the prior art Powder metallurgically manufactured molded parts are related to the maximum permeability, which is determined at 50 Hz and H = 10 A / cm, conventional inferior to soft magnetic alloy materials. In general, maximum permeabilities of up to 200 are achieved. For certain Applications of the molded parts, for example as core material in solenoid valves automotive engineering, however, is often a maximum permeability of at least 275 preferably greater than 300, he wishes.

Object of the present invention it is therefore a molded part with soft magnetic properties, higher maximum permeability, which is determined at 50 Hz and H = 10 A / cm, at the same time to provide high mechanical strength. Another job The present invention is to provide a soft magnetic powder metallurgically manufactured molded part with quick response, understood by a good response behavior according to the invention is that the frequency dependent maximum permeability a core of this material in the entire frequency band from 0 to 4 kHz is preferably at least 200.

According to the invention, the object is achieved by a powder-metallurgically produced molded part made of compressed and annealed soft magnetic phosphate-coated powder particles, the phosphate-coated powder particles having been coated with organofunctional silanes prior to annealing, the proportion by weight of the organofunctional silanes being between 0.1 and 3% by weight of the unannealed molding and after the annealing the molded part does not contain any polymerized organosilanes, characterized by a specific resistance ρ ≥ 10 μΩm, a coercive field strength H _c ≤ 3.0 A / cm, hysteresis losses W _H ≤ 0.1 J / kg with a modulation of B = 1 Tesla, a maximum permeability (measured at f = 50 Hz)> 275 and a density γ ≥ 7.1 g / cm ³ .

The essential idea of the present invention lies on the one hand in the insulating effect of the material and on the other hand in the lubricating effect of the silane layer. The latter results from the fact that the organofunctional silane is not polymerized out to siloxane like that in the above US 2,601,212 the case is. This would take place at temperatures of approx. 100-150 ° C, but the powder is only dried at approx. 50 ° C during the coating process. The subsequent annealing of the pressed parts then leads to polymerization, but the resulting siloxanes are not very temperature-resistant, so that they are destroyed above approx. 200 ° C. Essentially SiO ₂ remains in the material.

Overall, it has been shown that a glow, in which the organosilanes are decomposed, suitable after pressing is to reduce said losses. For the most effective healing possible of crystalline defects and to promote grain growth would be in themselves preferably high temperatures in the range of approximately 1100 ° C. are desirable. However, at this temperature is that on the surface of the powder particles Phosphate insulation destroyed become.

Due to the lubricating effect of unpolymerized silane layer of the powder before pressing the proportion of the pressing aid can be significantly reduced. Typically, pressing aids are used in an amount of approx. 0.5 % By weight added. This proportion can be reduced to 0.25 or 0.125% by weight or even 0% by weight can be reduced. This is beneficial for the resulting density of the material and for the specific total power loss (in W / kg).

This consists of the hysteresis losses and the eddy current losses: p Fe = p H + p W (1)

A proportional dependence of the hysteresis power loss on the frequency applies: p H = W H ⋅f (2)

The eddy current losses in turn contain two parts. On the one hand, the eddy currents flow within the powder particles, on the other hand also over the entire part volume: p W = p WP + p WV (3)

(geometrieabhängiger Vorfaktor z, Durchmesser d, spez. Widerstand ρ_el, Dichte γ, Induktion B mit Exponenten q, Frequenz f)The following generally applies to the calculation of the eddy current power loss:

(geometry-dependent pre-factor z, diameter d, specific resistance ρ _el , density γ, induction B with exponent q, frequency f)

The pre-factor applies to the eddy current power loss within the powder particles (average diameter d) z = π 2 / 20 (according to K. Honma and N. Hirano, R&D 2, 40-42 (1980)). The values for pure iron should be used for the resistance and density (γ _Fe = 7.87 g / cm ³ and ρ _Fe = 0.1 μΩm).

For the calculation of the eddy current power loss over the entire part volume, the examined ring geometry is approximated with a toroidal shape. You get the pre-factor z = π 2 / 16 (after RM Bozorth, Ferromagnetism, IEEE Press, NewYork, 1993). You also need the iron diameter D of the toroid and the macroscopic density. If the measured hysteresis losses and resistances are taken as a basis, the following equation results for the total power loss (with a modulation of B = 1 T):
p Fe ≤ W H × f + 627 (Ws 2 ) / (Kgm 2 ) × d 2 × f 2 + c × D 2 × f 2
with the upper limit for the hysteresis losses W _H ≤ 0.14 J / kg.

