Process for producing a soft magnetic alloy

Abstract

A method for producing a soft magnetic alloy, comprising: Providing a precursor product comprising a composition consisting essentially of 5 wt.% ≤ Co ≤ 25 wt.% 0.3 wt.% ≤ V ≤ 5.0 wt.% 0 wt.% ≤ Cr ≤ 3.0 wt% 0 wt.% ≤ Si ≤ 3.0 wt% 0 wt.% ≤ Mn ≤ 3.0 wt% 0 wt.% ≤ Al ≤ 3.0 wt% 0 wt.% ≤ Ta ≤ 0.5 wt% 0 wt.% ≤ Ni ≤ 0.5 wt% 0 wt.% ≤ Mon ≤ 0.5 wt% 0 wt.% ≤ Cu ≤ 0.2 wt% 0 wt.% ≤ Nb ≤ 0.25 wt% 0 wt.% ≤ Ti ≤ 0.05 wt% 0 wt.% ≤ Ce ≤ 0.05 wt% 0 wt.% ≤ Ca ≤ 0.05 wt% 0 wt.% ≤ Mg ≤ 0.05 wt% 0 wt.% ≤ C ≤ 0.02 wt% 0 wt.% ≤ Zr ≤ 0.1 wt.% 0 wt.% ≤ O ≤ 0.025 wt% 0 wt.% ≤ S ≤ 0.015 wt% The remainder is iron, wherein Cr+Si+Al+Mn ≤ 3.0 wt.%, and up to 0.2 wt.% of other melt-related impurities, and which has a cold-rolled texture or a fiber texture, wherein the precursor product has a phase transition from a BCC phase region, into a BCC / FCC mixed region to an FCC phase region, wherein with increasing temperature the phase transition between the BCC phase region and the BCC / FCC mixed region occurs at a first transition temperature T Ü1 and with further increasing temperature the transition between the BCC / FCC mixed region and the FCC phase region at a second transition temperature T Ü2 takes place, where T Ü2 > T Ü1 and the difference T ü2 - T ü1 is less than 45K, final heat treatment of the precursor product at a temperature T 1 and then cooling from T 1 to room temperature at a rate of 25°C / h to 500°C / h, and then heating from room temperature to T 2 , where the precursor of T 2 is cooled to room temperature at a rate of 10°C / h to 50,000°C / h, where T 1 above T Ü2 lies and T 2 below T Ü1 where 940°C ≤ T 1 < T m , and 700°C ≤ T 2 ≤ 1050°C, where T 2 < T 1 is and T m is the solidus temperature, with the precursor at T 2 for a time t 2 heat treated, where 30 minutes ≤ t 2 ≤ 20 hours.

Description

[0001] The present invention relates to a soft magnetic alloy, in particular a highly permeable soft magnetic alloy.

[0002] Non-grain-oriented electrical steel with approximately 3 wt% silicon (SiFe) is the most widely used crystalline soft magnetic material in laminated cores for electrical machines. As electromobility advances, more efficient materials are needed that offer superior performance compared to SiFe. This means, in addition to a sufficiently high electrical resistance, a higher induction level is particularly desirable for achieving high torques and / or a small footprint.

[0003] Even more efficient materials are desirable for use in certain technologies, such as the automotive industry and electromobility. Soft magnetic cobalt-iron alloys (CoFe) are also used in electrical machines due to their exceptionally high saturation induction. Commercially available CoFe alloys typically have a composition of 49 wt.% Fe, 49 wt.% Co, and 2% V. With such a composition, a saturation induction of approximately 2.35 T is achieved while maintaining a high electrical resistance of 0.4 µΩm. However, it is desirable to reduce the material and manufacturing costs for CoFe alloys, which arise, for example, due to the high Co content, the additional manufacturing steps, and the scrap content.

[0004] US 4 204 887 A discloses an alloy with high damping capacity containing 1-45 wt.% Co and the balance Fe and, as the case may be, further 0.01-30% in total as an additional component of at least one of Ni, Cr, Al, Cu, Mn, Sb, Nb, Mo, W, Ti, V, Ta, Si, Sn, Zn, Zr, C and Y.

[0005] DE 11 80 954 A discloses a method for producing a CoFe alloy. WO 01 / 00 895 A1 discloses an Fe-based alloy with 10-20 wt.% Co, 2 to 6.5 wt.% Cr, Mo, and V, with less than 0.4 wt.% Ni and Mn, and less than 0.02 wt.% C.

[0006] US 7 128 790 B2 discloses an FeCo alloy with, in weight percent, 10 to 22% Co, traces up to 2.5% Si, traces up to 2% Al, 0.1 to 1% Mn, traces up to 0.0100% C, total O, N and S content in the range from traces to 0.0070%; total content of Si, Al, Cr, Mo, V, Mn in the range between 1.1 and 3.5%, total Cr, Mo and V content in the range from traces to 3%, total Ta and Nb content in the range from traces to 1%, the remainder being iron and production-related impurities.

[0007] US 2011 / 0 050 376 A1 discloses a laminated core made of soft magnetic individual sheets. DE 10 2008 039 326 A1 discloses a method for insulating electrical steel.

[0008] The task to be solved is therefore to provide a FeCo alloy that has lower material costs and is at the same time easy to process in order to reduce the manufacturing costs of the alloy up to the laminated core, while at the same time enabling a high power density.

[0009] The solution is the subject of the independent claims. Further advantageous developments are the subject of the respective dependent claims.

[0010] A soft magnetic alloy is provided, in particular a highly permeable soft magnetic FeCo alloy, which essentially consists of 5 wt.% ≤ Co ≤ 25 wt% 0.3 wt.% ≤ V ≤ 5.0 wt% 0 wt.% ≤ Cr ≤ 3.0 wt% 0 wt.% ≤ Si ≤ 3.0 wt% 0 wt.% ≤ Mn ≤ 3.0 wt% 0 wt.% ≤ Al ≤ 3.0 wt% 0 wt.% ≤ Ta ≤ 0.5 wt% 0 wt.% ≤ Ni ≤ 0.5 wt% 0 wt.% ≤ Mon ≤ 0.5 wt% 0 wt.% ≤ Cu ≤ 0.2 wt% 0 wt.% ≤ Ce ≤ 0.05 wt% 0 wt.% ≤ Nb ≤ 0.25 wt% 0 wt.% ≤ Ti ≤ 0.05 wt% 0 wt.% ≤ Ca ≤ 0.05 wt% 0 wt.% ≤ Mg ≤ 0.05 wt% 0 wt.% ≤ C ≤ 0.02 wt% 0 wt.% ≤ Zr ≤ 0.1 wt% 0 wt.% ≤ O ≤ 0.025 wt% 0 wt.% ≤ S ≤ 0.015 wt% The remainder is iron, with Cr+Si+Al+Mn ≤ 3.0 wt% and up to 0.2 wt% of other impurities. The alloy has a maximum permeability µ max ≥ 5,000, preferably µ max ≥ 10,000, preferably µ max ≥ 12,000, preferably µ max ≥ 17,000. Other impurities include B, P, N, W, Hf, Y, Re, Sc, Be, and other lanthanides except Ce.

[0011] Due to the lower Co content, the raw costs of the alloy are reduced compared to an alloy based on 49 wt.% Fe, 49 wt.% Co, 2% V. An FeCo alloy is created with a maximum cobalt content of 25 wt.%, which offers better soft magnetic properties, in particular, significantly higher permeability, than other FeCo alloys with a maximum cobalt content of 25 wt.%, such as existing and commercially available FeCo alloys such as VACOFLUX 17, AFK 18, or HIPERCO 15. These existing and commercially available alloys have a maximum permeability below 5000.

[0012] The alloy exhibits no significant ordering, so unlike alloys with over 30 wt.% Co, this alloy can be cold-rolled without a prior quenching process. Quenching is difficult to control, especially with large quantities of material, because sufficiently rapid cooling rates are difficult to achieve, allowing ordering to occur, resulting in embrittlement of the alloy. The absence of an order-to-disorder transition in the alloy thus simplifies large-scale production.

[0013] A significant order-to-disorder transition, such as that observed in CoFe alloys with a Co content of more than 30 wt.%, can be detected for an alloy using DSC (differential scanning calorimetry) measurements, as it results in a peak in the DSC measurement. Such a peak is not detected for the alloy in a DSC measurement under the same conditions.

[0014] At the same time, this new alloy offers significantly lower hysteresis losses than previously known and commercially available alloys with Co contents between 10 and 30 wt.%, as well as higher saturation and a significantly higher permeability level never before achieved for such alloys. The FeCo alloy can also be produced cost-effectively on an industrial scale.

[0015] Due to its higher permeability, the alloy can be used in applications such as the rotor or stator of an electric motor to reduce the size of the rotor or stator, and thus the electric motor, and / or increase its performance. For example, higher torque can be generated with the same size and / or weight, which would be advantageous for applications in electric or hybrid-powered vehicles.

[0016] In addition to a maximum permeability µ max≥ 5,000, preferably µ max ≥ 10,000, preferably µ max ≥ 12,000, preferably µ max ≥ 17,000 the alloy can have an electrical resistance p ≥ 0.25 µΩm, preferably p ≥ 0.30 µΩm, and / or hysteresis losses P Hys ≤ 0.07 J / kg preferably hysteresis losses P Hys ≤ 0.06 J / kg preferably hysteresis losses P Hys ≤ 0.05 J / kg, each at an amplitude of 1.5 T, and / or a coercive field strength H c of ≤ 0.7 A / cm preferably a coercive field strength H c of ≤ 0.6 A / cm preferably a coercive field strength H c of ≤ 0.5 A / cm preferably H c of ≤ 0.4 A / cm, preferably H c of ≤ 0.3 A / cm and / or induction B ≥ 1.90 T at 100 A / cm, preferably B ≥ 1.95 T at 100 A / cm, preferably B ≥ 2.00 T at 100 A / cm.

[0017] The hysteresis losses P Hystare determined from the core losses P at an induction amplitude of 1.5T across the y-axis intercept in a P / f plot versus frequency f by linear regression. The linear regression is performed using at least 8 measured values, which are distributed approximately evenly over the frequency range from 50 Hz to 1 kHz (e.g., at 50, 100, 200, 300, 400, 500, 600, 700, 800, 900, 1,000 Hz).

[0018] In one embodiment, the alloy has a maximum permeability µ max ≥ µ max ≥ 10,000, an electrical resistance p ≥ 0.28 µΩm, hysteresis losses P Hys ≤ 0.055 J / kg at an amplitude of 1.5 T, a coercive field strength H cof ≤ 0.5 A / cm and an induction B ≥ 1.95 T at 100 A / cm. This combination of properties is particularly advantageous for use as or in a rotor or stator of an electric motor to reduce the size of the rotor or stator and thus the electric motor and / or increase the power, or to generate higher torque with the same size and / or weight.

[0019] The soft magnetic alloy can thus be used in an electrical machine, such as in a stator and / or rotor of an electric motor and / or a generator, and / or in a transformer and / or in an electromagnetic actuator. It can be provided in the form of a sheet, for example, with a thickness of 0.5 mm to 0.05 mm. Several sheets of the alloy can be stacked to form a laminated core, which is used as a stator or rotor.

[0020] The alloy has an electrical resistivity of at least 0.25 µΩm, preferably at least 0.3 µΩm. Eddy current losses can be reduced to a lower level by choosing a slightly lower strip thickness.

[0021] In further embodiments, the composition of the soft magnetic alloy is defined in more detail, where 10 wt.% ≤ Co ≤ 20 wt.%, preferably 15 wt.% ≤ Co ≤ 20 wt.% and 0.3 wt.% ≤ V ≤ 5.0 wt.%, preferably 1.0 wt.% ≤ V ≤ 3.0 wt.%, preferably 1.3 wt.% ≤ V ≤ 2.7 wt.% and / or 0.1 wt.% ≤ Cr+Si ≤ 2.0 wt.%, preferably 0.2 wt.% ≤ Cr+Si ≤ 1.0 wt.%, preferably 0.25 wt.% ≤ Cr+Si ≤ 0.7 wt.%.

[0022] In one embodiment, the molecular formula is defined in more detail, where 0.2 wt.% ≤ Cr+Si+Al+Mn ≤ 1.5 wt.%, preferably 0.3 wt.% ≤ Cr+Si+Al+Mn ≤ 0.6 wt.%.

[0023] The soft magnetic alloy may also contain silicon, where 0.1 wt% ≤ Si ≤ 2.0 wt%, preferably 0.15 wt% ≤ Si ≤ 1.0 wt%, preferably 0.2 wt% ≤ Si ≤ 0.5 wt%.

[0024] Aluminum and silicon can be exchanged for each other, so that in one embodiment the sum of Si and aluminum (Si+Al) is 0 wt% ≤ (Si + Al) ≤ 3.0 wt%.

[0025] The alloys are virtually carbon-free and contain a maximum of 0.02 wt% carbon, preferably ≤ 0.01 wt% carbon. This maximum carbon content is considered an unavoidable impurity.

[0026] Calcium, beryllium, and / or magnesium can be added to the alloys in small amounts up to 0.05 wt.% for deoxidation and desulfurization. To achieve particularly good deoxidation, up to 0.05 wt.% cerium or mixed cerium metal can be added.

[0027] The improved magnetic properties can be achieved according to the invention through a heat treatment tailored to the composition as follows. In particular, it has been found that determining the phase transition temperatures for the selected compositions and determining the heat treatment temperatures and cooling rates in relation to these determined phase transition temperatures leads to improved magnetic properties. Furthermore, it is taken into account that alloys with a cobalt content of a maximum of 25 weight percent do not exhibit an order-to-disorder transition, so that no quenching is necessary during production to avoid ordering and the resulting embrittlement.

[0028] CoFe alloys are conventionally used in strip thicknesses ranging from 0.50 mm down to very thin dimensions of 0.050 mm. For strip processing, the material is conventionally hot-rolled and then cold-rolled to the final thickness. During cooling after hot rolling, an embrittlement of the order formation occurs at approximately 730°C, so that for sufficient cold rollability, a special intermediate annealing followed by quenching is required to suppress the order formation. This quenching is omitted for this alloy because it does not exhibit an order-to-disorder transition, which simplifies production.

[0029] To achieve their magnetic properties, CoFe alloys undergo a final heat treatment, also known as final magnetic annealing. For this, the material is heated to the annealing temperature, held at that temperature for a specific time, and then cooled at a defined rate. It is advantageous to perform this final annealing at the highest possible temperatures and in a dry, pure hydrogen atmosphere. High temperatures, on the one hand, increase the reduction of impurities by the hydrogen and, on the other hand, coarsen the grain structure, thus improving the soft magnetic properties such as coercivity and permeability.

[0030] In practice, the annealing temperature in the CoFe system is limited because in the binary system, a phase transition occurs at approximately 950°C, transforming the magnetic and ferritic BCC phase into the non-magnetic and austenitic FCC phase. When alloyed, a two-phase region is formed between the FCC and BCC phases, in which both phases coexist. The transition between the BCC phase and the two-phase or BCC / FCC mixed region occurs at a temperature T Ü1 and the transition between the two-phase region and the FCC phase at a temperature T Ü2 , where T Ü2 > T Ü1The position and size of the two-phase region further depend on the type and extent of the additional alloying. If annealing takes place in the two-phase region or in the FCC region, residues of the FCC phase can damage the magnetism after cooling and incomplete re-transformation. Even with complete re-transformation, a damaging effect remains across the additional grain boundaries because the coercive field strength is inversely proportional to the grain diameter. Consequently, the known, commercially available alloys with Co contents of around 20 wt.% are finally annealed at temperatures below the two-phase region BCC+FCC. For example, the recommendation for AFK 18 is 3h / 850°C, for AFK 1 3h / 900°C. For VACOFLUX 17 the recommendation is 10h / 850°C.

[0031] At such low final annealing temperatures and due to the relatively high magnetocrystalline anisotropy (K1 approx. 45,000 J / m 3At 17 wt.% Co), the potential for particularly good soft magnetic properties in these FeCo alloys is limited. For example, with VACOFLUX 17 tape, maximum permeabilities of around 4,000 can only be achieved, with a coercive field strength of typically 1 A / cm, which limits their application.

[0032] In contrast to these known final annealing processes, the composition enables a heat treatment that produces better magnetic properties than the single-stage annealing with furnace cooling commonly used for FeCo alloys, regardless of the temperature range in which the single-stage annealing takes place. The alloys are selected to shift the lower limit of the two-phase region and the BCC / FCC phase transition upwards, enabling annealing at high temperatures, for example, above 925°C in the pure BCC region. Annealing at such high temperatures is not feasible with previously known FeCo alloys.

[0033] Furthermore, due to the composition, the width of the two-phase region, ie the difference between the lower transition temperature T Ü1 and the upper transition temperature T Ü2 , kept as narrow as possible. Thus, by conducting a final anneal above the two-phase region, combined with cooling through the two-phase region and subsequent holding time or controlled cooling in the pure BCC region, the advantages of a high final anneal, ie, the elimination of potentially magnetically unfavorable textures, the cleaning effect under H2, and the growth of large grains, are obtained without the risk of magnetically harmful residues of the FCC phase.

[0034] It has been found that compositions with a phase transition between the pure BCC region and the BCC / FCC mixed region exhibit significantly improved magnetic properties at higher temperatures, for example, above 925°C, and with a narrow two-phase region, for example, less than 45 K. Compositions with this particular combination of phase diagram features are selected according to the invention and heat-treated accordingly to ensure a high permeability of more than 5000 or more than 10,000.

[0035] Vanadium has been identified as one of the most effective elements in an Fe-Co alloy, increasing electrical resistance while simultaneously shifting the two-phase region to higher temperatures. With lower Co contents, the increase in transition temperatures by vanadium is more effective. In the Fe-17Co alloy, the addition of approximately 2% vanadium can even raise the transition temperatures above the value of the binary FeCo composition.

[0036] In the Fe-Co system, starting with approximately 15% cobalt, the BCC / FCC phase transition occurs at temperatures lower than the Curie temperature. Since the FCC phase is paramagnetic, the magnetic phase transition is no longer determined by the Curie temperature, but rather by the BCC / FCC phase transition. Vanadium in sufficiently high amounts shifts the BCC / FCC phase transition above the Curie temperature T c , so that the paramagnetic BCC phase becomes visible.

[0037] However, if the vanadium content is too high, the width of the mixed region increases. These compositions exhibit lower maximum permeability values, even though the phase transition between the BCC / FCC mixed region and the pure BCC region occurs at higher temperatures. Consequently, it has been determined that the composition influences both the temperatures at which the phase transitions occur and the width of the mixed region and should be considered when selecting the composition. The heat treatment temperatures can be selected relative to the temperatures at which the phase transitions occur for this composition to achieve the highest permeability values.

[0038] It was thus found that a more precise determination of the temperatures at which phase transitions occur for a specific composition is advantageous in optimizing the manufacturing process. These can be determined using DSC (differential scanning calorimetry) measurements. The DSC measurement can be performed with a sample mass of 50 mg and a DSC heating rate of 10 Kelvin per minute, and the resulting phase transition temperatures during heating and cooling of the sample can be used to determine the temperatures for heat treatment.

[0039] Chromium and other elements can be added to improve electrical resistance or mechanical properties, for example. Chromium, like most other elements, lowers the two-phase region of the binary Fe-17Co alloy. The proportion of the alloying element alongside vanadium is therefore preferably selected so that, in combination with vanadium, the two-phase region is increased compared to the binary FeCo alloy. To achieve this, impurities and elements that particularly stabilize austenite (e.g., nickel) must be kept as low as possible.

[0040] The following contents have proven to be preferred for achieving very good magnetic properties: Cobalt of 5 wt.% ≤ Co ≤ 25 wt.% and preferred are contents of 10 wt.% ≤ Co ≤ 20 wt.%, most preferred are contents of 15 wt.% ≤ Co ≤ 20 wt.% Vanadium of 0.3 wt% ≤ V ≤ 5.0 wt% and preferred are contents of 1.0 wt% ≤ V ≤ 3.0 wt% and the following molecular formula: 0.2 wt% ≤ Cr + Si + Al + Mn ≤ 3.0 wt%.

[0041] The alloys are virtually carbon-free and contain a maximum of 0.02 wt% carbon, preferably ≤ 0.01 wt% carbon. This maximum carbon content is considered an unavoidable impurity.

[0042] Calcium, beryllium, and / or magnesium can be added to the alloys in small amounts up to 0.05 wt.% for deoxidation and desulfurization. To achieve particularly good deoxidation and desulfurization, up to 0.05 wt.% cerium or cerium mixed metal can be added.

[0043] The composition allows for further improvement. Cobalt has a higher diffusion coefficient in the paramagnetic BCC phase than in the ferromagnetic BCC phase. Therefore, vanadium enables the separation of the two-phase region and the Curie temperature T c a further temperature range with high self-diffusion, so that heat treatment in this range or cooling through this range enables a larger BCC grain structure and thus better soft magnetic properties. Furthermore, the separation of the two-phase region and the Curie temperature T c This means that upon cooling, both the transition through the BCC / FCC two-phase region and the transition into the pure BCC phase region occur entirely in the paramagnetic state. This also has a positive effect on the soft magnetic properties.

[0044] According to the invention, a method for producing a soft magnetic FeCo alloy according to claim 1 or claim 2 is provided. A precursor is provided which has a composition consisting essentially of 5 wt.% ≤ Co ≤ 25 wt% 0.3 wt.% ≤ V ≤ 5.0 wt% 0 wt.% ≤ Cr ≤ 3.0 wt% 0 wt.% ≤ Si ≤ 3.0 wt% 0 wt.% ≤ Mn ≤ 3.0 wt% 0 wt.% ≤ Al ≤ 3.0 wt% 0 wt.% ≤ Ta ≤ 0.5 wt% 0 wt.% ≤ Ni ≤ 0.5 wt% 0 wt.% ≤ Mon ≤ 0.5 wt% 0 wt.% ≤ Cu ≤ 0.2 wt% 0 wt.% ≤ Nb ≤ 0.25 wt% 0 wt.% ≤ Ti ≤ 0.05 wt% 0 wt.% ≤ Ce ≤ 0.05 wt% 0 wt.% ≤ Ca ≤ 0.05 wt% 0 wt.% ≤ Mg ≤ 0.05 wt% 0 wt.% ≤ C ≤ 0.02 wt% 0 wt.% ≤ Zr ≤ 0.1 wt% 0 wt.% ≤ O ≤ 0.025 wt% 0 wt.% ≤ S ≤ 0.015 wt% The remainder is iron, with Cr+Si+Al+Mn ≤ 3.0 wt.%, and up to 0.2 wt.% of other melt-related impurities. The other impurities may include, for example, one or more of the elements B, P, N, W, Hf, Y, Re, Sc, Be, and other lanthanides except Ce. The precursor has a cold-rolled texture or a fibrous texture.

[0045] The precursor or the parts manufactured from the precursor are heat-treated. In one embodiment, the precursor is heat-treated at a temperature T1 and then cooled from T1 to room temperature.

[0046] In an alternative embodiment, the precursor is cooled at a temperature T1, then to a temperature T2 above room temperature, and further heat-treated at temperature T2, where T1 > T2. Only after the heat treatment at temperature T2 is the precursor cooled to room temperature.

[0047] The precursor exhibits a phase transition from a BCC phase region, into a BCC / FCC mixed region to an FCC phase region, whereby with increasing temperature the phase transition between the BCC phase region and the BCC / FCC mixed region occurs at a first transition temperature T Ü1 and with further increasing temperature the transition between the BCC / FCC mixed region and the FCC phase region at a second transition temperature T Ü2 takes place, where T Ü2 > T Ü1 . The temperature T1 is above T Ü2 and the temperature T2 is below T Ü1 .

[0048] The transition temperatures T Ü1 and T Ü2 depend on the composition of the precursor. The transition temperatures T Ü1 and T Ü2 can be determined by DSC measurements, whereby the transition temperature T Ü1 during heating and the transition temperature T Ü2 during cooling. In one embodiment, the transition temperature T Ü1 with a sample mass of 50 mg and a DSC heating rate of 10 Kelvin per minute above 900°C, preferably above 920°C, and preferably above 940°C.

[0049] In one embodiment, the solidus temperature of the precursor is taken into account when selecting temperatures T1 and T2. It is 940°C ≤ T1 < T m , preferably 960°C ≤ T1 < T m , and 700°C ≤ T2 ≤ 1050°C and T2 < T1, where T m is the solidus temperature.

[0050] The difference T ü2 - T ü1is less than 45K, preferably less than 25K.

[0051] In one embodiment, the cooling rate over at least the temperature range from T1 to T2 is 10°C / h to 900°C / h, preferably 20°C / h to 1000°C / h, preferably 20°C / h to 900°C / h, preferably 25°C / h to 500°C / h. This cooling rate can be used in both of the above-mentioned heat treatments.

[0052] In one embodiment, the difference T ü2 - T ü1 less than 45K, preferably less than 25K, T1 is above T Ü2 and T2 is below T Ü1 where 940°C ≤ T1 < T m , 700°C ≤ T2 ≤ 1050°C and T2 < T1, where T m is the solidus temperature, and the cooling rate is 10°C / h to 900°C / h over at least the temperature range from T1 to T2. This combination of alloy properties, ie T ü2 and T ü1, with the temperatures T1 and T2 of the heat treatment can be used to achieve particularly high permeability values.

[0053] In one embodiment, the precursor is kept above T for a time of more than 30 minutes. Ü2 heat treated and then cooled to T2.

[0054] In one embodiment, the precursor is heat-treated at T1 for a time t1, where 15 minutes ≤ t1 ≤ 20 hours, and then cooled from T1 to T2. In one embodiment, the precursor is cooled from T1 to T2, heat-treated at T2 for a time t2, where 30 minutes ≤ t2 ≤ 20 hours, and then cooled from T2 to room temperature.

[0055] In embodiments where the precursor is cooled from T1 to room temperature, the precursor may then be heated from room temperature to T2 and heat treated at T2 according to any of the embodiments described herein.

[0056] Since the alloy does not exhibit an order-to-disorder transition, quenching over the temperature range of 800°C to 600°C is not required. The cooling rate from 800°C to 600°C can, for example, be between 100°C / h and 500°C / h. However, it can also be chosen slower in principle. The cooling rates mentioned can also be easily maintained until cooling to room temperature.

[0057] The precursor can be cooled from T1 to room temperature at a rate of 25°C / h to 500°C / h.

[0058] The cooling rate of T2 to room temperature has less influence on the magnetic properties, so the precursor of T2 can be cooled to room temperature at a rate of 10°C / h to 50,000°C / h, preferably 100°C / h to 1000°C / h.

[0059] In another alternative embodiment, the precursor is cooled from T1 to room temperature at a cooling rate of 10°C / h to 900°C / h. In embodiments with a slow cooling from T1 to room temperature, for example, at a cooling rate of less than 500°C / h, preferably less than 200°C / h, further heat treatment at temperature T2 can be omitted.

[0060] After heat treatment, the soft magnetic alloy can exhibit one of the following combinations of properties: a maximum permeability µ max ≥ 5,000, and / or an electrical resistance p ≥ 0.25 µΩm, and / or hysteresis losses P Hys ≤ 0.07 J / kg at an amplitude of 1.5 T, a coercive field strength H c of 0.7 A / cm and induction B ≥ 1.90 T at 100 A / cm, or a maximum permeability µ max≥ 10,000, and / or an electrical resistance p ≥ 0.25 µΩm, and / or hysteresis losses P Hys ≤ 0.06 J / kg at an amplitude of 1.5 T, and / or a coercive field strength H c of ≤ 0.6 A / cm, preferably H c ≤ 0.5 A / cm and / or induction B ≥ 1.95 T at 100 A / cm, or a maximum permeability µ max ≥ 12,000, preferably µ max ≥ 17,000 and / or an electrical resistance p ≥ 0.30 µΩm, and / or hysteresis losses P Hys ≤ 0.05 J / kg at an amplitude of 1.5 T, and / or a coercive field strength H c of ≤ 0.5 A / cm, preferably H c ≤ 0.4 A / cm, preferably H c ≤ 0.3 A / cm and / or induction B ≥ 2.00 T at 100 A / cm.

[0061] In certain embodiments, the soft magnetic alloy has one of the following combinations of properties: a maximum permeability µ max≥ 5,000, an electrical resistance p ≥ 0.25 µΩm, hysteresis losses P Hys ≤ 0.07 J / kg at an amplitude of 1.5 T, a coercive field strength H c of ≤ 0.7 A / cm and induction B ≥ 1.90 T at 100 A / cm, or a maximum permeability µ max ≥ 10,000, an electrical resistance p ≥ 0.25 µΩm, hysteresis losses P Hys ≤ 0.06 J / kg at an amplitude of 1.5 T, a coercive field strength H c of ≤ 0.6 A / cm and induction B ≥ 1.95 T at 100 A / cm, or a maximum permeability µ max ≥ 12,000, an electrical resistance p ≥ 0.28 µΩm, hysteresis losses P Hys ≤ 0.05 J / kg at an amplitude of 1.5 T, a coercive field strength H c of ≤ 0.5 A / cm and induction B ≥ 2.00 T at 100 A / cm. a maximum permeability µ max ≥ 17,000, an electrical resistance p ≥ 0.30 µΩm, hysteresis losses P Hys≤ 0.05 J / kg at an amplitude of 1.5 T, a coercive field strength H c of ≤ 0.4 A / cm, preferably H c of ≤ 0.3 A / cm and induction B ≥ 2.00 T at 100 A / cm.

[0062] In one embodiment, the maximum difference in coercive field strength H c after heat treatment, measured parallel to the rolling direction, measured diagonally (45°) to the rolling direction, or measured perpendicular to the rolling direction between two of these directions, a maximum of 6%, preferably a maximum of 3%. In other words, the maximum difference in coercive field strength H c measured parallel to the rolling direction and measured diagonally (45°) to the rolling direction is a maximum of 6%, preferably a maximum of 3% and / or the maximum difference in the coercive field strength H c measured parallel to the rolling direction and measured perpendicular to the rolling direction is a maximum of 6%, preferably a maximum of 3% and / or the maximum difference in the coercive field strength H cMeasured diagonally (45°) to the rolling direction, or measured perpendicular to the rolling direction between two of these directions, a maximum of 6%, preferably a maximum of 3%. This anisotropy, which is extremely low for soft magnetic FeCo alloys, leads to uniform properties along the circumference in rotor or stator applications, and therefore there is no need to twist rotor or stator laminations in each lamination layer to ensure sufficient isotropy of the magnetic properties in the lamination stack.

[0063] The heat treatment can be carried out under a hydrogen-containing atmosphere or under an inert gas.

[0064] In one embodiment, the heat treatment is performed at T1 in a stationary furnace and at T2 in a stationary furnace or a continuous furnace. In another embodiment, the heat treatment is performed at T1 in a continuous furnace and at T2 in a stationary furnace or a continuous furnace.

[0065] The precursor product may have a cold-rolled texture or a fiber texture before heat treatment.

[0066] The precursor product can be provided in the form of a strip. At least one sheet can be manufactured from the strip by punching, laser cutting, or waterjet cutting. In one embodiment, the heat treatment is performed on punched, laser-cut, eroded, or waterjet-cut sheet metal sections manufactured from the strip material.

[0067] In one embodiment, after heat treatment, several sheets are bonded to form a laminated core using an insulating adhesive, or are superficially oxidized to create an insulating layer and then bonded or laser welded to form the laminated core, or are coated with an inorganic-organic hybrid coating and then further processed to form the laminated core.

[0068] In some embodiments, the precursor product has the shape of a laminated core, and the laminated core is heat-treated according to one of the embodiments described herein. The heat treatment can thus be performed on punched or welded laminated cores manufactured from sheet metal blanks.

[0069] The precursor product can be produced as follows. A melt can be provided, for example, by vacuum induction melting, electroslag remelting or vacuum arc remelting, wherein the melt consists essentially of 5 wt.% ≤ Co ≤ 25 wt% 0.3 wt.% ≤ V ≤ 5.0 wt% 0 wt.% ≤ Cr ≤ 3.0 wt% 0 wt.% ≤ Si ≤ 3.0 wt% 0 wt.% ≤ Mn ≤ 3.0 wt% 0 wt.% ≤ Al ≤ 3.0 wt% 0 wt.% ≤ Ta ≤ 0.5 wt% 0 wt.% ≤ Ni ≤ 0.5 wt% 0 wt.% ≤ Mon ≤ 0.5 wt% 0 wt.% ≤ Cu ≤ 0.2 wt% 0 wt.% ≤ Nb ≤ 0.25 wt% 0 wt.% ≤ Ti ≤ 0.05 wt% 0 wt.% ≤ Ce ≤ 0.05 wt% 0 wt.% ≤ Ca ≤ 0.05 wt% 0 wt.% ≤ Mg ≤ 0.05 wt% 0 wt.% ≤ C ≤ 0.02 wt% 0 wt.% ≤ Zr ≤ 0.1 wt% 0 wt.% ≤ O ≤ 0.025 wt% 0 wt.% ≤ S ≤ 0.025 wt% The remainder is iron, with Cr+Si+Al+Mn ≤ 3.0 wt.%, and up to 0.2 wt.% other impurities. Other impurities may include one or more of the elements B, P, N, W, Hf, Y, Re, Sc, Be, and other lanthanides except Ce. The melt is solidified into an ingot, which is then formed into a precursor with final dimensions. The forming is carried out by means of hot rolling and / or forging and / or cold forming.

[0070] In one embodiment, the cast ingot is formed into a slab with a thickness D1 by hot rolling at temperatures between 900°C and 1300°C and then formed into a strip with a thickness D2 by cold rolling, where 1.0 mm ≤ D1 ≤ 5.0 mm and 0.05 mm ≤ D2 ≤ 1.0 mm, where D2 < D1. The degree of cold deformation by cold rolling can be >40%, preferably >80%.

[0071] In one embodiment, the cast ingot is formed into a billet by hot rolling at temperatures between 900°C and 1300°C and then formed into a wire by cold drawing. The degree of cold deformation by cold drawing can be >40%, preferably >80%.

[0072] Intermediate annealing at an intermediate dimension in a continuous furnace or in a stationary furnace can be carried out to reduce work hardening and thus adjust the desired degree of cold deformation.

[0073] The Curie temperature of the alloy can be taken into account when selecting temperatures T1 and / or T2. For example, T ü1 > T c , where T c is the Curie temperature, and T c ≥ 900°C. In one embodiment, T ü1 > T2 > T c chosen.

[0074] For compositions where there is a separation of the two-phase region and the Curie temperature T cThere is a further temperature range with high self-diffusion, so that heat treatment in this range or cooling through this range enables a larger BCC grain structure and thus better soft magnetic properties. Furthermore, the separation of the two-phase region and the Curie temperature T c This means that upon cooling, both the passage through the two-phase region BCC / FCC and the transition into the region of the pure BCC phase occur entirely in the paramagnetic state. By selecting the temperature T2 such that T ü1 > T2 > T c the soft magnetic properties can be further improved.

[0075] In one embodiment, the average grain size after the final annealing is at least 100µm, preferably at least 200µm, preferably at least 250µm.

[0076] In one embodiment, the measured density of the annealed alloy is more than 0.10% lower than the density calculated by the rule of three from the average atomic weight of the metallic elements of the alloy, from the average atomic weight of the metallic elements of the corresponding binary FeCo alloy and from the measured density of this annealed binary FeCo alloy.

[0077] Due to heat treatment, the sulfur content in the finished alloy may be lower than in the melt. For example, the upper limit of the sulfur content in the melt may be 0.025 weight percent, while in the finished soft magnetic alloy, the upper limit is 0.015 weight percent.

[0078] In one embodiment, the precursor is further coated with an oxide layer for electrical insulation. This embodiment can be used, for example, when the precursor is used in a laminated core. The laminated cores or the laminated core can be coated with an oxide layer. The precursor can be coated with a layer of magnesium methylate or, preferably, zirconium propylate, which converts into an insulating oxide layer during heat treatment. The precursor can be heat-treated in an oxygen- or water vapor-containing atmosphere to form the electrically insulating layer.

[0079] In one embodiment, furthermore, punched, laser-cut, or eroded sheet metal sections from the preliminary product are subjected to a final annealing, and the annealed individual sheets are then bonded to a sheet stack using an insulating adhesive, or the annealed individual sheets are superficially oxidized to create an insulating layer and then bonded, welded, or laser-welded to form the sheet stack, or the annealed individual sheets are coated with an inorganic-organic hybrid coating such as Remisol-C5 and then further processed to form the sheet stack.

[0080] The soft magnetic alloy according to any of the preceding embodiments, which can be produced by any of the methods described herein, can be used in an electrical machine, such as as or in a stator and / or rotor of an electric motor and / or a generator, and / or in a transformer and / or in an electromagnetic actuator.