While the annealing treatment the organofunctional silanes settle in their respective Reaction products arising reaction conditions around. Examples for such Reaction products are silicon oxides and silicon carbides.

It has surprisingly been found that molded parts, the powder part isolated in a known manner Chen, for example powder particles isolated by means of phosphates, can be further improved by using organofunctional silanes. The properties of the molded part according to the invention also improve compared to an insulation layer formed exclusively by the use of a substance containing silicon.

The moldings according to the invention have all known moldings with comparable high mechanical strength a higher one maximum permeability on.

The maximum permeability is according to the invention determined at H = 10 A / cm and f = 50 Hz.

Description of the method of determination the maximum permeability.

On an isolated ring of the sample with dimensions 33 × 20 × 6 mm ² (outer / inner diameter / height) a primary winding with 100 turns and a secondary winding with 20 turns are applied. The field is excited by means of a sinusoidal voltage with adjustable frequency. The induction voltage on the secondary winding is determined with a voltmeter.

The maximum permeability is in generally by varying the strength of the field and searching of the permeability maximum determined on the new curve. As a rule, the maximum permeability of the molded part according to the invention lies however at about H = 10 A / cm, so that the indication of the permeability at this Magnetic field of maximum permeability with sufficient agreement equivalent.

The values according to the invention for the maximum permeability at 50 Hz essentially correspond to the value of the maximum permeability in static Field.

The maximum permeability of the molded parts according to the invention in the quasi-static field at f = 50 Hz is preferably at least 275, in particular at least 300. Are very particularly preferred Moldings with maximum permeabilities of more than 400, especially 480.

In the entire frequency band from 0 and is up to 4 kHz the maximum permeability preferably at least 200. It is particularly preferred if the maximum permeability between 0 to 4 kHz above 300, in particular 350. All those molded parts whose maximum permeability between are particularly preferred 0 and 4 kHz is above 400.

For certain applications it is desirable if the frequency dependent permeability the moldings according to the invention in the range from 0 to 4 kHz with a higher modulation of B = 1 D (H> 10 A / cm) preferably is great.

The frequency-dependent permeability at high Level (1 T) is for the Moldings according to the invention preferably at least 200, in particular 250.

The flexural strength of the molded parts according to the invention, which is determined by the method described below, is preferably at least 30 N / mm ² . Values of more than 50 N / mm ² , in particular 60 N / mm ² , are particularly preferred. Those molded parts according to the invention which have a bending strength of more than 80 N / mm ² are very particularly preferred.

The ferromagnetic used according to the invention Material is preferably iron, cobalt iron, nickel iron or Silicon-iron, which is used in the form of a powder. Although for the ferromagnetic Material one if possible high purity is preferred, low production-related Impurities practically unavoidable. The ferromagnetic according to the invention Contains material therefore small amounts of impurities such as nitrogen, Oxygen, sulfur or carbon. The carbon content is preferably below 0.1%, in particular below 0.03%. The nitrogen content is preferably below 0.01%, in particular below 0.003%, examples for usable according to the invention commercially available Iron powders are those with the designations "AT40.29", "ASC100.29" and "ABC100.30" from Höganäs AB, Sweden.

A value of at least about 50 μm is preferably expedient for the particle size (d ₅₀ ) of the powder particles. In general, larger particles also lead to higher maximum permeabilities. An upper limit can expediently be specified at 400 μm.

When optimizing the molded parts according to the invention for one high permeability with a modulation of about B = 1 T is a range from 50 to 200 μm in particular preferred because an upper limit due to the occurring in the alternating field Eddy current losses are given. To achieve a high maximum permeability is a Range of more than 200 to about 400 microns is particularly preferred.

The coercive field strength of the Moldings according to the invention is preferably 1 to 3 A / cm.

Step in an alternating magnetic field in the molding according to the invention electrical losses, which essentially result from hysteresis losses and eddy current losses. As a rule, the losses increase at higher Frequencies. Under losses in the sense of the invention, the Total losses understood from all measured losses.