[0081] Embodiments of the invention will now be explained in more detail with reference to the drawings and the following examples. Fig. Figure 1 shows a schematic (not to scale) representation of three variants of heat treatment. Fig. Figure 2 shows a typical DSC heating and cooling curve during phase transition using batch 930423 as an example. Fig.Figure 3 shows the first onset temperatures of the phase transition of the Fe-17Co-Cr-V alloys with increasing V content compared to the binary Fe-17Co melt for heating (DSC) and cooling (DSC). The maximum permeability µ is plotted against a second Y-axis. max applied. Fig. Figure 4 shows coefficients of the induction values ​​B after multilinear regression. Fig. Figure 5 shows coefficients of electrical resistance after multilinear regression. Fig. Figure 6 shows the coercive field strength Hc of batch 930329 (Fe-17Co1.5V-0.5Cr) as a function of the reciprocal grain diameter d for different annealings. Fig. Figure 7 shows the transition temperatures T for different batches ü1 and T ü2 and the best achieved coercive field strength H cof these Fe-17Co special melts with different V contents. The alloys also contain up to a total of 0.6 wt.% of Cr and / or Si. The data on Fig. 7 including the respective annealing is shown in Table 29. Fig. Figure 8 shows maximum permeability and coercive field strength after step annealing of the first annealing stage. Fig. Figure 9 shows maximum permeability and coercive field strength after step annealing of the second annealing stage below the phase transition after previous first annealing stage 4h 1000°C above the phase transition. Fig. Figure 10 shows the coercive field strength Hc of batches 930329 (Fe-17Co-0.5Cr-1.5V) and 930330 (Fe-17Co-2.0V) as a function of the degree of cold deformation. Fig. 11 shows (200) pole figures of batch 93 / 0330 (Fe-17Co-2V). a) Cold-formed: top left. b) After final annealing at 910°C for 10h: top center. c) After final annealing at 1050°C for 4h: top right. d) After final annealing at 1050°C for 4h and 910°C for 10h: Below. Fig. Figure 12 shows the coercive field strength Hc of charge 930330 (Fe-17Co-2V) measured parallel to the rolling direction (“longitudinal”), at 45° to the rolling direction and perpendicular to the rolling direction (“transverse”) for the indicated annealings. Fig. Figure 13 shows the coercive field strength Hc of charge 930335 (Fe-23Co-2V) measured parallel to the rolling direction (“longitudinal”), at 45° to the rolling direction and perpendicular to the rolling direction (“transverse”) for the indicated annealings. Fig. Figure 14 shows new curves of the inventive batches 930329 (Fe-17Co-1.5V-0.5Cr), 930505 (Fe-17Co-1.4V-0.4Si) and 930330 (Fe-17Co-2V) after optimal annealing in comparison to a typical SiFe (TRAFOPERM N4) and typical FeCo alloys. Fig.Figure 15 shows permeability of the inventive charges 930329 (Fe-17Co-1.5V-0.5Cr), 930505 (Fe-17Co-1.4V-0.4Si) and 930330 (Fe-17Co-2V) after optimal annealing in comparison to a typical SiFe (TRAFOPERM N4) and typical FeCo alloys. Fig. Figure 16 shows losses of the inventive batches 930329 (Fe-17Co-1.5V-0.5Cr) and 930330 (Fe-17Co-2V) after optimal annealing at an induction amplitude of 1.5T compared to a typical SiFe (TRAFOPERM N4) and FeCo alloy. The sheet thickness in each case was 0.35 mm. Fig. Figure 17 shows a diagram of the maximum permeability as a function of the relative density difference Δp for Fe-17Co based alloys for the data from Table 25.

[0082] A soft magnetic alloy is provided which consists essentially of: 5 wt.% ≤ Co ≤ 25 wt% 0.3 wt.% ≤ V ≤ 5.0 wt% 0 wt.% ≤ Cr ≤ 3.0 wt% 0 wt.% ≤ Si ≤ 3.0 wt% 0 wt.% ≤ Mn ≤ 3.0 wt% 0 wt.% ≤ Al ≤ 3.0 wt% 0 wt.% ≤ Ni ≤ 0.5 wt% 0 wt.% ≤ Mon ≤ 0.5 wt% 0 wt.% ≤ Ta ≤ 0.5 wt% 0 wt.% ≤ Cu ≤ 0.2 wt% 0 wt.% ≤ Nb ≤ 0.1 wt% 0 wt.% ≤ Ti ≤ 0.05 wt% 0 wt.% ≤ Ce ≤ 0.05 wt% 0 wt.% ≤ Mg ≤ 0.05 wt% 0 wt.% ≤ C ≤ 0.02 wt% 0 wt.% ≤ Ca ≤ 0.05 wt% 0 wt.% ≤ Zr ≤ 0.1 wt% 0 wt.% ≤ O ≤ 0.025 wt% 0 wt.% ≤ S ≤ 0.015 wt% The remainder is iron, and up to 0.2 wt.% of other melt-related impurities. The impurities can be, for example, one or more of the elements B, P, N, W, Hf, Y, Re, Sc, Be, or other lanthanides except Ce.

[0083] To increase the electrical resistance, in addition to the alloying element vanadium, one or more of the group of Cr, Si, Al and Mn can be added to the extent that the following molecular formula is fulfilled: 0.05 wt.%≤Cr+Si+Al+Mn≤3.0 wt.%

[0084] The alloy is preferably melted in vacuum induction furnaces. However, processing via vacuum arc remelting and electroslag remelting is also possible. The melt first solidifies into an ingot, which is freed from the oxide skin and then forged or hot-rolled at temperatures between 900 °C and 1300 °C. Alternatively, the oxide skin can be removed from previously forged or hot-rolled bars. The desired size can be achieved by hot-forming strips, billets, or bars. Hot-rolled material can be freed of surface oxides by blasting, grinding, or peeling. The desired final size can also be achieved by cold-forming strips, bars, or wires. For cold-rolled strips, a grinding process can be inserted between the hot-rolling process to remove oxide roots.If excessive hardening has occurred after cold forming, one or more intermediate annealings can be performed for recovery and recrystallization at temperatures between 400 °C and 1300 °C. The thickness or diameter for the intermediate annealing should be selected so that a cold deformation of > 40% of the final thickness is achieved, preferably a cold deformation of > 80%.

[0085] The final processing step is a heat treatment at temperatures between 700 °C and the solidus temperature T m (typically, however, a maximum of 1200°C), also known as magnetic final annealing. The final annealing is preferably carried out in a pure, dry hydrogen atmosphere. Annealing under protective gas or in a vacuum is also possible.

[0086] Fig.Figure 1 shows a schematic representation of three heat treatment variants with respect to the phase transitions and in particular to the FCC, FCC+BCC and BCC regions.

[0087] In variant 1, which is part of the claimed invention and is indicated by the solid line in Fig. As shown in Figure 1, a first annealing step in the FCC region is immediately followed by a second annealing step in the BCC region. The second annealing step is optional and can be used to further improve the soft magnetic properties, in particular the permeability and the hysteresis losses. In variant 2, which is part of the claimed invention and is indicated by the dashed line in Fig. 1, the first annealing stage in the FCC region is first cooled to room temperature. The second annealing stage in the BCC region takes place at a later time. In variant 3, which is not part of the claimed invention and is indicated by the dotted line in the Fig. 1, the annealing stage is cooled to room temperature in a controlled manner in the FCC area. Such controlled cooling can also be carried out in variant 1 when cooling from the 1st stage to the 2nd stage (in Fig. 1 not shown).

[0088] Annealing can be performed either in two stages or by controlled cooling from a temperature above the upper transition temperature. Controlled cooling means that a defined cooling rate is maintained to optimally adjust the soft magnetic properties. In any case, one of the annealing stages takes place in the FCC region. The annealing processes according to the invention can be carried out either in a continuous furnace or in a stationary furnace.

[0089] During the annealing according to the invention, the alloy is heated at least once at a temperature above T ü2 between 900°C (when T ü2 > 900°C, then above T ü2 ) and T mannealed in the austenitic FCC region to produce a large grain, utilize the cleaning effect of hydrogen, and remove any magnetically unfavorable textures. This final annealing stage above T ü2 takes place either in a stationary annealing process or in a continuous furnace. This heat treatment step can alternatively be performed on the strip in a continuous furnace. The alloy is then cooled to room temperature or to a temperature between 700°C and 1,000°C in the BCC region at a rate of 10 to 50,000°C per hour, preferably at a rate of 20 to 1,000°C per hour.

[0090] A second annealing step can be carried out either by heating or by holding in the ferritic BCC region at a temperature between 700°C and 1000°C (when T ü1 < 1000°C, then below T ü1) to remove any remaining FCC phase residues. After a final magnetic anneal, the alloy is then cooled from the annealing temperature at a rate of 10 to 50,000°C per hour, preferably at a rate of 20-1,000°C per hour.

[0091] The alloys exhibit a phase transition from a BCC phase region into a BCC / FCC mixed region and, at a slightly higher temperature, a further phase transition from the BCC / FCC mixed region to an FCC phase region, whereby, with increasing temperature, the phase transition between the BCC phase region and the BCC / FCC mixed region occurs at a first transition temperature T Ü1 and with further increasing temperature the transition between the BCC / FCC mixed region and the FCC phase region at a second transition temperature T Ü2 takes place, as in the Fig. 2 is shown.

[0092] The temperature at which the phase transitions from a BCC phase region to a BCC / FCC mixed region and from the BCC / FCC mixed region to an FCC phase region occur can be determined by DSC measurements. Fig. Figure 2 shows a typical DSC heating and cooling curve during the phase transition using the example of batch 930423. The Curie temperature and the 1st onset temperatures of the phase transition are shown in the Fig. 2 also shown.

[0093] The following figures show the results of DSC measurements carried out using a dynamic heat flow differential calorimeter from Netzsch. Two identical crucibles made of corundum (Al2O3) are placed in a furnace, one containing the actual test sample and the other a calibration sample serving as a reference. Both crucibles are subjected to the same temperature program, which can consist of a combination of heating, cooling, or isothermal phases. The heat flow difference is quantitatively determined by measuring the temperature difference at a defined heat conduction path between the sample and the reference. The various maxima and minima (peaks) determined during a DSC measurement can be assigned to specific types of phase transformations based on their curve shapes. Typical curve progressions arise that are material-specific but also depend on the measurement conditions, in particular the sample mass and the heating and cooling rates.To ensure comparability of the measurements, the heating and cooling rates of the measuring device and the sample masses of the samples examined here were chosen to be the same. The heating and cooling rates used in these studies were 10 K / min each, and the sample mass was 50 mg each.

[0094] The transition temperatures T Ü1 and T Ü2are determined using a DSC measurement by heating the sample to a defined mass and heating rate. In this measurement, the transition temperatures are represented by the first onset. This parameter, defined in DIN 51005 ("Thermal Analysis"), is also referred to as the extrapolated peak onset temperature, which represents the beginning of the phase transition and is defined as the intersection point of the extrapolated initial baseline with the tangent through the linear part of a rising or falling peak flank. The advantage of this parameter is that it is independent of sample mass and heating or cooling rates. The width of the two-phase region is defined as the difference between the temperatures of the first onset: T1. Onset(BCC+FCC→FCC)(from DSC heating)−T1. Onset(BCC+FCC→BCC)=TU¨2−TU¨1(from DSC cooling)

[0095] The influence of composition on the transition temperatures T Ü1 and T Ü2are determined using a DSC measurement.

[0096] Fig. Figure 3 shows the first onset temperatures of the phase transition of the Fe-17Co-Cr-V alloys with increasing V content (circles) compared to the binary Fe-17Co alloy (squares) for heating (filled symbols) and cooling (open symbols). The compositions of the alloys are given in Tables 1 to 4.

[0097] The peak Curie temperatures T c of heating (DSC) and cooling (DSC) are shown as diamonds. For the special melts with lower V contents, T c the temperature of the phase transition. The highest measured maximum permeability µ max (triangles) is plotted on the secondary axis. The highest maximum permeabilities are achieved here for V contents between 1 and 3 wt.%.

[0098] Fig. 3 shows that with increasing V content the phase transitions T Ü2and T Ü1 to higher temperatures and that the width of the two-phase region BCC+FCC, ie (T Ü2 - T Ü1 ) becomes larger.

[0099] To adjust the soft magnetic properties, a final annealing is performed. This was always carried out in a protective H2 atmosphere during this study. The H2 quality used was always hydrogen 3.0 (or technical hydrogen) with an H2 content of > 99.9%, where H2O ≤ 40 ppm-mol, O2 ≤ 10 ppm-mol, and N2 ≤ 100 ppm-v.

[0100] The magnetic properties of the alloys were investigated using strip material made from 5 kg cast ingots. The alloys were melted under vacuum and then cast into a flat mold at approximately 1500 °C. After milling off the oxide skin from the individual cast ingots, the ingots were hot-rolled into 3.5 mm thick strips at a temperature of approximately 1000 °C to 1300 °C. The resulting hot-rolled strips were then pickled to remove the oxide skin and then cold-rolled to a thickness of 0.35 mm. To characterize the magnetic properties, sample rings were punched from the strip and resistance strips were cut. The electrical resistance p was determined on the resistance strips. The maximum permeability µ max , the coercive field strength H c , the inductions B at field strengths of 20, 25, 50, 90, 100 and 160A / cm, the remanence B r and the hysteresis losses P Hystwas measured on the manufactured sample rings in the annealed state at room temperature. The hysteresis losses were determined by measuring the losses at an induction amplitude of 1.5T for various frequencies. The intercept in the plot P / f versus f, determined by linear regression, yields the hysteresis losses.

[0101] A slice was sawn off the cast ingots for element analysis. The results of the analysis can be seen in Tables 1 to 4. Table 1 shows the wet chemical analysis of the metallic elements to determine the basic composition. The remainder is iron, other elements < 0.01% are not specified; the values ​​are in wt.%. Table 2 shows the analysis of the non-metallic impurities in the batches from Table 1 using hot gas extraction; the values ​​are in wt.%. Table 3 shows the wet chemical analysis of the metallic elements to fine-tune the basic composition and to limit the composition ranges and impurities. The remainder is iron, other elements < 0.01% are not specified. Values ​​are in wt.%. For batches 930502 and 930503, iron feedstock with a higher level of impurities was used.Table 4 shows the analysis of non-metallic impurities of the batches from Table 3 by hot gas extraction, with the values ​​given in wt.%.

[0102] Table 3 also shows the analysis of the metallic elements of two large melts. The remainder is iron, the P content of large melt 76 / 4988 is 0.003 wt.%, the P content of large melt 76 / 5180 is 0.002 wt.%. Other elements < 0.01% are not listed. Table 4 also shows the analysis of the non-metallic impurities of the two large melts from Table 3 by hot gas extraction, with the values ​​given in wt.%.

[0103] The Fig. 4 and Fig. 5 shows a statistical evaluation of the influence of the main alloying elements cobalt, vanadium and chromium on the induction values ​​after optimal annealing and the electrical resistance using multilinear regression.

[0104] Fig.Figure 4 shows the coefficients of the induction values ​​B after multilinear regression. The numbers after the B values ​​(e.g., B20) indicate the field strength in A / cm. The bars indicate the change in the induction values ​​when alloying with 1 wt.%. Only those elements whose regression value is greater than the regression error are shown.

[0105] Fig. Figure 5 shows electrical resistance coefficients after multilinear regression. The bars indicate the change in electrical resistance when alloying with 1 wt% of the respective elements.

[0106] From these figures, it can be seen that vanadium reduces low induction values ​​less than chromium. However, chromium increases electrical resistance more than vanadium for the same saturation drop (B160). Co increases saturation (B160) but has little effect on the low induction values ​​and electrical resistance.

[0107] Table 7 shows annealing variants according to the invention of the batch 93 / 0330 with a strip thickness of 0.35 mm compared to non-inventive annealing variants, see Fig. 1. The cooling rate is 150°C / h unless otherwise stated. The sample was not demagnetized prior to measurement.

[0108] Fig. Figure 6 shows the coercive field strength Hc of batch 930329 (Fe-17Co1.5V-0.5Cr) as a function of the reciprocal grain diameter d for different annealings. Table 5 shows the mean grain sizes d and coercive field strengths H c and maximum permeabilities µ max after specified annealing, see Fig. 4. The cooling rate was 150°C / h.

[0109] Table 6 shows DSC transition temperatures and Curie temperatures T c . Values ​​in °C. #NV means that no signal is detectable in the DSC measurement.

[0110] One of the reasons for the excellent soft magnetic properties is the unusually large grain structure for Fe-Co alloys, which is achieved after annealing in the FCC region. For example, after a brief annealing period of 4 hours at 1050°C, grain sizes of 354–447 µm were observed for batch 93 / 0330 (Fe-17Co-2V). Similarly large grains can only be achieved by annealing in the BCC region after several days of annealing. Fig. 6 shows, using batch 930329 as an example, the coercive field strength H c versus the reciprocal grain size. A linear relationship is shown.

[0111] To compare the above-mentioned annealing variants, the batch 930330 was examined as an example. Table 8 shows the results after a staged annealing of the first annealing stage (batch 93 / 0330), see Fig.6. The cooling rate is 150°C / h. As long as the first annealing step is performed in the lower FCC region (here at 1050°C), all annealing variants exhibit very good soft magnetic properties, which are significantly better than annealing in the pure BCC region. A second annealing step in the upper BCC region after the first annealing step in the FCC region further improves the values.

[0112] Fig. 7 shows the transition temperatures T ü1 and T ü2 as a function of the best achieved coercive field strength H c of the Fe-17Co special melts with different V contents. The labels indicate the V content. Fig. Figure 7 shows that the V content is crucial for adjusting the soft magnetic properties. If the V content is too low, there is no increase in T ü1 If the V content is too high, the soft magnetic properties deteriorate because the two-phase region (T ü2 - T ü1) is expanded by vanadium, see also Fig. 3 and Table 6. This results in a minimum of the coercive field strength H c at approximately 1.4 to 2 wt.% vanadium.

[0113] To find the optimal annealing temperature, samples are annealed at different annealing temperatures and then measured. If the number of annealings required exceeds the number of available samples, the same set of samples is usually annealed at different temperatures. In this so-called "step annealing," a low starting temperature is used and the temperature is gradually increased. Step annealing can be used to detect precipitation zones, recrystallization temperatures, or phase transformations that have a direct influence on magnetic properties.