The losses at B = 1 T and f = 1 kHz of the molded parts according to the invention are preferably in a range from 80 to 450 W / kg. Especially Preferred are molded parts according to the invention which have losses of less than 250 W / kg at B = 1 T and f = 1 kHz. All Shaped parts whose losses are below 160 are particularly preferred W / kg.

The losses are measured on a toroidal core measuring 33 × 20 × 6 mm ² with n ₁ = 170 and n ₂ = 20 performed.

The specific resistance of the molded parts is preferably greater than 500 μΩm.

• – Behandlung eines Pulvers aus einem ferromagnetischen Material mit einer Phosphatkomponente
• – Behandlung mit einer weiteren Komponente enthaltend organofunktionelle Silane oder Behandlung des Pulvers mit einer Komponente, die sowohl Phosphate als auch organofunktionelle Silane enthält,
• – Ggf. Zugabe von Presshilfsmitteln, Bindern, Harzen oder Gleitmitteln,
• – Pressen des behandelten Pulvers zu einem Grünling und
• – Glühung des Grünlings zu einem mechanisch verfestigten Formteil.

The invention also relates to a method for producing a magnetizable molded part comprising the steps:

• - Treatment of a powder made of a ferromagnetic material with a phosphate component
• Treatment with a further component containing organofunctional silanes or treatment of the powder with a component which contains both phosphates and organofunctional silanes,
• - Possibly. Addition of pressing aids, binders, resins or lubricants,
• - pressing the treated powder into a green compact and
• - Annealing the green body to a mechanically solidified molded part.

wobei X eine leicht hydrolysierbare Gruppe ist und R für einen organischen Rest steht, enthalten.The organofunctional silanes which can be used are substances which are preferably building blocks of the general formula

where X is an easily hydrolyzable group and R represents an organic radical.

Examples of easily hydrolyzable groups are Cl, OCH ₃ , OCH ₂ H ₅ or OCH ₂ CH ₂ OCH ₃ ,

Suitable organic radicals are, for example Hydrogen or aliphatic or aromatic radicals with 2 to 10 carbon atoms that can be either unsubstituted or partially substituted. Suitable substituents are, for example, F, Br, I or preferably chlorine. Preferably unsubstituted organic residues are used.

The organofunctional used Substances containing silanes are, for example, vinyl silanes, such as vinyltrichlorosilane, vinyltriethoxysilane, vinyltrimethoxysilane, Vinyl-tris- (β-metoxyethoxy) silane or vinyl triacetoxysilane, aminosilanes, such as γ-aminopropyl-triethoxysilane, γ-aminopropyl-trimethoxysilane, N-β- (aminoethyl) -γ-aminopropyl-trimethoxysilane or N-β- (aminoethyl) -γ-aminopropyl-trimethoxysilane or N-β- (aminoethyl) -N- (β-aminoethyl) -γ-aminopropyl-trimethoxysilane, Ureisosalkylsilane, epoxyalkylsilanes, such as β-glyxidyloxypropyl-trimethoxysilane, Methacrylic alkyl silanes, such as γ-methacryloxypropyl trimetoxysilane or γ-methacryloxypropyl-tris (β-methoxyethoxy) silane or mercaptoalkysilanes, such as γ-mercaptopropyl-trimethoxysilane or γ-mercaptopropyl-triethoxysilane.

The proportion by weight of organofunctional Silanes are preferably in the range of 0.1 to 3% by weight, in particular 0.25 to 2% by weight.

Common lubricants are preferably used in the molded parts available to improve the density. Examples of suitable ones Lubricants are calcium, lithium, magnesium, zinc and stearate Stearic acid. In principle, other lubricants are also conceivable, as long as they supportive of the pressing process act and do not adversely affect the flowability of the powder.

Preferably as a lubricant Lithium stearate, stearic acid or Ca stearate used in an amount which on the one hand supports the pressing process sufficiently, on the other hand however, still leads to high maximum permeabilities. The weight percentage is preferably in the range from 0 to 5% by weight, in particular between 0 and 0.6% by weight.

The powders which can be used according to the invention can be annealed (pretreated) or not annealed be used. If the powders are used annealed, there is one reducing atmosphere, especially a hydrogen-containing atmosphere, preferred.

The powder is treated in a manner known per se, as for example in W. Rausch et. al, "The phosphating of Metallen ", 2nd edition, Eugen Leuze Verlag, Saulgau (1988).

The powder particles can be used as the outer layer a thermoplastic or thermoset are applied, which before Press to a green body hardened However, preferably no thermoplastic or thermoset is applied.

The pressing process can either at Room temperature or at a temperature above room temperature (Hot pressing). When hot pressing, there are temperatures of at least 80 ° C prefers.

Preferably, the annealing of the green compact in an oxidizing atmosphere, such as air or humidified hydrogen.

The green body is preferably annealed a temperature of at least 500 ° C instead. The temperature is capped by the temperature at which the insulation layer becomes ineffective. For the insulation means used is preferably this limit around 680 ° C. It can help increase Strength can be advantageous, the annealing at different temperature levels perform.

It is possible to carry out the silane treatment before or after the phosphating treatment. However, the phosphating is preferably carried out before the silane treatment. The phosphates can be used in aqueous or non-aqueous solution.

In a further preferred embodiment, it is also possible to carry out the phosphate coating and silane coating in one operation. It has been shown that the powder particles are analogous to those in the DE-A1-4 403 876 described method for passivation of metallic surfaces can be coated by screws. In this method, the silane or polysiloxane contains built-in phosphorus-oxygen assemblies, which can preferably be built in as intermediate links in polysiloxane chains (SI-O-Si-OPP-Si -...). The atomic ratio P: SI in the siloxane layer is preferably greater than 0.01.

The moldings according to the invention can each have an open residual porosity after manufacturing conditions, which is disadvantageous on the corrosion resistance can impact. To improve corrosion protection is preferred the molded part after annealing a vacuum impregnation with liquid Resin and subsequent hardening subjected. Suitable resins are known crosslinking or thermoplastic resins such as anaerobic methacrylate resins. The penetration of the resin into the molding can be done with the help of Pressurized gas promoted become. Suitable pressures are expedient in the range of 0.3 to 3.0 MPa In this way oil and petrol resistant Manufacture molded part with good temperature resistance up to about 250 ° C.

The present invention further encompasses the use of the molding according to the invention in solenoid valves, as cores of ignition coils or as yokes in Magnetic systems for valve control or as a rotor or stator in Motor applications or other electrical machines.

• 1 die Frequenzabhängigkeit der Maximalpermeabilität von Proben gemäß Herstellung nach den Beispielen 1, 3, 4, 6, 7, und 8,
• 2 die Frequenzabhängigkeit der Maximalpermeabilität von Proben gemäß Herstellung nach den Beispielen 1 und 10–19 und
• 3 die Frequenzabhängigkeit der Maximalpermeabilität von Proben gemäß Herstellung nach den Beispielen 20 und 21 mit variierter Aussteuerung des Ringkerns.

The invention is explained in more detail below with reference to exemplary embodiments shown in the drawing figures. It shows:

• 1 the frequency dependence of the maximum permeability of samples according to the production according to Examples 1, 3, 4, 6, 7 and 8,
• 2 the frequency dependence of the maximum permeability of samples according to the preparation according to Examples 1 and 10-19 and
• 3 the frequency dependence of the maximum permeability of samples according to the production according to Examples 20 and 21 with a variable modulation of the toroid.

Example 1 (comparison)

Manufacture of cores with phosphate insulation in aqueous solution

200 g of iron powder (AT 40.29, Höganäs) with an average particle size d ₅₀ = 265 μm and a C or N content of about 0.003% and an O content of about 0.081% was etched onto HCl and with a treated aqueous solution for phosphating.

The solution was prepared the commercially available Phosphating Novaphos® F 2311 (Novamax) dissolved in water (15 g F 2311 per liter of water) and the solution at 57 ° C with sodium hydroxide solution to a pH set from 5.0. Subsequently the iron powder was mixed with 1 liter of the solution. After 5 min the reaction by rinsing stopped with water and the powder dried at 130 ° C in air.