[0114] Fig.Figure 8 shows the maximum permeability and coercive field strength after the first annealing stage. Table 9 shows the results after a step annealing of batch 93 / 0330 below the phase transition after a previous first annealing stage of 4 hours at 1000°C above the phase transition. The cooling rate is 150°C / h. An extended maximum around 1000°C is visible. The corresponding DSC measurement is included for comparison with the phase position.

[0115] Fig.Figure 9 shows maximum permeability and coercive field strength after step annealing in the second annealing stage below the phase transition (circles) after a previous first annealing stage for 4 hours at 1000°C above the phase transition (diamonds). Demagnetization was not performed before measuring the static values. A maximum at 950°C is visible. After the last annealing of the step annealing stage at 1000°C, the samples were annealed again for 10 hours at 950°C (triangles). The original values ​​of the step annealing at 950°C were no longer achieved. Passing through the two-phase region BCC+FCC again leads to deterioration of the soft magnetic properties.

[0116] The magnetic properties were measured for alloys of different compositions after different annealing processes. The results are summarized in Tables 10 to 24. The values ​​B 20 , B 25 , B 50 , B 90 , B 100 , B 160 (T) H c (A / cm), µmax , Br (T) and P Hyst . 1.5T (Ws / kg) are specified.

[0117] Table 10 shows the results after annealing a selection of the batches at 850°C for 4 hours with a cooling rate of 150°C / h. These embodiments are not in accordance with the invention.

[0118] Table 11 shows the results after annealing a selection of the batches for 10 hours at 910°C with a cooling rate of 150°C / h. Demagnetization was not performed prior to measuring the static values. These exemplary embodiments are not in accordance with the invention.

[0119] Table 12 shows the results after annealing a selection of the batches for 10 hours at 910°C and cooling to room temperature, followed by 70 hours at 930°C. The cooling rate is 150°C / h. Demagnetization was not performed prior to measuring the static values. These exemplary embodiments are not in accordance with the invention.

[0120] Table 13 shows the results after annealing a selection of the batches for 4 hours at 1000°C. Cooling rate 150°C / h. No demagnetization was performed prior to measuring the static values.

[0121] Table 14 shows the results after annealing a selection of the batches. The first annealing stage lasted 4 hours at 1000°C, followed by cooling to room temperature, and a second annealing stage lasted 10 hours at 910°C. The cooling rate was 150°C / h. Demagnetization was not performed prior to measuring the static values.

[0122] Table 15 shows the results after annealing all Fe-Co-V-Cr charges for 4 hours at 1050°C. Cooling rate 150°C / h. No demagnetization was performed prior to measuring the static values. The resistances of charges 930322 to 930339 were measured after annealing for 4 hours at 850°C. For the V-rich charges 930422 and 930423, T ü2 to just below 1050°C. Adapted annealing stages are given in Table 18.

[0123] Table 16 shows the results after annealing all Fe-Co-V-Cr batches in the first annealing stage for 4 hours at 1050°C with cooling to room temperature and a subsequent second annealing stage for 10 hours at 910°C. Cooling rate 150°C / h. Demagnetization was performed prior to measurement. For the batches marked in gray, T ü1 either too close or too far above 910°C. Adapted annealing stages can be found in Table 17.

[0124] Table 17 shows the results after adjusting the annealing of those batches where the transition temperatures of the DSC measurement (Table 6) do not match, or only slightly match, the annealing of 4h 1050°C + 10h 910°C (Tables 15 and 16) according to the invention. The cooling rate is 150°C / h. The annealing of 4h 1050°C was not demagnetized prior to the measurement; all other annealings were demagnetized prior to the measurement.

[0125] Table 18 shows the results after annealing of the batch 930423 in different phase areas to clarify the influence of the ferromagnetic and paramagnetic BCC area on the magnetic properties, see also Fig. 2.

[0126] The cooling rate is 150°C / h. For the 4h annealing at 1050°C, the sample was not demagnetized prior to measurement; for all other annealings, demagnetization was performed prior to measurement.

[0127] Table 19 shows the results after annealing a selection of the batches for 4 hours at 1050°C, followed by slow cooling at 50°C / h to room temperature. Demagnetization was not performed prior to measuring the static values.

[0128] Table 20 shows the results after annealing a selection of the batches for 4 hours at 1050°C with slow cooling to room temperature at 50°C / h and a second annealing stage of 10 hours at 910°C with furnace cooling at approximately 150°C / h. Demagnetization was not performed before measuring the static values.

[0129] Table 21 shows the results after annealing a selection of the batches for 4 hours at 1100°C. The cooling rate is 150°C / h. Except for batches 930422 and 930423, no demagnetization was performed prior to measuring the static values.

[0130] Table 22 shows the results after annealing a selection of the batches with a first annealing stage of 4 hours at 1100°C and cooling to room temperature, and a second annealing stage of 10 hours at 910°C. The cooling rate is 150°C / h. Demagnetization was not performed before measuring the static values.

[0131] Table 23 shows the results after annealing a selection of the batches for 4 hours at 1150°C. The cooling rate is 150°C / h. Except for batch 930442, no demagnetization was performed prior to measuring the static values.

[0132] Table 24 shows the results after annealing a selection of the batches with a first annealing stage of 4 hours at 1150°C and cooling to room temperature, and a second annealing stage of 10 hours at 910°C. The cooling rate is 150°C / h. Demagnetization was not performed before measuring the static values.

[0133] Table 25 shows the maximum permeability and density data for various Fe-17Co alloy compositions with various additives. Starting with the binary Fe-16.98Co alloy, whose measured density is 7.942 g / cm 3, and their average atomic weight of 56.371 g / mol (calculated from the analyzed contents of the metallic alloying elements), the fictive density of Fe-17Co alloys with additions of V, Cr, Mn, Si, Al, and other metallic elements is calculated based on their average atomic weight and compared with the measured density. For example, for an alloy Fe-17.19Co-1.97V (batch 93 / 0330), the average atomic weight is 56.281 g / mol. Using the rule of three, one can then calculate 7.942 g / cm 3 × 56.281 / 56.371 = 7.929g / cm 3 Calculate a fictitious density that this Fe-17.19Co-1.97V alloy would have if its lattice constant were unchanged from the binary Fe-16.98Co alloy. In reality, however, this alloy is measured at 7.909 g / cm 3 a density which is -0.26% lower than the fictitious density 7.929g / cm 3 This means that the lattice constant of this alloy must be approximately 0.085% larger than that of the binary alloy.

[0134] Table 26 shows the data for selected batches and anneals which show particularly high maximum permeabilities and at the same time low hysteresis losses, and this at a very high level of induction B at 100A / cm (B 100 ).

[0135] Table 27 shows the data for the impurities C and S in ppm for selected batches and annealings. Annealing at 1050°C under hydrogen effectively reduces these impurities.

[0136] Table 28 shows the magnetic values ​​for the two large melts 76 / 4988 and 76 / 5180. The notation A and B indicate ingot A and ingot B, respectively—the melts were cast into two molds each. The resistivity of batch 76 / 4988 is 0.306 µΩm, and that of batch 76 / 5180 is 0.318 µΩm.

[0137] Table 29 shows the transition temperatures T for different batches ü1 and T ü2and the best achieved coercive field strength H c of these Fe-17Co special melts with different V contents, including details of the respective annealing treatment. The alloys also contain up to a total of 0.6 wt.% Cr and / or Si. The graphic representation of these data shows Fig. 7.

[0138] The Fig. 8 and Fig. 9 show that the BCC / FCC phase transition present in the alloy 930330 according to the invention has a strong influence on the maximum permeability and coercive field strength.

[0139] At the first glow stage ( Fig. 8) the 1st onset of cooling (= Tü1, lower limit of the two-phase region) agrees with the increase of µ max agree, µ max becomes maximum or Hc becomes minimum above the 1st onset of heating (= T Ü2 , upper limit of the two-phase region). At higher temperatures in the FCC region, the magnetic properties deteriorate again.

[0140] In the second glow stage ( Fig. 9) becomes µ max maximum below T Ü1 and decreases as the two-phase region is entered. If the two-phase region is exceeded and the annealing temperature is below T Ü1 (here 950°C) the maximum of µ max no longer achieved, probably due to the fact that this sample passed through the BCC+FCC mixed area twice and the resulting additional grain boundaries.

[0141] In summary, the best magnetic properties are achieved when the first annealing stage is carried out above T Ü2 takes place and the second annealing stage below T Ü1 .

[0142] The influence of the degree of cold deformation on the magnetic properties is investigated.

[0143] Fig. 10 shows coercive field strength H cof batches 930329 (Fe-17Co-0.5Cr-1.5V) and 930330 (Fe-17Co-2.0V) depending on the degree of cold working. For "without intermediate annealing," the hot-rolled thickness corresponds to a KV of 0%; for "with intermediate annealing," the thickness of the intermediate annealing corresponds to a KV of 0%.

[0144] The degree of cold deformation (KV) for strip with a final thickness of D2 is defined as the percentage reduction in thickness relative to a non-cold-formed initial thickness D1, since expansion during rolling can be neglected. The non-cold-formed initial thickness D1 can be achieved, for example, by hot rolling or intermediate annealing (ZGL). KV[%]=[(D1−D2) / D1]×100

[0145] In Fig. 10 can be recognized by the coercive field strength H c that with increasing KV, realized by intermediate annealing at different D1 = 1.3mm; 1.0mm; 0.60mm and the same final thickness D2 = 0.35mm, the magnetic properties improve up to about 90% KV.

[0146] Assuming a constant D1 at 3.5mm (hot rolling thickness) and realizing the cold forming by high rolling degrees at 0.20mm and 0.10mm, there is again an increase of H c , which is shown with the dashed line. This can be explained by the fact that at the highest degrees of cold work, too many nucleation sites for grains are created and the grains hinder each other's growth during annealing. For example, the alloy of batch 930329 (Fe-17Co-0.5Cr-1.5V) (each in wt.%), manufactured without intermediate annealing, after final annealing for 4 hours at T1=1000°C and for 10 hours at T2=910°C, has an average grain size of 0.25mm at a final thickness of 0.35mm, an average grain size of 0.21mm at a final thickness of 0.20mm, and an average grain size of 0.15mm at a final thickness of 0.10mm. There is therefore an optimal degree of cold work, which is around 90%.

[0147] To investigate whether texture formation is crucial for the magnetic properties, the texture was determined by X-ray diffraction on sheets measuring 50 mm x 45 mm.

[0148] Fig. Figure 11 shows (200) pole figures from batch 93 / 0330 (Fe-17Co-2V). The left panel shows the result for an unannealed sheet with a rolling texture. The middle panel shows the result for a sheet annealed at 910°C for 10 hours, which exhibits only a very weak texture. The right panel shows the result for a sheet annealed at 1050°C for 4 hours, which exhibits no texture. The bottom panel shows the result for a sheet annealed at 1050°C for 4 hours and 910°C for 10 hours, which exhibits no texture.

[0149] The angle-dependent Cu-K α= 0.154059295 nm was irradiated onto the sample, and the diffracted intensity was measured with a 2 mm pinhole. A Lynxexe semiconductor strip detector with a 2° angular range and energy-dispersive operation was used as the detector. As shown, for example, by the (200) pole figures, a rolling texture is present in the unannealed, as-rolled state, which completely dissolved after annealing in the FCC region at 1050°C in H2 for 4 hours.

[0150] The absence of texture is also consistent with the measurements of the direction-dependent H c For this purpose, five H c -Strips measuring 50mm × 10mm were taken from different directions relative to the rolling direction (longitudinal = 0°, diagonal = 45°, transverse = 90°) and measured in the Förster coercimate.

[0151] Fig. 12 shows the coercive field strength H cof batch 930330 (Fe-17Co-2V) measured parallel to the rolling direction ("longitudinal"), at 45° to the rolling direction, and perpendicular to the rolling direction ("transverse") for the specified annealing processes. Each point is the mean of five measurements. The error bars represent the standard deviation.

[0152] Fig. Figure 13 shows the coercive field strength Hc of batch 930335 (Fe-23Co-2V) measured parallel to the rolling direction ("longitudinal"), at 45° to the rolling direction, and perpendicular to the rolling direction ("transverse") for the specified annealing processes. Each point is the mean of five measurements. The error bars represent the standard deviation.

[0153] After annealing for 4 hours at 910°C, the mean values ​​show an anisotropic behavior. However, taking the statistical error into account, this anisotropy is not significant. This slight anisotropy, however, corresponds to the residual texture from the corresponding pole figure (middle image above of the Fig.11). After annealing for 4 hours at 1050°C and 4 hours at 1050°C + 10 hours at 910°C, almost identical mean values ​​for Hc are obtained. Annealing in the FCC region at 1050°C thus completely erases the existing texture, and the subsequent second annealing step in the BCC region at 910°C does not produce any new texture.

[0154] In the following, the magnetic properties of the alloy are compared with reference alloys using the inventive batches 930329 (Fe-17Co-1.5V-0.5Cr) and 930330 (Fe-17Co-2.0V). The reference alloys are a typical electrical steel TRAFOPERM N4 (Fe-2.5Si-Al-Mn) and three FeCo alloys: VACOFLUX 17 (Fe-17Co-2Cr-Mo-V-Si), VACOFLUX 48 (Fe-49Co-1.9V), and a HYPOCORE special melt. The HYPOCORE special melt was melted according to the composition published by Carpenter Technologies (Fe-5Co-2.3Si-1Mn-0.3Cr - data in wt.%).

[0155] Fig.Figure 14 shows new curves of the inventive batches 930329 (Fe-17Co-1.5V-0.5Cr), 930505 (Fe-17Co-1.4V-0.4Si) and 930330 (Fe-17Co-2V) after optimal annealing in comparison to a SiFe (TRAFOPERM N4) and FeCo comparison alloys.

[0156] Fig. Figure 15 shows permeability of the inventive charges 930329 (Fe-17Co-1.5V-0.5Cr), 930505 (Fe-17Co-1.4V-0.4Si) and 930330 (Fe-17Co-2V) after optimal annealing in comparison to a pSiFe (TRAFOPERM N4) and FeCo comparison alloys.

[0157] Fig. Figure 16 shows losses of the inventive heats 930329 (Fe-17Co-1.5V-0.5Cr) and 930330 (Fe-17Co-2V) after optimal annealing at an amplitude of 1.5T compared to a SiFe (TRAFOPERM N4) and FeCo reference alloy. The hysteresis losses (y-intercept) of 930329, 930330, and TRAFOPERM N4 are similar. The sheet thickness was 0.35 mm in each case.

[0158] Fig.Figure 17 shows the maximum permeability as a function of the relative density difference Δρ for Fe-17Co-based alloys (data from Table 25). It can be seen that high maximum permeabilities are obtained for alloys with a relative density difference of -0.10% to -0.35%, and particularly high maximum permeabilities for alloys with a relative density difference of -0.20% to -0.35%. This relative density difference compared to the binary Fe-17Co alloy ultimately means that the lattice constant of these alloys must be somewhat larger than that of the binary alloy. A larger lattice constant means a lower activation energy for site exchange processes due to the larger interatomic spacing in the crystal lattice, and thus better diffusion. This also contributes to grain growth and thus to a lower coercive field strength or higher permeability.

[0159] To investigate the properties of alloys on a production scale, two large melts were conducted under normal production conditions. 2.2 tons of the desired composition were melted in a vacuum induction furnace and, after adjustment and analysis of the precise composition, poured into two 340 mm diameter round molds. After solidification and cooling, the round ingots were removed from the mold and heated to 1170°C in a gas-fired rotary hearth furnace for hot rolling. The thoroughly heated ingots were then rolled on an ingot roller into slabs with a cross-section of 231 × 96 mm. 2 These slabs were then hot-rolled to remove the oxide skin on all sides to a size of 226 × 93 mm 2 sanded.

[0160] From batch 76 / 4988, both slabs obtained in this way were rolled into hot strip on a hot rolling mill. The slabs were first soaked at a temperature of 1130°C and, after sufficient soaking, then rolled into hot strip. A final thickness of 2.6 mm was selected for one strip. The final rolling temperature of this strip was 900°C, and the coiling temperature was 828°C. The final thickness of the other strip was 1.9 mm. The final rolling temperature of this strip was 871°C, and the coiling temperature was 718°C. Both hot strips were subsequently blasted to remove the oxide skin. One portion of the hot-rolled strip was intermediate annealed for 1 hour at 750°C in an H2 protective gas atmosphere. Another portion of the hot-rolled strip was intermediate annealed for 1 hour at 1050°C in an H2 protective gas atmosphere. The remaining portion of the hot-rolled strip remained without intermediate annealing. Rolling to final thickness then took place, with oxide removal from both sides of the strip at an intermediate thickness.Before hot rolling the strip, 15 mm thick sections were sawn off the slabs and then hot rolled (3.5 mm thick), pickled, and then cold rolled in the pilot plant. The results obtained are included for comparison.

[0161] From batch 76 / 5180, a 15 mm thick slice was sawn off at each end of each slab. These slices were heated to 1200°C and then hot-rolled into a 3.5 mm thick strip. The resulting hot-rolled strips were pickled to remove oxides. They were then cold-rolled to a thickness of 0.35 mm.

[0162] Stamped rings were made from all the strips obtained in this way and subjected to a final annealing treatment. Table 28 shows the results obtained for the magnetic values. The resistivity of batch 76 / 4988 is 0.306 µΩm, and that of batch 76 / 5180 is 0.318 µΩm.

[0163] As can be seen from Table 28, better magnetic properties were measured for samples from the large melt than for commercially available alloys with a Co content below 30 weight percent, such as VACOFLUX 17. A maximum permeability of over 20,000 was measured for a sample from the large melt 76 / 5180B. Thus, the alloy is suitable for the large-scale production of ribbon material with improved magnetic properties.

[0164] The alloy exhibits higher induction values ​​than VACOFLUX 17 for every field strength. For induction values ​​above the breakpoint, the new alloy lies between TRAFOPERM N4 and VACOFLUX 48. The airflow-corrected induction B at a field strength of 400 A / cm near magnetic saturation is 2.264 T for both batches (corresponding to a polarization J of 2.214 T). In the operating range of typical electric motors and generators, the torque will therefore be higher for the new alloy than for VACOFLUX 17 and TRAFOPERM N4.

[0165] Comparing 930329 and 930330, it can be seen that vanadium, in conjunction with the heat treatment described above, increases the squareness of the hysteresis loop to such an extent that, depending on the alloying, the maximum permeability is almost as high as that of VACOFLUX 48. This is astonishing and extremely surprising, since at approximately 50% Co, a zero crossing of the anisotropy constant K1 exists, which is not present at 17% Co. At 17% Co, on the contrary, the anisotropy constant K1 is very high in the Fe-Co system.

[0166] The excellent soft magnetic properties are also evident in the hysteresis losses, which are at a comparable level to those of TRAFOPERM N4. However, with increasing frequency, the losses of TRAFOPERM N4 increase less than those of the new alloy due to the higher electrical resistance of the same strip thickness. This effect can be compensated for by choosing a slightly thinner strip thickness, resulting in correspondingly lower eddy current losses.

[0167] In summary, a highly permeable soft magnetic alloy is provided that exhibits better soft magnetic properties, such as significantly higher permeability and lower hysteresis losses, while simultaneously offering higher saturation than existing and commercially available FeCo alloys. At the same time, this new alloy offers significantly lower hysteresis losses than previously known and commercially available alloys with Co contents between 10 and 30 wt.%, and, above all, a significantly higher permeability level never before achieved for such alloys. The alloy can also be produced on an industrial scale and cost-effectively. Table 1 Batch 93 / Co Ni Cr Mn V Si Al Mon Be cerium 0322 17,80 < 0,01 0,01 < 0,01 < 0,01 < 0,01 < 0,01 2,50 < 0,01 - 0323 16,98 < 0,01 < 0,01 < 0,01 < 0,01 < 0,01 < 0,01 < 0,01 < 0,01 - 0324 23,20 < 0,01 < 0,01 < 0,01 < 0,01 < 0,01 < 0,01 < 0,01 < 0,01 - 0325 17,05 < 0,01 2,01 < 0,01 < 0,01 < 0,01 < 0,01 < 0,01 < 0,01 - 0326 23,25 < 0,01 2,03 < 0,01 < 0,01 < 0,01 < 0,01 < 0,01 < 0,01 - 0327 17,14 < 0,01 1,54 < 0,01 0,50 < 0,01 < 0,01 < 0,01 < 0,01 - 0328 17,08 < 0,01 1,04 < 0,01 0,98 < 0,01 < 0,01 < 0,01 < 0,01 - 0329 17,12 < 0,01 0,54 < 0,01 1,46 < 0,01 < 0,01 < 0,01 < 0,01 - 0330 17,19 < 0,01 < 0,01 < 0,01 1,97 < 0,01 < 0,01 < 0,01 < 0,01 - 0331 23,09 0,012 1,04 < 0,01 0,99 < 0,01 < 0,01 < 0,01 < 0,01 - 0332 22,97 < 0,01 1,04 < 0,01 0,99 0,19 < 0,01 < 0,01 < 0,01 - 0333 22,96 < 0,01 1,03 < 0,01 0,98 < 0,01 0,18 < 0,01 < 0,01 - 0334 23,01 0,022 1,04 < 0,01 0,98 < 0,01 < 0,01 < 0,01 0,06 - 0335 22,93 < 0,01 < 0,01 < 0,01 1,95 < 0,01 < 0,01 < 0,01 < 0,01 - 0336 23,07 < 0,01 1,04 < 0,01 0,98 < 0,01 < 0,01 < 0,01 < 0,01 <0,001 (Einsatz 0,02) 0337 22,93 < 0,01 1,03 < 0,01 0,98 < 0,01 < 0,01 < 0,01 < 0,01 <0,001 (Einsatz 0,01) 0338 23,07 < 0,01 1,04 < 0,01 0,98 < 0,01 < 0,01 < 0,01 < 0,01 <0,001 (Einsatz 0,005) 0339 23,06 0,017 < 0,01 < 0,01 < 0,01 < 0,01 1,96 < 0,01 < 0,01 - Table 2 Charge 93 / C S O N 0322 0,0050 0,0012 0,0016 0,0012 0323 0,0045 0,0010 0,0150 0,0011 0324 0,0038 0,0010 0,0130 0,0009 0325 0,0031 0,0011 0,0100 0,0011 0326 0,0032 0,0011 0,0085 0,0012 0327 0,0032 0,0011 0,0097 0,0011 0328 0,0029 0,0011 0,0100 0,0013 0329 0,0028 0,0012 0,0093 0,0013 0330 0,0024 0,0011 0,0092 0,0014 0331 0,0030 0,0011 0,0087 0,0011 0332 0,0022 0,0011 0,0068 0,0012 0333 0,0040 0,0011 0,0014 0,0011 0334 0,0036 0,0010 0,0022 0,0013 0335 0,0034 0,0010 0,0120 0,0016 0336 0,0040 0,0010 0,0088 0,0014 0337 0,0039 0,0010 0,0058 0,0012 0338 0,0036 0,0011 0,0082 0,0012 0339 0,0025 0,0009 0,0026 0,0010 Table 4 Charge 93 / C S O N 0420 0,0034 0,0012 0,0130 0,0016 0421 0,0021 0,0012 0,0110 0,0014 0422 0,0021 0,0012 0,0110 0,0015 0423 0,0034 0,0012 0,0100 0,0014 0424 0,0028 0,0011 0,0110 0,0010 0425 0,0032 0,0012 0,0089 0,0012 0426 0,0020 0,0012 0,0081 0,0011 0427 0,0022 0,0011 0,0084 0,0010 0428 0,0026 0,0012 0,0086 0,0013 0429 0,0056 0,0012 0,0070 0,0012 0430 0,0170 0,0012 0,0048 0,0012 0431 0,0014 0,0013 0,0094 0,0013 0432 0,0019 0,0013 0,0096 0,0012 0433 0,0019 0,0012 0,0100 0,0012 0434 0,0017 0,0025 0,0110 0,0010 0435 0,0030 0,0032 0,0150 0,0007 0436 0,0022 0,0030 0,0110 0,0007 0437 0,0023 0,0017 0,0110 0,0006 0438 0,0027 0,0010 0,0093 0,0011 0439 0,0050 0,0010 0,0023 0,0006 0440 0,0022 0,0008 0,0050 0,0010 0441 0,0020 0,0009 0,0075 0,0008 0442 0,0027 0,0008 0,0017 0,0005 0443 0,0032 0,0009 0,0130 0,0070 0502 0,0038 0,0028 0,0120 0,0029 0503 0,0058 0,0022 0,0035 0,0028 0504 0,0025 0,0010 0,0092 0,0008 0505 0,0024 0,0010 0,0063 0,0008 Großschmelzen 76 / 4988 0,0010 0,0042 0,0121 0,0023 76 / 5180 0,0021 0,0062 0,0073 0,0026 Table 5 Charge 93 / Banddicke mm Glühung mittl. Korngröße d mm 1 / d 1 / mm H c A / cm µ max 0329 0,35 4h 850°C 0,075 13,33 1,035 3584 0329 0,35 10h 910°C 0,151 6,62 0,622 5090 0329 0,35 10h 910°C + 70h 930°C 0,254 3,94 0,418 5737 0329 0,35 4h 1100°C 0,214 4,67 0,524 7497 0329 0,35 4h 1100°C + 10h 910°C 0,360 2,78 0,396 12084 0329 0,35 4h 1050°C 0,302 3,31 0,501 7943 0329 0,35 4h 1050°C +10h 910°C 0,214 4,67 0,367 14291 0329 0,35 4h 1150°C 0,254 3,94 0.473 7860 0325 0,35 4h 1050°C 0,197 5,08 1,004 3554 0328 0,35 4h 1050°C 0,278 3,60 0,6925 5387 0330 0,35 4h 1050°C 0,401 2,49 0.353 11509 0329 0,35 4h 1000°C + 10h 910°C 0,250 4,00 0,384 15658 0329 0,20 4h 1000°C + 10h 910°C 0,213 4,69 0,474 10978 0329 0,10 4h 1000°C + 10h 910°C 0,151 6,62 0,523 10965 Table 6 Charge 93 / 1. Onset heating (T ü2 ) Peak Aufheizen 1. Onset cooling (T ü1 ) Peak Abkühlen T c Peak heating T c Peak cooling Mitte Tc Peak 0322 928 938 908 897 #NV #NV #NV 0323 940 951 932 919 #NV #NV #NV 0324 950 964 944 928 #NV #NV #NV 0325 905 918 880 859 #NV #NV #NV 0326 921 937 884 862 #NV #NV #NV 0327 919 930 897 879 #NV #NV #NV 0328 934 943 914 898 #NV #NV #NV 0329 952 958 933 926 937 #NV #NV 0330 980 987 958 951 943 931 937 0331 934 946 913 895 #NV #NV #NV 0332 931 945 910 893 #NV #NV #NV 0333 937 950 915 898 #NV #NV #NV 0334 933 945 912 895 #NV #NV #NV 0335 962 974 953 939 #NV #NV #NV 0336 933 947 912 895 #NV #NV #NV 0337 933 947 912 895 #NV #NV #NV 0338 934 947 913 895 #NV #NV #NV 0339 1070 1088 1020 1011 962 950 956 0420 988 995 964 958 941 933 937 0421 971 978 956 947 960 #NV #NV 0422 1017 1026 979 974 940 931 936 0423 1037 1063 994 988 938 929 934 0424 993 997 952 947 886 878 882 0425 965 971 939 933 916 907 912 0426 949 958 935 923 #NV #NV #NV 0427 951 963 939 924 #NV #NV #NV 0428 951 960 934 923 936 #NV #NV 0429 947 960 934 922 938 #NV #NV 0430 944 952 932 917 938 #NV #NV 0431 950 958 931 920 937 #NV #NV 0432 946 953 925 912 935 #NV #NV 0433 949 957 929 919 938 #NV #NV 0434 944 952 921 911 937 #NV #NV 0435 953 961 932 924 938 #NV #NV 0436 952 959 931 922 935 #NV #NV 0437 954 961 934 926 937 #NV #NV 0438 955 962 934 926 938 #NV #NV 0439 958 965 936 926 934 #NV #NV 0440 954 961 934 925 936 #NV #NV 0441 952 959 932 924 937 #NV #NV 0442 #NV #NV (1065) (1050) 924 916 920 0443 #NV #NV 1012 1001 936 925 931 0502 960 968 941 930 939 #NV #NV 0503 959 968 941 929 939 #NV #NV 0504 975 982 956 949 939 929 934 0505 970 977 953 946 936 926 931 76 / 4988 989 995 962 957 939 929 934 76 / 5180 965 974 949 942 938 #NV #NV Table 7 Glühung Glüh- Variante B20 in T B25 in T B50 in T B90 in T B100 in T B160 in T Hc in A / cm µ max Br in T P Hyst. 1,5T Ws / kg 4h 1050°C Abk.50°C / h +10h, 910°C 1 1,813 1,84 1,933 2,025 2,043 2,121 0,296 1965 3 1,505 0,045 4h 1050°C +10h 910°C 1 1,814 1,84 1,931 2,024 2,042 2,12 0,340 1776 7 1,525 0,046 10h 1050°C Abk.30°C / h +10h 910°C 1 1,760 1,788 1,888 1,990 2,010 2,102 0,316 1435 8 1,457 0,050 4h 1050°C +10h 910°C 1 1,790 1,817 1,916 2,015 2,034 2,122 0,346 1258 4 1,378 0,049 4h 1050°C Kühlzone +10h, 910°C 1 1,643 1,672 1,776 1,892 1,917 2,035 0,660 6010 1,392 0,075 4h 1050°C ,10h 910°C 2 1,799 1,825 1,921 2,018 2,037 2,124 0,326 1458 6 1,542 0,043 4h 1050°C ,2h 930°C 2 1,795 1,820 1,915 2,012 2,032 2,119 0,341 1383 7 1,532 0,043 4h 1050°C ,2h 910°C 2 1,798 1,824 1,921 2,018 2,037 2,125 0,354 1310 5 1,517 0,044 2h 1050°C ,4h 910°C 2 1,798 1,824 1,919 2,016 2,036 2,123 0,380 1258 1 1,508 0,046 10h 1050°C Abk.50°C / h bis 930°C 10h 2 1,749 1,776 1,877 1,982 2,003 2,098 0,293 1249 4 1,482 0,045 4h 1050°C ,2h 910°C 2 1,790 1,817 1,914 2,012 2,031 2,119 0,413 9787 1,384 0,051 4h 1050°C Abk.50°C / h 3 1,812 1,839 1,932 2,025 2,043 2,122 0,305 1401 5 1,518 0,043 4h 1050°C Abk.150°C / h 3 1,812 1,838 1,929 2,021 2,04 2,119 0,347 1267 0 1,502 0,045 10h 1050°C Abk.30°C / h 3 1,756 1,783 1,885 1,986 2,007 2,095 0,342 1041 9 1,438 0,051 4h 1050°C Abk.150°C / h 3 1,791 1,819 1,917 2,016 2,036 2,124 0,359 1034 8 1,405 0,047 10h 910°C +70h 930°C +61h 950°C nicht nach Erfindung 1,595 1,622 1,723 1,838 1,863 1,991 0,456 5415 1,271 0,072 10h 910°C +70h 930°C nicht nach Erfindung 1,613 1,640 1,740 1,853 1,877 1,999 0,662 4868 1,148 0,072 10h 910°C nicht nach Erfindung 1,615 1,642 1,74 1,848 1,873 1,989 0,684 4868 1,112 0,074 4h 1050°C Kühlzone nicht nach Erfindung 1,635 1,667 1,775 1,893 1,917 2,035 0,740 3769 0,969 0,095 4h 850°C nicht nach Erfindung 1,648 1,677 1,776 1,883 1,906 2,019 1,052 3533 0,867 0,081 Table 8 Glühung B20 in T B25 in T B50 in T B90 in T B100 in T B160 in T Hc in A / cm µ max Br in T 10h 910°C 1,615 1,642 1,740 1,848 1,873 1,989 0,684 4868 1,112 10h 910°C +70h 930°C 1,613 1,640 1,740 1,853 1,877 1,999 0,662 4868 1,148 10h 910°C +70h 930°C +61h 950°C 1,595 1,622 1,723 1,838 1,863 1,991 0,456 5415 1,271 10h 910°C +70h 930°C +61h 950°C +4h 960°C 1,596 1,623 1,722 1,838 1,863 1,990 0,473 5557 1,222 10h 910°C +70h 930°C +61h 950°C +4h 960°C +4h 970°C 1,713 1,742 1,842 1,948 1,969 2,070 0,544 8117 1,391 10h 910°C +70h 930°C +61h 950°C +4h 960°C +4h 970°C +4h 980°C 1,783 1,811 1,909 2,011 2,030 2,119 0,414 10784 1,452 10h 910°C +70h 930°C +61h 950°C +4h 960°C +4h 970°C +4h 980°C +4h 990°C 1,792 1,822 1,923 2,025 2,045 2,131 0,358 11337 1,432 10h 910°C +70h 930°C +61h 950°C +4h 960°C +4h 970°C +4h 980°C +4h 990°C +4h 1000°C 1,779 1,808 1,911 2,015 2,035 2,117 0,315 11155 1,406 10h 910°C +70h 930°C +61h 950°C +4h 960°C +4h 970°C +4h 980°C +4h 990°C +4h 1000°C +4h 1010°C 1,772 1,803 1,908 2,015 2,036 2,128 0,321 11227 1,397 10h 910°C +70h 930°C +61h 950°C +4h 960°C +4h 970°C +4h 980°C +4h 990°C +4h 1000°C +4h 1010°C +4h 1030°C 1,757 1,787 1,892 2,002 2,023 2,120 0,343 10375 1,387 10h 910°C +70h 930°C +61h 950°C +4h 960°C +4h 970°C +4h 980°C +4h 990°C +4h 1000°C +4h 1010°C +4h 1030°C +4h 1050°C 1,703 1,734 1,844 1,962 1,986 2,095 0,371 8527 1,343 Table 9 Glühung B20 in T B25 in T B50 in T B90 in T B100 in T B160 in T Hc in A / cm µ max Br in T Entmagnetisiert? 4h 1000°C 1,801 1,828 1,923 2,019 2,038 2,123 0,407 10618 1,444 no 4h 1000°C +4h 900°C 1,796 1,825 1,921 2,018 2,038 2,124 0,422 10593 1,324 no 4h 1000°C +4h 900°C +4h 910°C 1,796 1,824 1,921 2,018 2,037 2,123 0,414 11436 1,359 no 4h 1000°C +4h 900°C +4h 910°C +4h 920°C 1,795 1,822 1,918 2,015 2,034 2,119 0,406 12326 1,363 no 4h 1000°C +4h 900°C +4h 910°C +4h 920°C +4h 930°C 1,799 1,826 1,921 2,017 2,036 2,121 0,386 13961 1,410 no 4h 1000°C +4h 900°C +4h 910°C +4h 920°C +4h 930°C +4h 940°C 1,791 1,818 1,916 2,013 2,031 2,119 0,387 15856 1,511 yes 4h 1000°C +4h 900°C +4h 910°C +4h 920°C +4h 930°C +4h 940°C +4h 950°C 1,793 1,819 1,916 2,013 2,032 2,119 0,401 16609 1,550 yes 4h 1000°C +4h 900°C +4h 910°C +4h 920°C +4h 930°C +4h 940°C +4h 950°C +4h 960°C 1,794 1,820 1,916 2,012 2,031 2,117 0,427 15298 1,554 yes 4h 1000°C +4h 900°C +4h 910°C +4h 920°C +4h 930°C +4h 940°C +4h 950°C +4h 960°C +4h 970°C 1,767 1,794 1,890 1,990 2,009 2,102 0,525 11053 1,497 yes 4h 1000°C +4h 900°C +4h 910°C +4h 920°C +4h 930°C +4h 940°C +4h 950°C +4h 960°C +4h 970°C +4h 980°C 1,787 1,815 1,917 2,017 2,036 2,123 0,433 9550 1,469 no 4h 1000°C +4h 900°C +4h 910°C +4h 920°C +4h 930°C +4h 940°C +4h 950°C +4h 960°C +4h 970°C +4h 980°C 1,787 1,815 1,917 2,018 2,037 2,124 0,430 11789 1,463 yes 4h 1000°C +4h 900°C +4h 910°C +4h 920°C +4h 930°C +4h 940°C +4h 950°C +4h 960°C +4h 970°C +4h 980°C +4h 990°C 1,782 1,811 1,910 2,011 2,031 2,119 0,431 12585 1,482 yes 4h 1000°C +4h 900°C +4h 910°C +4h 920°C +4h 930°C +4h 940°C +4h 950°C +4h 960°C +4h 970°C +4h 980°C +4h 990°C 1,783 1,812 1,912 2,012 2,032 2,120 0,429 9965 1,485 nein 4h 1000°C +4h 900°C +4h 910°C +4h 920°C +4h 930°C +4h 940°C +4h 950°C +4h 960°C +4h 970°C +4h 980°C +4h 990°C +4h 1000°C 1,778 1,807 1,907 2,009 2,028 2,117 0,433 11762 1,424 ja 4h 1000°C +4h 900°C +4h 910°C +4h 920°C +4h 930°C +4h 940°C +4h 950°C +4h 960°C +4h 970°C +4h 980°C +4h 990°C +4h 1000°C 1,779 1,807 1,908 2,009 2,029 2,118 0,437 9405 1,425 nein 4h 1000°C +4h 900°C +4h 910°C +4h 920°C +4h 930°C +4h 940°C +4h 950°C +4h 960°C +4h 970°C +4h 980°C +4h 990°C +4h 1000°C +10h 950°C 1,775 1,804 1,905 2,007 2,026 2,116 0,460 11012 1,430 ja Table 10 Charge 93 / B20 T B25 T B50 T B90 T B100 T B160 T H c Alcm µ max Br T rho in µΩm PHyst . 