The powder was then mixed with an epoxy resin which was flexible after curing (Epikote® EP 1055, Shell; softening temperature 90-95 ° C., density: 1.19 d / cm ³ ). The resin was used in the form of a 20% acetone solution and added to the powder in an amount of 2.5 g per 100 g powder (0.5% EP 1055). The mixing time was 30 minutes. The solvent was then evaporated in vacuo.

Before pressing was used as a lubricant 0.5% by weight of calcium stearate was added and mixed in for about 30 minutes.

The powder so produced was in a non-directional press with a pressure of 600 MPa with an outer diameter of 33 mm, inner diameter of 20 mm and a height of 6 mm pressed. Finally there was a glow in 2 stages, initially 1 h at 600 ° C alternate air / vacuum and then 1 h at 520 ° C in air.

Example 2 (comparison)

Non-aqueous phosphating

The production corresponds Example 1 with the following difference:

1000 g of iron powder according to Example 1 are reaction mixed with 80 g of acetone and 3.37 g of H ₃ PO ₄ and 1 g of H ₂ O for 30 min and dried at room temperature under vacuum.

The maximum permeability over the frequency of this sample is in 1 (AT 40.29 OF) and 2 (AT 40.20 OF / 0.5% EP 1055 =, 5% Ca RT).

Examples 3 to 5

Phosphate and silane treatment

According to Example 2, iron powder was provided with a phosphate layer and then coated with different organofunctional silanes. Silane compounds used:

From these silane compounds different solutions the composition 4 g silane, 95 g isopropanol and 1 g aqua dest manufactured.

To form the silane layer were the phosphated Fe powder with the silane solution in proportion 0.5 g of silane mixed per 100 g of iron powder and reaction mixed for 1 h. The mixtures were then dried in vacuo at 150 ° C. for 1.5 h.

Then the powders were made accordingly Example 1 processed into cores.

The measured maximum permeability is in 1 shown.

Examples 6 to 8

Variation of the silane content

Cores according to Examples 3 to 5 with different silane contents were produced.

1 shows the maximum permeability of the cores produced as a function of the frequency of the magnetic field compared to samples without the addition of organofunctional silanes (AT 40.29 OF).

Examples 10 to 19

Variations in the lubricant and the pressing temperature

Cores were produced in accordance with Examples 3 and 9, in which 0.5% of a lubricant was added to the powders before pressing. The powders were pressed either at room temperature (RT) or at 150 ° C.

The maximum permeability of the nuclei as a function of the frequency of the applied field is in 2 shown.

Table 1 shows the measured values of the maximum permeability at a frequency of the applied field of f = 50 Hz for the examples 10, 11 and 13-19 summarized.

Example 20

5 kg of the powder AT 40.29 (Höganäs) with d ₅₀ = 265 μm were phosphated with 15 g of H ₃ PO ₄ and acetone in a mixer. The acetone was then pumped off. After adding 50 g of silane A187 with isopropanol and water, the mixture was mixed again and pumped off. The powder obtained was mixed with 0.5% Li stearate in a tumble mixer. Rings were produced in accordance with Example 1.

The maximum permeability (H = 10 A / cm) was 440.

The frequency dependence of the maximum permeability and the permeability at B = 1 T shows 3 ,

Example 21

According to Example 20, further rings were produced, but by using a powder with d ₅₀ = 120 μm (ABC100.30, Höganäs).

At f = 3 kHz and an induction B = 1 T (higher modulation compared to example 20), a permeability of 304 is achieved. The frequency dependence of the maximum permeability and the permeability at B = 1 T is in 3 shown.

Flexural strength measurement

In order to determine the bending strength of the cores, parallelepiped-shaped bars with dimensions l _s = 40 mm, b = 10 mm, h = 4 mm were pressed analogously to the examples above.

The measurement was carried out in the usual way by placing the rod at two points with a distance of 15 mm and applying a downward force in the middle between these points. From the measured bending force F _B is the bending strength _B s is calculated by the following formula:
S B = 1.5 × (F B × l s ) / (wxh 2 )

The flexural strength was measured in each case on 3 similar samples and the mean value was determined from the values for s _B. The results of the measurements are shown in Tab. 2.

The examples show that by the use of organofunctional silanes the permeability of powder cores elevated can be. Especially in the frequency range up to 4 kHz and above shows a significant improvement over known powder cores (AT 40.29 OF).