1,5T Ws / kg 0322 1,676 1,709 1,815 1,924 1,947 2,056 1,465 3130 1,098 0,3081 0,107 0323 1,765 1,795 1,892 1,995 2,016 2,121 1,120 3815 1,015 0,1872 0,079 0324 1,800 1,836 1,949 2,059 2,082 2,189 1,451 2544 0,766 0,1570 0,093 0325 1,700 1,729 1,830 1,937 1,959 2,068 0,894 4195 0,919 0,3360 0,067 0326 1,715 1,753 1,873 1,992 2,016 2,133 1,144 2735 0,533 0,3739 0,074 0327 1,665 1,694 1,794 1,904 1,926 2,039 0,890 4059 0,908 0,3287 0,070 0328 1,656 1,686 1,787 1,895 1,918 2,031 0,928 3890 0,945 0,3154 0,076 0329 1,651 1,681 1,780 1,887 1,911 2,024 1,035 3584 0,876 0,3042 0,079 0330 1,648 1,677 1,776 1,883 1,906 2,019 1,052 3533 0,867 0,2859 0,081 0331 1,693 1,729 1,847 1,967 1,991 2,110 1,167 2639 0,551 0,3326 0,080 0332 1,681 1,719 1,837 1,956 1,980 2,098 1,229 2633 0,588 0,3580 0,083 0333 1,703 1,740 1,856 1,972 1,996 2,109 1,328 2788 0,756 0,3518 0,088 0334 1,788 1,822 1,929 2,035 2,055 2,151 0,968 3656 0,692 0,3475 0,069 0335 1,673 1,710 1,826 1,945 1,970 2,089 1,248 2643 0,658 0,2857 0,089 0336 1,696 1,733 1,850 1,969 1,992 2,109 1,198 2626 0,586 0,3396 0,081 0337 1,698 1,735 1,852 1,969 1,992 2,107 1,270 2563 0,578 0,3388 0,082 0338 1,696 1,734 1,852 1,970 1,994 2,110 1,241 2653 0,636 0,3334 0,084 Table 11 Charge 931 B20 T B25 T B50 T B90 T B100 T B160 T H c Alcm µ max Br T rho in µΩm PHyst . 1,5T Ws / kg 0328 1,623 1,652 1,751 1,864 1,887 2,005 0,627 4902 1,022 - 0,067 0329 1,618 1,646 1,746 1,858 1,881 2,002 0,622 5090 1,129 - 0,069 0330 1,615 1,642 1,74 1,848 1,873 1,989 0,684 4868 1,112 - 0,074 0331 1,657 1,69 1,807 1,933 1,961 2,09 0,659 3795 0,502 - 0,074 0334 1,799 1,832 1,938 2,039 2,059 2,148 0,659 4556 0,81 - 0,059 0335 1,652 1,686 1,801 1,923 1,948 2,073 0,928 3059 0,587 - 0,082 Table 12 Charge 93 / B20 T B25 T B50 T B90 T B100 T B160 T H c A / cm µ max B r T Rho in µΩm P Hyst. 1,5T Ws / kg 0328 1,771 1,802 1,911 2,017 2,036 2,126 0,473 6912 1,164 - 0,061 0329 1,598 1,624 1,725 1,842 1,868 1,997 0,418 5737 1,168 - 0,061 0330 1,613 1,64 1,74 1,853 1,877 1,999 0,662 4868 1,148 - 0,072 0331 1,658 1,693 1,811 1,941 1,967 2,098 1,265 2702 0,938 - 0,104 0334 1,787 1,820 1,931 2,038 2,060 2,155 1,289 3228 1,158 - 0,099 0335 1,652 1,688 1,809 1,943 1,972 2,116 0,978 3246 0,546 - 0,084 Table 13 Charge 931 B20 T B25 T B50 T B90 T B100 T B160 T H c A / cm µ max Br T Rho in µΩm P Hyst. 1,5T Ws / kg 0323 1,719 1,75 1,855 1,973 1,997 2,111 0,492 5433 1,003 0,189 0,071 0328 1,768 1,797 1,895 1,994 2,013 2,102 0,643 5392 1,212 0,317 0,065 0329 1,803 1,83 1,923 2,017 2,035 2,117 0,509 7929 1,377 0,310 0,055 0330 1,809 1,836 1,927 2,019 2,037 2,117 0,369 16218 1,498 0,291 0,046 0331 1,703 1,739 1,86 1,985 2,01 2,127 1,033 2980 0,967 0,335 0,091 0334 1,707 1,742 1,860 1,979 2,002 2,113 1,145 2994 0,958 0,350 0,091 0335 1,801 1,833 1,942 2,046 2,067 2,155 0,414 6043 1,168 0,289 0,064 0339 1,707 1,739 1,851 1,968 1,990 2,089 0,297 7651 0,869 - 0,051 Table 14 Charge 93 / B20 T B25 T B50 T B90 T B100 T B160 T H c A / cm µ max B r T Rho in µΩm P Hyst. 1,5T Ws / kg 0323 1,72 1,748 1,853 1,971 1,995 2,11 0,402 7983 1,312 0,189 0,060 0328 1,777 1,805 1,902 2,001 2,02 2,108 0,415 11322 1,493 0,317 0,049 0329 1,808 1,834 1,927 2,02 2,038 2,12 0,383 13490 1,529 0,311 0,046 0330 1,807 1,834 1,927 2,02 2,039 2,119 0,353 14673 1,529 0,290 0,047 0331 1,701 1,734 1,854 1,982 2,008 2,129 0,926 4382 1,277 0,335 0,081 0334 1,705 1,738 1,855 1,975 1,999 2,113 0,998 4145 1,184 0,348 0,087 0335 1,802 1,834 1,941 2,047 2,066 2,156 0,401 5998 1,234 0,288 0,065 Table 15 Charg e 93 / B20 T B25 T B50 T B90 T B100 T B160 T H c A / cm µ max B r T rho in µΩ m P Hyst. 1,5T Ws / kg 0322 1,691 1,722 1,828 1,942 1,965 2,077 0,731 4574 1,093 - 0,074 0323 1,713 1,742 1,852 1,972 1,997 2,114 0,456 5732 0,998 - 0,074 0324 1,757 1,79 1,908 2,036 2,063 2,186 0,713 4522 1,051 - 0,078 0325 1,680 1,710 1,816 1,929 1,952 2,063 1,004 3554 0,925 - 0,082 0326 1,695 1,732 1,858 1,988 2,014 2,136 1,336 2397 0,899 - 0,107 0327 1,674 1,705 1,813 1,929 1,953 2,068 0,826 4061 0,948 - 0,078 0328 1,767 1,796 1,893 1,993 2,012 2,103 0,625 5387 1,179 - 0,066 0329 1,809 1,836 1,928 2,021 2,039 2,12 0,501 7943 1,388 - 0,054 0330 1,812 1,838 1,929 2,021 2,040 2,119 0,347 12670 1,502 - 0,045 0331 1,707 1,743 1,863 1,986 2,012 2,125 0,969 3049 0,948 - 0,088 0332 1,700 1,734 1,854 1,977 2,002 2,115 0,974 2982 0,894 - 0,087 0333 1,677 1,712 1,833 1,960 1,986 2,109 0,921 3259 0,903 - 0,084 0334 1,704 1,740 1,857 1,976 2,000 2,112 1,071 3042 0,925 - 0,087 0335 1,809 1,840 1,947 2,051 2,070 2,159 0,480 5631 1,194 - 0,068 0336 1,701 1,735 1,855 1,979 2,004 2,120 0,931 3140 0,907 - 0,085 0337 1,703 1,737 1,857 1,983 2,007 2,125 0,950 3157 0,926 - 0,087 0338 1,707 1,743 1,860 1,982 2,006 2,121 1,058 2934 0,912 - 0,089 0339 1,674 1,716 1,849 1,971 1,993 2,094 0,623 3911 0,552 - 0,053 0420 1,792 1,817 1,910 2,001 2,019 2,101 0,393 11121 1,483 0,3000 0,049 0421 1,795 1,822 1,919 2,017 2,037 2,124 0,459 7856 1,387 0,3013 0,058 0422 1,749 1,774 1,866 1,960 1,978 2,064 0,472 9770 1,441 0,3289 0,052 0423 1,577 1,604 1,703 1,815 1,838 1,956 0,798 5361 1,287 0,3552 0,079 0424 1,728 1,752 1,840 1,934 1,953 2,039 0,352 13523 1,458 0,2683 0,045 0425 1,783 1,808 1,898 1,989 2,007 2,089 0,404 11119 1,464 0,2928 0,048 0426 1,783 1,812 1,913 2,017 2,037 2,129 0,562 5515 1,229 0,2993 0,064 0427 1,782 1,817 1,934 2,049 2,071 2,171 0,765 3805 1,013 0,3137 0,078 0428 1,764 1,790 1,885 1,981 2,001 2,089 0,580 6594 1,284 0,3004 0,059 0429 1,780 1,806 1,900 1,996 2,015 2,102 0,514 7120 1,276 0,3019 0,055 0430 1,777 1,804 1,898 1,993 2,012 2,097 0,637 5092 0,997 0,2999 0,061 0431 1,796 1,822 1,913 2,005 2,023 2,106 0,672 6160 1,263 0,3069 0,059 0432 1,795 1,821 1,910 1,997 2,015 2,099 0,746 5357 1,204 0,3149 0,064 0433 1,774 1,801 1,897 1,995 2,014 2,104 0,544 6782 1,291 0,3038 0,058 0434 1,746 1,775 1,873 1,976 1,998 2,094 0,683 5514 1,255 0,3057 0,066 0435 1,795 1,821 1,915 2,010 2,029 2,113 0,488 8261 1,437 0,3020 0,057 0436 1,769 1,798 1,896 1,995 2,015 2,105 0,500 6983 1,322 0,3128 0,059 0437 1,763 1,791 1,889 1,991 2,010 2,101 0,436 7917 1,336 0,3064 0,056 0438 1,804 1,830 1,924 2,016 2,034 2,116 0,470 8359 1,370 0,3065 0,054 0439 1,643 1,673 1,780 1,898 1,923 2,041 0,578 5351 1,228 0,3026 0,076 0440 1,800 1,828 1,921 2,016 2,035 2,117 0,391 10119 1,301 0,2996 0,052 0441 1,800 1,828 1,925 2,021 2,039 2,121 0,353 8636 1,260 0,3053 0,053 0442 1,654 1,684 1,791 1,903 1,926 2,026 0,243 8863 0,803 0,3464 0,050 0443 1,561 1,590 1,693 1,807 1,830 1,949 0,792 4639 1,133 0,3869 0,078 0502 1,742 1,770 1,871 1,974 1,996 2,092 0,615 7186 1,307 0,2999 0,068 0503 1,751 1,779 1,878 1,979 1,999 2,094 0,547 6764 1,157 0,3019 0,057 0504 1,772 1,801 1,899 1,998 2,018 2,109 0,394 10716 1,303 0,3059 0,055 0505 1,785 1,814 1,912 2,012 2,031 2,119 0,334 12009 1,264 0,3085 0,051 Table 16 Charge 931 B20 T B25 T B50 T B90 T B100 T B160 T H c A / cm µ max Br T P Hyst. 1,5T Ws / kg 0322 1,693 1,722 1,826 1,940 1,964 2,077 0,586 8599 1,373 0,061 0323 1,715 1,744 1,852 1,973 1,996 2,114 0,400 9047 1,272 0,062 0324 1,753 1,786 1,903 2,032 2,058 2,180 0,718 4769 1,126 0,079 0325 1,669 1,701 1,815 1,936 1,960 2,075 0,813 3928 0,961 0,082 0326 1,694 1,731 1,856 1,986 2,013 2,135 1,782 1959 0,886 0,131 0327 1,704 1,736 1,849 1,965 1,988 2,093 0,653 4605 1,034 0,075 0328 1,773 1,800 1,896 1,995 2,014 2,102 0,410 13856 1,488 0,050 0329 1,808 1,833 1,925 2,018 2,035 2,115 0,369 17227 1,528 0,046 0330 1,813 1,839 1,930 2,021 2,039 2,118 0,354 19591 1,514 0,046 0331 1,717 1,750 1,868 1,993 2,018 2,132 0,883 4899 1,281 0,079 0332 1,704 1,738 1,855 1,980 2,004 2,119 0,852 4964 1,267 0,076 0333 1,671 1,705 1,824 1,953 1,979 2,104 0,771 5067 1,240 0,073 0334 1,707 1,740 1,855 1,976 2,000 2,114 0,944 4607 1,187 0,080 0335 1,817 1,846 1,951 2,053 2,073 2,161 0,451 9277 1,273 0,064 0336 1,713 1,746 1,864 1,989 2,014 2,131 0,766 5201 1,271 0,073 0337 1,707 1,74 1,859 1,986 2,011 2,131 0,792 5153 1,275 0,074 0338 1,71 1,743 1,859 1,981 2,006 2,120 0,904 4893 1,239 0,078 0339 1,684 1,723 1,850 1,968 1,990 2,089 0,512 4711 0,596 0,052 0420 1,786 1,811 1,904 1,997 2,015 2,098 0,445 12018 1,506 0,058 0421 1,797 1,824 1,920 2,018 2,037 2,122 0,489 8162 1,433 0,066 0422 1,746 1,773 1,866 1,962 1,980 2,066 0,512 9799 1,423 0,062 0423 1,573 1,601 1,702 1,814 1,838 1,955 0,845 5155 1,282 0,092 0424 1,726 1,750 1,839 1,931 1,949 2,035 0,383 14713 1,504 0,053 0425 1,780 1,806 1,896 1,987 2,005 2,089 0,399 15271 1,553 0,053 0426 1,785 1,814 1,915 2,017 2,038 2,129 0,561 6785 1,415 0,067 0427 1,791 1,825 1,941 2,055 2,077 2,176 0,823 4271 1,173 0,083 0428 1,772 1,799 1,893 1,990 2,009 2,097 0,540 8640 1,450 0,061 0429 1,781 1,807 1,901 1,996 2,015 2,103 0,465 10832 1,486 0,056 0430 1,782 1,809 1,901 1,995 2,014 2,101 0,520 9229 1,463 0,057 0431 1,801 1,827 1,918 2,010 2,027 2,110 0,572 9119 1,503 0,060 0432 1,815 1,840 1,927 2,017 2,033 2,113 0,516 11109 1,491 0,050 0433 1,782 1,808 1,903 2,000 2,020 2,108 0,412 12767 1,478 0,050 0434 1,752 1,780 1,877 1,980 2,001 2,095 0,495 11386 1,467 0,054 0435 1,795 1,821 1,914 2,009 2,027 2,111 0,404 15751 1,542 0,049 0436 1,775 1,802 1,900 1,998 2,017 2,104 0,402 13814 1,480 0,049 0437 1,767 1,793 1,891 1,993 2,013 2,103 0,409 13273 1,488 0,053 0438 1,810 1,836 1,929 2,021 2,039 2,120 0,406 15090 1,547 0,047 0439 1,647 1,676 1,783 1,901 1,925 2,042 0,761 4766 1,319 0,087 0440 1,801 1,829 1,921 2,016 2,033 2,115 0,347 15730 1,499 0,047 0441 1,804 1,832 1,927 2,022 2,040 2,120 0,327 16232 1,493 0,048 0442 1,655 1,685 1,792 1,903 1,925 2,026 0,256 9205 0,784 0,050 0443 1,559 1,590 1,694 1,808 1,831 1,946 0,865 4148 1,143 0,097 0502 1,744 1,772 1,869 1,973 1,993 2,089 0,527 10468 1,423 0,056 0503 1,757 1,784 1,879 1,980 2,000 2,095 0,453 11708 1,408 0,050 0504 1,776 1,803 1,900 1,999 2,019 2,109 0,351 14009 1,396 0,051 0505 1,787 1,813 1,912 2,011 2,031 2,118 0,297 15480 1,362 0,047 Table 17 Charge 93 / Glühung B20 T B25 T B50 T B90 T B100 T B160 T H c A / cm µ max B r T P Hyst. 1,5T Ws / kg 0322 4h 1000°C +10h 880°C 1,724 1,729 1,754 1,759 1,859 1,862 1,969 1,972 1,991 1,995 2,097 2,102 0,768 0,737 4338 5449 1,069 1,261 0,079 0,074 0323 4h 1000°C +10h 880°C 1,719 1,721 1,750 1,750 1,858 1,858 1,976 1,978 2,000 2,002 2,116 2,118 0,486 0,483 5242 5573 0,913 0,968 0,079 0,075 0325 4h 1000°C +10h 850°C 1,684 1,687 1,716 1,716 1,824 1,823 1,938 1,939 1,962 1,963 2,073 2,075 0,999 0,903 3559 4733 0,940 1,224 0,083 0,077 0326 4h 1000°C +10h 850°C 1,711 1,710 1,749 1,745 1,873 1,866 1,996 1,992 2,021 2,018 2,137 2,137 1,485 1,478 2412 2945 0,911 1,010 0,110 0,102 0327 4h 1000°C +10h 850°C 1,688 1,689 1,719 1,720 1,827 1,828 1,941 1,942 1,964 1,965 2,072 2,073 0,830 0,890 4123 4324 0,992 1,130 0,076 0,080 0328 4h 1000°C +10h 880°C 1,768 1,772 1,795 1,799 1,892 1,896 1,991 1,995 2,011 2,014 2,101 2,104 0,655 0,637 5130 6179 1,160 1,368 0,068 0,067 0331 4h 1000°C +10h 880°C 1,716 1,717 1,753 1,752 1,873 1,870 1,995 1,992 2,019 2,016 2,132 2,130 1,053 1,192 3037 3336 0,942 1,065 0,090 0,093 0332 4h 1000°C +10h 880°C 1,706 1,709 1,741 1,745 1,862 1,865 1,986 1,988 2,011 2,013 2,124 2,128 0,994 1,079 3212 3460 0,950 1,153 0,088 0,095 0333 4h 1000°C +10h 880°C 1,691 1,683 1,726 1,718 1,843 1,837 1,964 1,961 1,989 1,986 2,105 2,107 1,147 1,089 3036 3858 0,944 0,972 0,090 0,081 0334 4h 1000°C +10h 880°C 1,707 1,706 1,742 1,742 1,860 1,859 1,979 1,978 2,003 2,001 2,115 2,114 1,144 1,100 3075 3581 0,928 1,000 0,090 0,089 0336 4h 1000°C +10h 880°C 1,732 1,736 1,766 1,770 1,883 1,885 2,001 2,003 2,024 2,027 2,133 2,137 1,035 1,092 3128 3634 0,893 1,125 0,085 0,088 0337 4h 1000°C +10h 880°C 1,707 1,704 1,741 1,738 1,861 1,857 1,985 1,982 2,010 2,007 2,127 2,123 1,027 1,095 3190 3449 0,943 1,108 0,089 0,095 0338 4h 1000°C +10h 880°C 1,712 1,713 1,749 1,748 1,866 1,864 1,986 1,986 2,010 2,010 2,122 2,125 1,161 1,260 2888 3421 0,919 1,057 0,092 0,094 0339 4h 1100°C +10h 910°C +4h 1000°C 1,686 1,687 1,692 1,722 1,723 1,726 1,841 1,843 1,841 1,961 1,963 1,960 1,983 1,986 1,983 2,085 2,087 2,086 0,587 0,507 0,438 5345 6186 6989 0,897 0,952 0,984 0,059 0,058 0,061 0420 4h 1050°C +10h 910°C +10h 950°C 1,788 1,789 1,794 1,813 1,816 1,820 1,905 1,907 1,912 1,998 2,000 2,004 2,018 2,017 2,023 2,101 2,098 2,102 0,420 0,444 0,433 11185 11842 14222 1,479 1,514 1,540 - 0,058 0,056 0421 4h 1050°C +10h 910°C +10h 940°C 1,795 1,797 1,798 1,822 1,824 1,825 1,919 1,920 1,921 2,017 2,018 2,018 2,037 2,037 2,037 2,124 2,122 2,121 0,459 0,489 0,467 7856 8162 11468 1,387 1,433 1,519 0,058 - 0,061 0422 4h 1100°C +10h 960°C 1,733 1,736 1,760 1,764 1,856 1,859 1,955 1,958 1,974 1,978 2,063 2,068 0,432 0,382 11411 14880 1,408 1,448 0,053 0,048 0423 4h 1100°C +4h 950°C 1,635 1,634 1,662 1,661 1,760 1,760 1,867 1,868 1,888 1,891 1,993 1,998 0,653 0,621 6647 7626 1,280 1,296 0,065 0,064 0424 4h 1050°C +10h 910°C +10h 940°C 1,728 1,726 1,716 1,752 1,750 1,743 1,840 1,839 1,836 1,934 1,931 1,930 1,953 1,949 1,948 2,039 2,035 2,033 0,352 0,383 0,329 13523 14713 12908 1,458 1,504 1,217 0,045 - 0,055 0425 4h 1050°C +10h 910°C +10h 925°C 1,783 1,780 1,781 1,808 1,806 1,807 1,898 1,896 1,897 1,989 1,987 1,988 2,007 2,005 2,006 2,089 2,089 2,088 0,404 0,399 0,361 11119 15271 18225 1,464 1,553 1,559 0,048 - 0,047 0432 4h 1000°C +10h 900°C 1,797 1,799 1,824 1,826 1,915 1,917 2,009 2,010 2,027 2,028 2,112 2,113 0,640 0,541 6876 10118 1,329 1,509 0,059 0,058 0434 4h 1000°C +10h 900°C 1,739 1,737 1,767 1,765 1,868 1,865 1,973 1,971 1,995 1,992 2,094 2,092 0,675 0,617 5583 7890 1,235 1,420 0,067 0,064 0443 60h 980°C 1,564 1,595 1,701 1,813 1,836 1,949 1,022 3991 1,245 0,108 Table 18 Char ge 931 Glühung B20 T B25 T B50 T B90 T B100 T B160 T H c A / cm µ max B r T P Hyst. 1,5T Ws / kg 0423 4h 1050°C +10h 910°C 1,577 1,573 1,604 1,601 1,703 1,702 1,815 1,814 1,838 1,838 1,956 1,955 0,798 0,845 5361 5155 1,287 1,282 0,079 0,092 0423 4h 1100°C +4h 950°C 1,635 1,634 1,662 1,661 1,760 1,760 1,867 1,868 1,888 1,891 1,993 1,998 0,653 0,621 6647 7626 1,280 1,296 0,065 0,064 4h 1100°C 1,639 1,666 1,764 1,871 1,893 1,998 0,630 6814 1,278 0,065 +4h 910°C 1,636 1,664 1,762 1,869 1,890 1,996 0,715 6508 1,241 0,071 0423 +4h 950°C 1,635 1,662 1,761 1,870 1,892 1,998 0,616 7820 1,321 0,065 +4h 1030°C 1,635 1,662 1,762 1,870 1,892 1,999 0,874 5103 1,303 0,076 0423 4h 910°C 1,597 1,625 1,723 1,831 1,853 1,964 0,777 4524 0,974 0,077 0423 20h 910°C 1,588 1,616 1,716 1,825 1,847 1,962 0,744 4412 1,016 0,074 0423 4h 950°C 1,576 1,604 1,703 1,816 1,839 1,959 0,593 4901 1,117 0,071 0423 20h 950°C 1,579 1,607 1,705 1,814 1,837 1,952 0,608 4782 1,193 0,080 Table 19 Charge 93 / B20 T B25 T B50 T B90 T B100 T B160 T H c Alcm µ max B r T P Hyst. 1,5T Ws / kg 0325 1,691 1,721 1,829 1,945 1,968 2,079 0,804 4377 1,139 0,079 0328 1,77 1,798 1,898 1,999 2,019 2,108 0,530 6309 1,283 0,060 0330 1,812 1,839 1,932 2,025 2,043 2,122 0,305 14015 1,518 0,043 Table 20 Charge 93 / B20 T B25 T B50 T B90 T B100 T B160 T H c A / cm µmax Br T PHyst . 1,5T Ws / kg 0325 1,679 1,71 1,822 1,941 1,966 2,078 0,657 4347 1,054 0,078 0328 1,773 1,801 1,899 1,999 2,019 2,108 0,369 9970 1,417 0,050 0330 1,813 1,84 1,933 2,025 2,043 2,121 0,296 19653 1,505 0,045 Table 21 Charge 93 / B20 T B25 T B50 T B90 T B100 T B160 T H c A / cm µ max B r T Rho in µΩm P Hyst. 1,5T Ws / kg 0322 1,674 1,705 1,813 1,929 1,953 2,069 0,694 4737 1,067 0,3155 0,071 0323 1,681 1,711 1,820 1,945 1,971 2,095 0,473 6562 1,154 0,1891 0,065 0324 1,747 1,781 1,903 2,034 2,061 2,185 0,655 4720 1,025 0,1572 0,078 0325 1,652 1,684 1,797 1,917 1,941 2,061 0,845 3729 0,878 0,3393 0,081 0326 1,685 1,724 1,852 1,984 2,012 2,136 1,283 2410 0,895 0,3731 0,108 0327 1,649 1,680 1,793 1,917 1,942 2,061 0,712 4155 0,909 0,3274 0,077 0328 1,726 1,754 1,854 1,958 1,980 2,077 0,685 4958 1,097 0,3171 0,069 0329 1,797 1,824 1,918 2,012 2,031 2,114 0,524 7497 1,347 0,3019 0,053 0330 1,786 1,814 1,910 2,009 2,028 2,117 0,382 10051 1,414 0,2904 0,051 0331 1,689 1,724 1,847 1,975 2,002 2,123 0,935 3003 0,884 0,3356 0,088 0332 1,679 1,715 1,838 1,968 1,995 2,115 0,907 3034 0,863 0,3624 0,089 0333 1,664 1,699 1,821 1,951 1,978 2,103 0,828 3402 0,869 0,3557 0,085 0334 1,718 1,754 1,872 1,992 2,016 2,126 0,979 2986 0,826 0,3533 0,083 0335 1,811 1,843 1,948 2,051 2,071 2,158 0,479 5484 1,141 0,2922 0,066 0336 1,687 1,723 1,845 1,972 1,998 2,117 0,877 3184 0,843 0,3372 0,086 0337 1,679 1,715 1,839 1,970 1,996 2,120 0,865 3245 0,882 0,3346 0,087 0338 1,703 1,739 1,858 1,979 2,004 2,119 0,999 2916 0,865 0,3356 0,088 0339 1,686 1,722 1,841 1,961 1,983 2,085 0,587 5345 0,897 0,3027 0,059 0422 1,733 1,760 1,856 1,955 1,974 2,063 0,432 11411 1,408 - 0,053 0423 1,635 1,662 1,760 1,867 1,888 1,993 0,653 6647 1,280 - 0,065 Table 22 Charge 93 / B20 T B25 T B50 T B90 T B100 T B160 T H c A / cm µ max B r T P Hyst. 1,5T Ws / kg 0322 1,674 1,702 1,808 1,926 1,950 2,069 0,471 7929 1,376 0,056 0323 1,684 1,714 1,823 1,946 1,971 2,096 0,383 8883 1,353 0,058 0324 1,750 1,783 1,903 2,034 2,060 2,184 0,695 4542 1,113 0,080 0325 1,649 1,681 1,796 1,921 1,946 2,066 0,783 3975 0,968 0,085 0326 1,690 1,728 1,854 1,986 2,012 2,137 1,644 1987 0,915 0,131 0327 1,667 1,699 1,813 1,936 1,961 2,075 0,616 4476 0,992 0,080 0328 1,730 1,757 1,856 1,962 1,982 2,080 0,489 8729 1,393 0,054 0329 1,805 1,831 1,923 2,016 2,034 2,116 0,396 12084 1,520 0,047 0330 1,787 1,814 1,908 2,006 2,025 2,113 0,378 9892 1,457 0,054 0331 1,693 1,726 1,846 1,974 2,001 2,123 0,854 4279 1,237 0,080 0332 1,679 1,714 1,834 1,964 1,990 2,113 0,817 4486 1,233 0,080 0333 1,664 1,698 1,817 1,949 1,977 2,104 0,656 5334 1,274 0,071 0334 1,722 1,755 1,869 1,987 2,011 2,121 0,851 4767 1,253 0,078 0335 1,815 1,845 1,948 2,051 2,070 2,158 0,457 5600 1,258 0,064 0336 1,696 1,729 1,849 1,977 2,002 2,125 0,747 4965 1,228 0,075 0337 1,685 1,719 1,841 1,972 1,999 2,123 0,738 4623 1,226 0,078 0338 1,712 1,745 1,861 1,983 2,008 2,125 0,897 4543 1,246 0,081 0339 1,687 1,723 1,843 1,963 1,986 2,087 0,507 6186 0,952 0,058 Table 23 Charge 93 / B20 T B25 T B50 T B90 T B100 T B160 T H c Alcm µ max B r T Rho in µΩm P Hyst. 1,5T Ws / kg 0323 1,678 1,708 1,818 1,943 1,97 2,095 0,397 6506 1,087 0,1929 0,069 0328 1,692 1,721 1,823 1,933 1,956 2,063 0,683 4863 1,088 0,3146 0,070 0329 1,778 1,806 1,902 1,999 2,018 2,106 0,473 7860 1,346 0,3022 0,053 0330 1,756 1,784 1,882 1,985 2,005 2,096 0,362 10568 1,438 0,2927 0,048 0334 1,683 1,719 1,84 1,967 1,992 2,113 0,856 3306 0,874 0,3474 0,083 0335 1,748 1,780 1,893 2,008 2,031 2,137 0,486 5009 1,119 0,2891 0,067 0339 1,599 1,641 1,776 1,910 1,938 2,062 0,489 4985 0,770 - 0,066 0442 1,612 1,654 1,780 1,897 1,919 2,022 0,412 5510 0,606 - 0,057 Table 24 Charge 93 / B20 T B25 T B50 T B90 T B100 T B160 T H c A / cm µ max B r T P Hyst. 1,5T Ws / kg 0323 1,672 1,701 1,811 1,937 1,964 2,089 0,348 8185 1,297 0,064 0328 1,693 1,721 1,823 1,934 1,957 2,063 0,511 8157 1,37 0,057 0329 1,778 1,804 1,9 1,998 2,017 2,105 0,383 11748 1,475 0,048 0330 1,759 1,786 1,883 1,983 2,004 2,093 0,344 14191 1,46 0,049 0334 1,684 1,717 1,837 1,966 1,992 2,113 0,753 4701 1,202 0,076 0335 1,749 1,781 1,892 2,008 2,031 2,136 0,457 5275 1,174 0,070 Table 25 Charge 93 / µ max Dichte (g / cm 3 ) Mittleres Atomgewicht Hauptelemente Dichte per Dreisatz Δρ (%) 323 9.047 7,942 56,371 7,942 0,00% 325 4.722 7,923 56,296 7,931 -0,11% 327 4.605 7,918 56,292 7,931 -0,17% 328 13.859 7,917 56,286 7,930 -0,16% 329 15.658 7,912 56,283 7,930 -0,22% 330 22.271 7,909 56,281 7,929 -0,26% 420 20.281 7,905 56,262 7,927 -0,27% 422 11.411 7,894 56,224 7,921 -0,34% 423 7.626 7,882 56,202 7,918 -0,46% 428 8.640 7,911 56,279 7,929 -0,23% 429 10.832 7,911 56,279 7,929 -0,23% 430 9.229 7,914 56,280 7,929 -0,19% 431 9.119 7,910 56,278 7,929 -0,24% 432 11.109 7,910 56,277 7,929 -0,24% 433 12.767 7,911 56,284 7,930 -0,23% 434 11.386 7,913 56,290 7,931 -0,22% 435 15.751 7,912 56,304 7,933 -0,26% 436 13.814 7,921 56, 403 7,947 -0,32% 437 13.273 7,908 56,266 7,927 -0,24% 438 15.090 7,917 56,380 7,943 -0,32% 440 15.730 7,910 56,274 7,928 -0,24% 441 16.232 7,913 56,283 7,930 -0,21 % 76 / 4988 12.150 7,899 56,249 7,925 -0,33% 0502 11.770 7,909 56,277 7,929 -0,25% 0503 11.708 7,910 56,276 7,929 -0,24% 0504 21.461 7,898 56,232 7,922 -0,31% 0505 25.320 7,894 56,192 7,917 -0,29% Table 26 Charge 93 / Glühung B20 T B25 T B50 T B90 T B100 T B160 T H c A / cm µ max B r in T P Hyst. 1,5T Ws / kg 0329 4h 1050°C + 10h 910°C 1,808 1,833 1,925 2,018 2,035 2,115 0,369 17227 1,528 0,046 0330 4h 1050°C + 10h 910°C 1,813 1,839 1,930 2,021 2,039 2,118 0,354 19591 1,514 0,046 0330 4h 1050°C Abkühlung 50°C / h + 10h, 910°C 1,815 1,840 1,934 2,027 2,045 2,122 0,305 22271 1,514 0,045 0420 4h 1000°C + 60h 950°C 1,798 1,824 1,914 2,006 2,024 2,104 0,347 20281 1,548 0,042 0420 4h 1050°C Abkühlung 150°C / h 1,767 1,793 1,889 1,988 2,007 2,094 0,378 14388 1,456 0,049 0505 4h 1050°C Abkühlung 150°C / h 1,809 1,837 1,935 2,031 2,049 2,129 0,279 13981 1,290 0,046 0505 4h 1050°C + 10h 910°C 1,787 1,813 1,912 2,011 2,031 2,118 0,297 15480 1,362 0,047 0505 4h 1050°C + 10h 910°C + 10h 930°C + 10h 940°C 1,790 1,817 1,914 2,012 2,032 2,117 0,244 25320 1,524 0,043 504 4h 1050°C Abkühlung 150°C / h 1,772 1,801 1,899 1,998 2,018 2,109 0,394 10716 1,303 0,055 504 4h 1050°C + 10h 910°C 1,776 1,803 1,900 1,999 2,019 2,109 0,351 14009 1,396 0,051 504 4h 1050°C + 10h 910°C + 10h 930°C + 10h 940°C 1,774 1,800 1,894 1,993 2,011 2,098 0,294 21461 1,52 0,046 Table 27 Charge Glühung C in ppmw S in ppmw 93 / 0435 ungeglüht 32 36 4h 1050°C, H2 + 10h 910°C, H2 (zwei Glühungen) 15 12 93 / 0440 ungeglüht 30 13 4h 1050°C, 10h 910°C, H2 (one annealing) 14 6 93 / 0505 unannealed 30 8 4h 1050°C, H2 (one annealing) 12 4 4h 1050°C, H2 + 10h 910°C, H2 (two annealings) 16 4 76 / 4998 unannealed 20 48 4h 1050°C, H2, 10h 910°C, H2 (one annealing) 21 23 76 / 5180 unannealed 26 60 4h 1050°C, H2 (one annealing) 17 40 4h 1050°C, H2 + 10h 930°C, H2 (two annealings) 15 36 76 / 5180 unannealed 26 60 6h 1050°C, H2 (one annealing) 17 31 6h 1050°C, H2 + 10h 930°C, H2 (two annealings) 17 28 Table 28 Batch sample Dimensions . (mm) Final annealing B20 in T B25 in T B50 in T B90 in T B100 in T B160 in T Hc Rings in A / cm µ max P Hyst. at 1.5T in Ws / kg from hot-rolled thickness 1.9mm 7604988A without intermediate annealing (ZGL) 0,35 4 hours, 1050°C 1,704 1,734 1,836 1,946 1,968 2,069 0,428 10836 0,054 7604988A without ZGL 0,35 4h, 1050°C + 10h, 910°C 1,702 1,732 1,834 1,944 1,965 2,068 0,429 11635 0,053 7604988A without ZGL 0,20 4 hours, 1050°C 1,723 1,753 1,857 1,964 1,985 2,080 0,423 10555 0,054 7604988A without ZGL 0,20 4h, 1050°C + 10h, 910°C 1,724 1,753 1,860 1,969 1,989 2,086 0,458 10478 0,054 7604988A ZGL 1h 750°C 0,20 4 hours, 1050°C 1,736 1,764 1,868 1,972 1,993 2,086 0,417 11196 0,053 7604988A ZGL 1h 750°C 0,20 4h, 1050°C + 10h, 910°C 1,738 1,766 1,868 1,973 1,994 2,088 0,421 12467 0,052 7604988A TGL 1h 1050°C 0,20 4 hours, 1050°C 1,740 1,769 1,872 1,976 1,996 2,088 0,437 10452 0,054 7604988A TGL 1h 1050°C 0,20 4h, 1050°C + 10h, 910°C 1,740 1,769 1,872 1,977 1,998 2,092 0,458 10668 0,054 from hot-rolled thickness 2.6mm 7604988B without ZGL 0,35 4 hours, 1050°C 1,707 1,735 1,838 1,945 1,968 2,067 0,394 11778 0,052 7604988B without ZGL 0,35 4h, 1050°C + 10h, 910°C 1,709 1,737 1,839 1,948 1,970 2,072 0,406 12741 0,052 7604988B without ZGL 0,20 4 hours, 1050°C 1,736 1,766 1,869 1,974 1,994 2,087 0,416 10529 0,053 7604988B without ZGL 0,20 4h, 1050°C + 10h, 910°C 1,734 1,763 1,867 1,974 1,994 2,089 0,441 11174 0,052 7604988B ZGL 1h 750°C 0,20 4 hours, 1050°C 1,762 1,790 1,888 1,989 2,009 2,096 0,383 12943 0,050 7604988B ZGL 1h 750°C 0,20 4h, 1050°C + 10h, 910°C 1,762 1,790 1,890 1,991 2,011 2,100 0,390 14125 0,049 7604988B TGL 1h 1050°C 0,20 4 hours, 1050°C 1,753 1,783 1,883 1,985 2,005 2,094 0,395 12036 0,052 7604988B TGL 1h 1050°C 0,20 4h, 1050°C + 10h, 910°C 1,758 1,786 1,886 1,989 2,009 2,098 0,399 13094 0,049 from slab section hot and cold rolled in the technical center 7604988A without ZGL 0,35 10h 1050°C cool. 50°C / h; 10h 930°C OK 1,728 1,757 1,858 1,963 1,984 2,078 0,299 18717 0,043 7604988A without ZGL 0,35 4h, 1050°C cooldown 10°C / h 1,732 1,761 1,860 1,965 1,985 2,077 0,485 8633 0,050 7604988A without ZGL 0,35 100h, 910°C 1,584 1,612 1,711 1,824 1,849 1,972 0,578 5190 0,068 7604988A without ZGL 0,35 4 hours, 1050°C 1,734 1,763 1,861 1,965 1,985 2,079 0,410 9315 0,050 7604988A without ZGL 0,35 10h 1050°C cool. 50°C / h; 10h 930°C OK 1,725 1,754 1,855 1,961 1,982 2,077 0,311 12150 0,043 7604988A without ZGL 0,35 2h 1050°C; 4h 910°C 1,735 1,765 1,867 1,972 1,993 2,090 0,422 9001 0,050 7605180A Head 0,35 4h 1050°C 1,760 1,787 1,888 1,990 2,010 2,101 0,388 9138 0,053 7605180A Head 0,35 4h 1050°C + 10h 930°C 1,759 1,786 1,886 1,986 2,006 2,097 0,368 14130 0,050 7605180B Head 0,35 6h 1050°C 1,782 1,810 1,908 2,008 2,028 2,114 0,334 10925 0,051 7605180B Head 0,35 6h 1050°C + 10h 930°C 1,782 1,809 1,907 2,005 2,025 2,111 0,254 22632 0,039 7605180A Foot 0,35 6h 1050°C 1,784 1,811 1,907 2,004 2,023 2,109 0,370 9222 0,052 7605180A Foot 0,35 6h 1050°C + 10h 930°C 1,791 1,817 1,912 2,010 2,030 2,115 0,287 18397 0,041 Table 29 Batch 93 / 1. Onset heating (T ü2 ) 1. Onset cooling (T ü1 ) best Hc in A / cm annealing 323 940 932 0,348 4h 1150°C + 10h 910°C 328 934 914 0,369 4h 1050°C Abk.50°C / h + 10h, 910°C 329 952 933 0,367 4h 1050°C + 10h 910°C 330 980 958 0,282 10h 1050°C cool. 50°C / h to 930°C 10h OK 420 988 964 0,347 4h 1000°C + 60h 950°C 422 1017 979 0,382 4h 1100°C + 10h 960°C 423 1037 994 0,593 4h 950°C 428 951 934 0,540 4h 1050°C + 10h 910°C 429 947 934 0,465 4h 1050°C + 10h 910°C 430 944 932 0,520 4h 1050°C + 10h 910°C 431 950 931 0,572 4h 1050°C + 10h 910°C 432 946 925 0,516 4h 1050°C + 10h 910°C 433 949 929 0,412 4h 1050°C + 10h 910°C 434 944 921 0,495 4h 1050°C + 10h 910°C 435 953 932 0,404 4h 1050°C + 10h 910°C 436 952 931 0,402 4h 1050°C + 10h 910°C 437 954 934 0,409 4h 1050°C + 10h 910°C 438 955 934 0,406 4h 1050°C + 10h 910°C 439 958 936 0,578 4h 1050°C 440 954 934 0,331 4h 1050°C + 10h 910°C 441 952 932 0,313 4h 1050°C + 10h 910°C 443 #NV 1012 0,792 4h 1050°C OK = Oven cooling Cooling of T1 at 150K / h, unless otherwise stated Cooling of T2 at 150K / h, unless otherwise stated "+" means 2 separate glows