2. Gruppe

3. Gruppe

Furthermore, three further groups of exemplary embodiments are presented. Two exemplary embodiments are listed below for each group. All powders (partially pre-annealed) were coated, pressed and annealed in accordance with the present invention. The manufacturing parameters and the resulting properties are listed in the tables below. 1st group

2nd group

3rd group

All data from the three listed above Groups refer to averages of measurements on three each Wrestling or five Bars.

The resistors were on bars oxidized surface measured. The oxidation results from the annealing, because of the very low Porosity of the material (high density) there is only a thin oxide layer.

The oxide layer is a better one electrical conductor as the actual powder composite. When measuring resistance over the bar length there is therefore a parallel connection of a thin oxide layer (less spec. Resistance) and powder composite material (high specific resistance) in front. The measured values of the spec. There is resistance for the entire staff smaller than the spec. Resistance for the actual powder composite.

Claims (20)

Powder metallurgically produced molded part from compressed and annealed soft magnetic phosphate-coated powder particles, the phosphate-coated powder particles having been coated with organofunctional silanes prior to annealing, the proportion by weight of the organofunctional silanes being between 0.1 and 3% by weight of the unannealed molded part and the molded part after Annealing does not contain polymerized organofunctional silanes, characterized by a specific resistance ρ ≥ 10 μΩm, a coercive field strength H _c ≤ 3.0 A / cm, hysteresis losses W _H ≤ 0.14 J / kg (with a modulation of B = 1 T), a maximum permeability (measured at f = 50 Hz)> 275 and a density γ ≥ 7.1 g / cm ³ . Molding according to claim 1, characterized in that the specific Resistance ρ ≥ 200 μΩm. Molding according to claim 2, characterized in that the specific Resistance ρ ≥ 750 μΩm. Shaped part according to one of claims 1 to 3, characterized in that the hysteresis losses W _H ≤ 0.115 J / kg with a modulation of 1 Tesla. Molding according to claim 4, characterized in that the hysteresis losses W _H ≤ 0.110 J / kg with a modulation of 1 Tesla. Shaped part according to one of claims 1 to 5, characterized in that the loss factor is c ≤ 1.00 (Ws ² ) / (kgm ² ). Shaped part according to claim 6, characterized in that the loss factor is c ≤ 0.50 (Ws ² ) / (kgm ² ). Shaped part according to one of claims 1 to 7, characterized in that that the frequency dependent maximum permeability at 10 A / cm in the entire frequency band from 0 to 4 kHz at least Is 200. Shaped part according to one of claims 1 to 8, characterized in that the bending strength is at least 30 MPa. Molding according to one of claims 1 to 9, characterized in that the powder particles consist of iron, nickel iron, cobalt iron or silicon iron with an average particle size d ₅₀ > 50 microns. Molding according to one of claims 1 to 10, characterized in that the powder particles consist of water-atomized iron. Molding according to one of claims 1 to 8, characterized in that the particle size d _{50 of} the powder particles is in the range from about 50 to about 400 microns. A method for producing a magnetizable molding comprising the steps: - treatment a powder of a ferromagnetic material with a phosphate component, - treatment with another component containing organofunctional silanes or treating the powder with a component that contains both phosphates as well as organofunctional silanes, - pressing the treated powder to a green body and - annealing the green compact above the decomposition temperature of the organofunctional silanes to a mechanically solidified molded part. A method according to claim 13, characterized in that the organofunctional silanes are building blocks of the general formula

where x is an easily hydrolyzable group and R represents an organic radical. A method according to claim 13 or 14, characterized in that the glow in an oxidizing atmosphere or carried out under protective gas becomes. Method according to one of claims 13 to 15, characterized in that that the glow of the green body takes place at a temperature of at least 400 ° C. Method according to one of claims 13 to 16, characterized in that that the phosphating is carried out before the silane treatment. Method according to one of claims 13 to 16, characterized in that that the phosphating and silane treatment in one step carried out becomes. Method according to one of claims 13 to 18, characterized in that that the molding after annealing a vacuum impregnation with liquid Resin is subjected. Use of the molding according to claim 1 in solenoid valves as Cores of ignition coils or as yokes in solenoid systems for valve control or as a stator or rotor in electrical machines.