Claims

[1] A method for producing a soft magnetic alloy, comprising: Providing a precursor product having a composition consisting essentially of 5 wt.% ≤ Co ≤ 25 wt% 0.3 wt.% ≤ V ≤ 5.0 wt% 0 wt.% ≤ Cr ≤ 3.0 wt% 0 wt.% ≤ Si ≤ 3.0 wt% 0 wt.% ≤ Mn ≤ 3.0 wt% 0 wt.% ≤ Al ≤ 3.0 wt% 0 wt.% ≤ Ta ≤ 0.5 wt% 0 wt.% ≤ Ni ≤ 0.5 wt% 0 wt.% ≤ Mon ≤ 0.5 wt% 0 wt.% ≤ Cu ≤ 0.2 wt% 0 wt.% ≤ Nb ≤ 0.25 wt% 0 wt.% ≤ Ti ≤ 0.05 wt% 0 wt.% ≤ Ce ≤ 0.05 wt% 0 wt.% ≤ Ca ≤ 0.05 wt% 0 wt.% ≤ Mg ≤ 0.05 wt% 0 wt.% ≤ C ≤ 0.02 wt% 0 wt.% ≤ Zr ≤ 0.1 wt% 0 wt.% ≤ O ≤ 0.025 wt% 0 wt.% ≤ S ≤ 0.015 wt% The remainder is iron, wherein Cr+Si+Al+Mn ≤ 3.0 wt.%, and up to 0.2 wt.% of other melt-related impurities, and which has a cold-rolled texture or a fiber texture, wherein the precursor product has a phase transition from a BCC phase region, into a BCC / FCC mixed region to an FCC phase region, wherein with increasing temperature the phase transition between the BCC phase region and the BCC / FCC mixed region at a first transition temperature T Ü1 and with further increasing temperature the transition between the BCC / FCC mixed region and the FCC phase region at a second transition temperature T Ü2 takes place, where T Ü2 > T Ü1 and the difference T ü2 - T ü1 is less than 45K, final heat treatment of the precursor at a temperature T1 and then cooling from T1 to room temperature at a rate of 25°C / h to 500°C / h, and then heating from room temperature to T2, whereby the precursor is cooled from T2 to room temperature at a rate of 10°C / h to 50,000°C / h, where T1 is above T Ü2 and T2 is below T Ü1 where 940°C ≤ T1 < T m , and 700°C ≤ T2 ≤ 1050°C, where T2 < T1 and T m is the solidus temperature, where the precursor is heat treated at T2 for a time t2, where 30 minutes ≤ t2 ≤ 20 hours. [2] A method for producing a soft magnetic alloy, comprising: Providing a precursor product having a composition consisting essentially of 5 wt.% ≤ Co ≤ 25 wt% 0.3 wt.% ≤ V ≤ 5.0 wt% 0 wt.% ≤ Cr ≤ 3.0 wt% 0 wt.% ≤ Si ≤ 3.0 wt% 0 wt.% ≤ Mn ≤ 3.0 wt% 0 wt.% ≤ Al ≤ 3.0 wt% 0 wt.% ≤ Ta ≤ 0.5 wt% 0 wt.% ≤ Ni ≤ 0.5 wt% 0 wt.% ≤ Mon ≤ 0.5 wt% 0 wt.% ≤ Cu ≤ 0.2 wt% 0 wt.% ≤ Nb ≤ 0.25 wt% 0 wt.% ≤ Ti ≤ 0.05 wt% 0 wt.% ≤ Ce ≤ 0.05 wt% 0 wt.% ≤ Ca ≤ 0.05 wt% 0 wt.% ≤ Mg ≤ 0.05 wt% 0 wt.% ≤ C ≤ 0.02 wt% 0 wt.% ≤ Zr ≤ 0.1 wt% 0 wt.% ≤ O ≤ 0.025 wt% 0 wt.% ≤ S ≤ 0.015 wt% The remainder is iron, wherein Cr+Si+Al+Mn ≤ 3.0 wt.%, and up to 0.2 wt.% of other melt-related impurities, and which has a cold-rolled texture or a fiber texture, wherein the precursor product has a phase transition from a BCC phase region, into a BCC / FCC mixed region to an FCC phase region, wherein with increasing temperature the phase transition between the BCC phase region and the BCC / FCC mixed region at a first transition temperature T Ü1 and with further increasing temperature the transition between the BCC / FCC mixed region and the FCC phase region at a second transition temperature T Ü2 takes place, where T Ü2 > T Ü1 and the difference T ü2 - T ü1 is less than 45K, final heat treatment of the precursor product at a temperature T1 and then at a temperature T2, where T1 > T2, where T1 is above T Ü2 and T2 is below T Ü1where 940°C ≤ T1 < T m , and 700°C ≤ T2 ≤ 1050°C, where T2 < T1 and T m the solidus temperature is, wherein the cooling rate over at least the temperature range from T1 to T2 is 10°C / h to 900°C / h, wherein the precursor is heat-treated at T1 for a time t1, where 15 minutes ≤ t1 ≤ 20 hours, and is then cooled from T1 to T2 and held and heat-treated at T2 for a time t2, where 30 minutes ≤ t2 ≤ 20 hours, and is then cooled from T2 to room temperature. [3] A method according to claim 1 or claim 2, wherein the transition temperature T Ü1 with a sample mass of 50 mg and a DSC (Differential Scanning Calorimetry) heating rate of 10 Kelvin per minute above 900°C, preferably above 920°C, and most preferably above 940°C. [4] Method according to one of claims 1 to 3, wherein 960°C ≤ T1 < T m is. [5] Method according to one of claims 1 to 4, wherein TÜ2 > T Ü1 and the difference T ü2 - T ü1 is less than 25K, [6] The process of claim 1, wherein the precursor of T2 is cooled to room temperature at a rate of 100°C / h to 1000°C / h. [7] Method according to one of claims 1 to 6, wherein after heat treatment the soft magnetic alloy has a maximum permeability µ max ≥ 5,000, and / or an electrical resistance p ≥ 0.25 µΩm, hysteresis losses P Hys ≤ 0.07 J / kg at an amplitude of 1.5 T, and / or a coercive field strength H c of ≤ 0.7 A / cm and / or induction B ≥ 1.90 T at 100 A / cm. [8] A method according to claim 7, wherein after heat treatment the soft magnetic alloy has a maximum permeability µ max ≥ 10,000, and / or an electrical resistance p ≥ 0.25 µΩm, and / or hysteresis losses P Hys ≤ 0.06 J / kg at an amplitude of 1.5 T, and / or a coercive field strength Hc of ≤ 0.6 A / cm and induction B ≥ 1.95 T at 100 A / cm. [9] A method according to claim 8, wherein after heat treatment the soft magnetic alloy has a maximum permeability µ max ≥ 12,000, preferably µ max ≥ 17,000 and / or an electrical resistance p ≥ 0.30 µΩm, and / or hysteresis losses P Hys ≤ 0.05 J / kg at an amplitude of 1.5 T, and / or a coercive field strength H c of ≤ 0.5 A / cm, preferably a coercive field strength H c of ≤ 0.4 A / cm, preferably a coercive field strength H c of ≤ 0.3 A / cm and / or induction B ≥ 2.00 T at 100 A / cm. [10] Method according to one of claims 1 to 9, wherein a maximum difference in the coercive field strength H c measured parallel to the rolling direction, measured diagonally (45°) to the rolling direction, or measured perpendicular to the rolling direction between two of these directions is a maximum of 6%, preferably a maximum of 3%. [11] A process according to any one of claims 1 to 10, wherein the heat treatment is carried out under a hydrogen-containing atmosphere or under an inert gas. [12] A method according to claim 1 or claim 2, wherein the heat treating is carried out at T1 in a stationary furnace and at T2 in a stationary furnace. [13] A process according to claim 1 or claim 2, wherein the heat treatment is carried out at T1 in a continuous furnace and at T2 in a continuous furnace. [14] The method of claim 1, wherein the heat treatment is carried out at T1 in a continuous furnace and at T2 in a stationary furnace. [15] The method of claim 1, wherein the heat treatment is carried out at T1 in a stationary furnace and at T2 in a continuous furnace. [16] Method according to one of claims 1 to 15, wherein the precursor product has the shape of one or more sheets. [17] Method according to one of claims 1 to 15, wherein the precursor product has the shape of one or more laminated cores. [18] Method according to claim 16, wherein the precursor initially has the shape of a strip from which at least one sheet is manufactured by punching, laser cutting or water jet cutting, wherein the heat treatment is carried out on one or more sheets. [19] Method according to claim 18, wherein a plurality of sheets are bonded to form a laminated core after heat treatment by means of an insulating adhesive, or are coated with an inorganic-organic hybrid coating and then further processed to form a laminated core. [20] Method according to claim 17, wherein the precursor initially has the shape of a laminated core and the heat treatment is carried out on one or more laminated cores. [21] Method according to one of claims 1 to 20, further comprising for producing the precursor: Providing a melt by vacuum induction melting, Electroslag remelting or vacuum arc remelting, which essentially consists of 5 wt.% ≤ Co ≤ 25 wt% 0.3 wt.% ≤ V ≤ 5.0 wt% 0 wt.% ≤ Cr ≤ 3.0 wt% 0 wt.% ≤ Si ≤ 3.0 wt% 0 wt.% ≤ Mn ≤ 3.0 wt% 0 wt.% ≤ Al ≤ 3.0 wt% 0 wt.% ≤ Ta ≤ 0.5 wt% 0 wt.% ≤ Ni ≤ 0.5 wt% 0 wt.% ≤ Mon ≤ 0.5 wt% 0 wt.% ≤ Cu ≤ 0.2 wt% 0 wt.% ≤ Nb ≤ 0.25 wt% 0 wt.% ≤ Ti ≤ 0.05 wt% 0 wt.% ≤ Ce ≤ 0.05 wt% 0 wt.% ≤ Ca ≤ 0.05 wt% 0 wt.% ≤ Mg ≤ 0.05 wt% 0 wt.% ≤ C ≤ 0.02 wt% 0 wt.% ≤ Zr ≤ 0.1 wt% 0 wt.% ≤ O ≤ 0.025 wt% 0 wt.% ≤ S ≤ 0.025 wt% The remainder is iron, with Cr+Si+Al+Mn ≤ 3.0 wt% and up to 0.2 wt% of other impurities, Solidification of the melt into a cast block, Forming the cast ingot, whereby the forming is carried out by means of heating rolling and / or forging and / or cold forming. [22] The method according to claim 21, wherein the cast ingot is formed into a slab by hot rolling at temperatures between 900°C and 1300°C, and then into a hot strip with a thickness D1, and then formed into a strip with a thickness D2 by cold rolling, where 0.05 mm ≤ D2 ≤ 1.0 mm, and D2 < D1. [23] The method according to claim 22, wherein the degree of cold deformation by cold rolling is >40%, preferably >80%. [24] A method according to claim 21, wherein the cast ingot is formed into a billet by hot rolling at temperatures between 900°C and 1300°C and is then formed into a wire by cold drawing. [25] Method according to claim 24, wherein the degree of cold deformation by cold drawing is >40%, preferably >80%. [26] The method of claim 25, further comprising an intermediate annealing. [27] Method according to one of claims 1 to 26, wherein Tü1 > T c where T c is the Curie temperature, and T c ≥ 900°C. [28] The method of claim 27, wherein T ü1 > T2 > T c is elected. [29] Process according to one of claims 1 to 28, wherein after the heat treatment the average grain size is at least 100µm, preferably at least 200µm, most preferably at least 250µm. [30] A method according to any one of claims 1 to 29, wherein after heat treatment the measured density of the annealed alloy is more than 0.10% lower than the density calculated by the rule of three from the average atomic weight of the metallic elements of the alloy, from the average atomic weight of the metallic elements of the corresponding binary FeCo alloy and from the measured density of this annealed binary FeCo alloy. [31] A method according to any one of claims 1 to 30, wherein after heat treatment the measured density of the annealed alloy is 0.20% to 0.35% lower than the density calculated by the rule of three from the average atomic weight of the metallic elements of the alloy, from the average atomic weight of the metallic elements of the corresponding binary FeCo alloy and from the measured density of this annealed binary FeCo alloy. [32] Process according to one of claims 21 to 31, wherein the sulphur content is reduced during the heat treatment under a protective gas atmosphere containing H2. [33] A method according to any one of claims 1 to 32, further comprising coating the precursor with an oxide layer for electrical insulation. [34] A process according to claim 33, wherein the precursor is coated with a layer of magnesium methylate or zirconium propylate, which is converted into an insulating oxide layer during the heat treatment. [35] A method according to claim 33, wherein the precursor is heat-treated in an oxygen- or water vapor-containing atmosphere to form the electrically insulating oxide layer. [36] Method according to claim 18, wherein a plurality of sheets after heat treatment oxidized on the surface to create an insulating layer and then glued or laser welded to form the laminated core.

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